Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/10009—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the number, the constitution or treatment of glass sheets
  • B32B17/10128—Treatment of at least one glass sheet
  • B32B17/10137—Chemical strengthening
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/10009—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the number, the constitution or treatment of glass sheets
  • B32B17/10036—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the number, the constitution or treatment of glass sheets comprising two outer glass sheets
  • B32B17/10045—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the number, the constitution or treatment of glass sheets comprising two outer glass sheets with at least one intermediate layer consisting of a glass sheet
  • B32B17/10055—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the number, the constitution or treatment of glass sheets comprising two outer glass sheets with at least one intermediate layer consisting of a glass sheet with at least one intermediate air space
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/10165—Functional features of the laminated safety glass or glazing
  • B32B17/10293—Edge features, e.g. inserts or holes
  • B32B17/10302—Edge sealing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/1055—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer
  • B32B17/10743—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer containing acrylate (co)polymers or salts thereof
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/1055—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer
  • B32B17/10761—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer containing vinyl acetal
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/1055—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer
  • B32B17/1077—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer containing polyurethane
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B32—LAYERED PRODUCTS
  • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
  • B32B17/00—Layered products essentially comprising sheet glass, or glass, slag, or like fibres
  • B32B17/06—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material
  • B32B17/10—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin
  • B32B17/10005—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing
  • B32B17/1055—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer
  • B32B17/10788—Layered products essentially comprising sheet glass, or glass, slag, or like fibres comprising glass as the main or only constituent of a layer, next to another layer of a specific material of synthetic resin laminated safety glass or glazing characterized by the resin layer, i.e. interlayer containing ethylene vinylacetate
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
  • C03B27/00—Tempering or quenching glass products
  • C03B27/016—Tempering or quenching glass products by absorbing heat radiated from the glass product
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
  • C03B27/00—Tempering or quenching glass products
  • C03B27/04—Tempering or quenching glass products using gas
  • C03B27/0413—Stresses, e.g. patterns, values or formulae for flat or bent glass sheets
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
  • C03B27/00—Tempering or quenching glass products
  • C03B27/04—Tempering or quenching glass products using gas
  • C03B27/044—Tempering or quenching glass products using gas for flat or bent glass sheets being in a horizontal position
  • C03B27/048—Tempering or quenching glass products using gas for flat or bent glass sheets being in a horizontal position on a gas cushion
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
  • C03B29/00—Reheating glass products for softening or fusing their surfaces; Fire-polishing; Fusing of margins
  • C03B29/04—Reheating glass products for softening or fusing their surfaces; Fire-polishing; Fusing of margins in a continuous way
  • C03B29/06—Reheating glass products for softening or fusing their surfaces; Fire-polishing; Fusing of margins in a continuous way with horizontal displacement of the products
  • C03B29/08—Glass sheets
  • C03B29/12—Glass sheets being in a horizontal position on a fluid support, e.g. a gas or molten metal
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
  • C03B35/00—Transporting of glass products during their manufacture, e.g. hot glass lenses, prisms
  • C03B35/14—Transporting hot glass sheets or ribbons, e.g. by heat-resistant conveyor belts or bands
  • C03B35/145—Transporting hot glass sheets or ribbons, e.g. by heat-resistant conveyor belts or bands by top-side transfer or supporting devices, e.g. lifting or conveying using suction
  • C03B35/147—Transporting hot glass sheets or ribbons, e.g. by heat-resistant conveyor belts or bands by top-side transfer or supporting devices, e.g. lifting or conveying using suction of the non-contact type
• • C—CHEMISTRY; METALLURGY
  • C03—GLASS; MINERAL OR SLAG WOOL
  • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
  • C03C23/00—Other surface treatment of glass not in the form of fibres or filaments
  • C03C23/007—Other surface treatment of glass not in the form of fibres or filaments by thermal treatment
• • E—FIXED CONSTRUCTIONS
  • E04—BUILDING
  • E04C—STRUCTURAL ELEMENTS; BUILDING MATERIALS
  • E04C2/00—Building elements of relatively thin form for the construction of parts of buildings, e.g. sheet materials, slabs, or panels
  • E04C2/54—Slab-like translucent elements
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/54—Fixing of glass panes or like plates
  • E06B3/5409—Means for locally spacing the pane from the surrounding frame
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/54—Fixing of glass panes or like plates
  • E06B3/5436—Fixing of glass panes or like plates involving holes or indentations in the pane
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/66—Units comprising two or more parallel glass or like panes permanently secured together
  • E06B3/6612—Evacuated glazing units
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/66—Units comprising two or more parallel glass or like panes permanently secured together
  • E06B3/663—Elements for spacing panes
  • E06B3/66304—Discrete spacing elements, e.g. for evacuated glazing units
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/66—Units comprising two or more parallel glass or like panes permanently secured together
  • E06B3/663—Elements for spacing panes
  • E06B3/66309—Section members positioned at the edges of the glazing unit
• • E—FIXED CONSTRUCTIONS
  • E06—DOORS, WINDOWS, SHUTTERS, OR ROLLER BLINDS IN GENERAL; LADDERS
  • E06B—FIXED OR MOVABLE CLOSURES FOR OPENINGS IN BUILDINGS, VEHICLES, FENCES OR LIKE ENCLOSURES IN GENERAL, e.g. DOORS, WINDOWS, BLINDS, GATES
  • E06B3/00—Window sashes, door leaves, or like elements for closing wall or like openings; Layout of fixed or moving closures, e.g. windows in wall or like openings; Features of rigidly-mounted outer frames relating to the mounting of wing frames
  • E06B3/66—Units comprising two or more parallel glass or like panes permanently secured together
  • E06B3/67—Units comprising two or more parallel glass or like panes permanently secured together characterised by additional arrangements or devices for heat or sound insulation or for controlled passage of light
  • E06B3/6715—Units comprising two or more parallel glass or like panes permanently secured together characterised by additional arrangements or devices for heat or sound insulation or for controlled passage of light specially adapted for increased thermal insulation or for controlled passage of light
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P40/00—Technologies relating to the processing of minerals
  • Y02P40/50—Glass production, e.g. reusing waste heat during processing or shaping
  • Y02P40/57—Improving the yield, e-g- reduction of reject rates

Definitions

• the disclosure relates generally to thermally conditioned architectural glass, and specifically relates to thermally strengthened architectural glass and to related methods and systems for the thermal strengthening of architectural glass, particularly for thin architectural glass sheets.
• Thermal strengthening of glass is distinguished from chemical strengthening of glass, in which surface compressive stresses are generated by changing the chemical composition of the glass in regions near the surface by a process such as ion diffusion.
• exterior portions of glass may be strengthened by exchanging larger ions for smaller ions near the glass surface to impart a compressive stress (also called negative tensile stress) on or near the surface.
• the compressive stress is believed to limit crack initiation and/or
• Thermal strengthening of glass also is distinguished from glass strengthened by processes in which exterior portions of the glass are strengthened or arranged by combining two types of glass. In such processes, layers of glass compositions that have differing coefficients of thermal expansion are combined or laminated together while hot. For example, by sandwiching molten glass with a higher coefficient of thermal expansion (CTE) between layers of molten glass with a lower CTE, positive tension in the interior glass compresses the outer layers when the glasses cool, again forming compressive stress on the surface to balance the positive tensile stress. This surface compressive stress provides strengthening.
• CTE coefficient of thermal expansion
• Thermally strengthened architectural glass has advantages relative to unstrengthened architectural glass.
• the surface compression of the strengthened architectural glass provides greater resistance to fracture than unstrengthened architectural glass.
• the increase in strength generally is proportional to the amount of surface compression stress. If a sheet possesses a sufficient level of thermal strengthening, relative to its thickness, then if the sheet is broken, generally it will divide into small fragments rather than into large or elongated fragments with sharp edges. Glass that breaks into sufficiently small fragments, or "dices,” as defined by various established standards, may be known as safety glass, or "fully tempered” glass, or sometimes simply "tempered” glass.
• aspects of the present disclosure also relate generally to an architectural glass or glass- ceramic that has a stress profile for strengthening exterior portions thereof.
• Architectural glass and glass-ceramic articles such as sheets of architectural glass, may be used for a broad range of applications. Examples of such applications include use in architectural windows, single and multi-pane windows, indoor and outdoor windows, vacuum insulated glass windows, and safety glass windows in buildings, homes, hotels, offices, and other similar structures.
• This disclosure relates, in part, to highly strengthened thin architectural glass sheets and articles, and to methods, processes, and systems that achieve surprisingly high levels of heat strengthening of architectural glass sheets at thicknesses not achieved in the past.
• the process and method of the current disclosure is believed to surpass the architectural glass thickness limits and heat transfer rates provided by conventional convective gas thermal strengthening processes without the need to contact the architectural glass with liquid or solid heat sinks.
• the architectural glass is contacted only with a gas.
• the systems and methods disclosed enable thermal strengthening, including up to "full temper" or dicing behavior, in architectural glass sheets having thicknesses down to at least as thin as 0.1 mm (in at least some contemplated
• these advantageous architectural glass sheet material properties are provided by a system and method with substantially lower quenching power requirements, as compared to conventional convective glass tempering systems.
• One embodiment of the disclosure relates to a process for thermally strengthening an architectural glass material.
• the process includes providing article formed from an architectural glass material.
• the process includes heating the article above a glass transition temperature of the architectural glass material.
• the process includes moving the heated article into a cooling station.
• the cooling station includes a heat sink having a heat sink surface facing the heated article and a gas gap separating the heat sink surface from the heated article such that the heat sink surface does not touch the heated article.
• the process includes cooling the heated article to a temperature below the glass transition temperature such that surface compressive stresses and central tensile stresses are created within the article.
• the article is cooled by transferring thermal energy from the heated article to the heat sink by conduction across the gap such that more than 20% of the thermal energy leaving the heated article crosses the gap and is received by the heat sink.
• the system includes a heating station including a heating element delivering heat to the glass sheet, and the glass sheet includes a first major surface, a second major surface and a thickness between the first and second major surfaces.
• the system includes a cooling station, including opposing first and second heat sink surfaces defining a channel therebetween such that during cooling the glass sheet is located within the channel.
• the system includes a gas bearing delivering pressurized gas to the channel such that the glass sheet is supported within the channel without touching the first and second heat sink surfaces, and the gas bearing defines a gap area.
• the gas bearing delivers a gas into the channel such that a total mass flow rate of gas into the channel is greater than zero and less than 2k/gC p per square meter of gap area, where k is the thermal conductivity of a gas within the channel evaluated in the direction of heat conduction, g is the distance between the glass sheet and the heat sink surface, and C p is the specific heat capacity of the gas within the channel.
• the article includes a first major surface, a second major surface opposite the first major surface and an interior region located between the first and second major surfaces.
• the article includes an average thickness between the first major surface and second major surface of less than 4 mm.
• the article includes at least 70% silicon dioxide by weight.
• An ion content and chemical constituency of at least a portion of both the first major surface and the second major surface is the same as an ion content and chemical constituency of at least a portion of the interior region.
• the first major surface and the second major surfaces are under compressive stress and the interior region is under tensile stress, and the compressive stress is greater than 150 MPa.
• a surface roughness of the first major surface is between 0.2 and 1.5 nm R a roughness.
• the window includes a first glass-based layer and a second glass-based layer.
• the first glass-based layer comprises first and second major surfaces, a first body formed from a first glass material, and a first outer edge.
• the second glass-based layer comprising first and second major surfaces, a second body formed from a second glass material, and a second outer edge.
• the second glass-based layer is spaced apart from and disposed substantially parallel to the first glass-based layer by a first distance.
• the second glass-based layer comprises an interior region located between the first and second major surfaces of the second glass-based layer.
• the second glass-based layer includes an ion content and chemical constituency of at least a portion of both the first major surface and the second major surface is the same as an ion content and chemical constituency of at least a portion of the interior region.
• the first and second major surfaces are under compressive stress and the interior region is under tensile stress, and the compressive stress is greater than 150 MPa.
• a surface roughness of the first major surface of the second glass-based layer is between 0.2 and 2.0 nm R a roughness.
• the window includes a first glass-based layer and a second glass-based layer.
• the first glass-based layer comprises first and second major surfaces, a first body formed from a first glass material, and a first outer edge.
• the second glass-based layer comprising first and second major surfaces, a second body formed from a second glass material, and a second outer edge. The first and second major surface of the second glass-based layer separated by the thickness t.
• the second glass-based layer is spaced apart from and disposed substantially parallel to the first glass-based layer by a first distance.
• the first major surface is flat to 100 ⁇ total indicator run-out (TIR) along any 50 mm or less profile of the first major surface of the second glass-based layer.
• the second glass-based layer includes a glass material having a low temperature linear CTE, expressed in 1/°C, of a CTE, a high temperature linear CTE, expressed in 1/°C, of a L cTE, an elastic modulus, expressed in GPa, of E, a strain temperature, expressed in units of °C, of T strain, and a softening temperature, expressed in units of °C, of T so f t .
• the first major surface of the second glass-based layer has a thermally induced surface compressive stress of less than 600 MPa and greater than
• h is greater than or equal to 0.020 cal/s cm 2 o C.
• the window includes a first glass oane and a second glass pane.
• the first glass pane comprises first and second major surfaces, a first body formed from a first glass material, and a first outer edge.
• the second glass pane comprising first and second major surfaces, a second body formed from a second glass material, and a second outer edge.
• the second glass pane is spaced apart from and disposed substantially parallel to the first glass pane by a first distance.
• the first major surface is flat to 100 ⁇ total indicator run-out (TIR) along any 50 mm or less profile of the first major surface of the second glass pane.
• TIR total indicator run-out
• the second glass pane includes a glass having a softening temperature, expressed in units of °C, of T so f t and an annealing temperature, expressed in units of °C, of T an neai, and a surface Active temperature measured on the first major surface of the second glass pane represented by Tfs, when expressed in units of °C.
• the second glass pane having a non-dimensional surface fictive temperature parameter 0s given by (Tfs - T an neai)l ⁇ Tsoft - Tanned)-
• the parameter 9s is in the range of from 0.20 to 0.9.
• FIG. 1 is a graph of blower power required for "full tempering" as a function of glass thickness.
• FIG. 2 is a graph of blower power required for "full tempering" as a function of glass thickness for an old process or machine O and a newer process or machine N.
• FIG. 3 (Prior Art) is a graph of the old curve O and the new curve N of FIG. 2 scaled to match and superimposed upon the graph of FIG. 1.
• FIG. 4 is a perspective view of an architectural glass or glass-ceramic article or sheet according to an exemplary embodiment.
• FIG. 5 is a diagrammatic partial cross-section of a thermally strengthened architectural glass sheet of FIG. 4 according an exemplary embodiment.
• FIG. 6 is a graphical representation of estimated tensile stress versus thickness for an architectural glass or glass-ceramic article according to an exemplary embodiment.
• FIG. 7 shows a portion of a fractured glass or glass-ceramic article according to an exemplary embodiment.
• FIG. 8 is a plot of fragmentation per square centimeter as a function of positive tensile stress from experiment.
• FIG. 9 is a plot of the magnitude of negative tensile stress at the surface as a function of initial hot zone temperature from experiment, showing a threshold to achieve dicing.
• FIG. 10 is a plot of the non-dimensional surface fictive temperature parameter 0s for fictive temperatures obtained by one or more embodiments of methods and systems of the present invention.
• FIG. 1 1 is a plot of surface compression stresses calculated by simulation for differing glass compositions, plotted against a proposed temperability parameter ⁇ for the various compositions shown.
• FIGS. 12 and 13 are graphs of two parameters Pi and P 2 as functions of heat transfer coefficient h.
• FIG. 14 is a graph of MPa of surface compression of a glass sheet as a function of thickness t of the sheet in millimeters, showing regions of performance newly opened by one or more embodiments of the systems and methods of the present disclosure.
• FIG. 15 is a graph showing compressive stress as a function of thickness plotted for selected exemplary embodiments of tempered glass sheets of the present disclosure.
• FIG. 16 is a flow chart illustrating some aspects of a method according to the present disclosure.
• FIG. 17 is a flow chart illustrating some aspects of another method according to the present disclosure.
• FIG. 18 is the graph of FIG. 3 with a region R and points A, B, A' and B' marked thereon to show a region in which the methods and systems of the present disclosure allow operation, in contrast to the prior art.
• FIG. 19 is another representation of the region R and points A, B, A and B' of FIG. 18, but shown adjacent to (and positioned relative to the scale) of a reduced size copy of FIG. 2.
• FIG. 20 (Prior Art) is a graph of the required heat transfer coefficient needed for tempering as a function of glass thickness.
• FIG. 21 is a diagrammatic cross-section of a glass sheet being cooled by conduction more than by convection, according to an exemplary embodiment.
• FIG. 22 is a schematic cross-sectional diagram of a conductive strengthening system according to an exemplary embodiment.
• FIG. 23 is a perspective cut-away view of another embodiment of a system similar to that of FIG. 22 according to an exemplary embodiment.
• FIG. 24 is a perspective cut-away view of an alternative embodiment of the inset feature of FIG. 23 according to an exemplary embodiment.
• FIG. 25 is a perspective cut-away view of yet another alternative embodiment of the inset feature of FIG. 23 according to an exemplary embodiment.
• FIG. 26 is a flow chart illustrating some aspects of yet another method according to an exemplary embodiment.
• FIG. 27 is a perspective view of a building with architectural glass windows according to an exemplary embodiment.
• FIG. 28 is a perspective view of a display on a countertop according to an exemplary embodiment.
• FIG. 29 is an exploded perspective view of a device including glass or glass-ceramic articles according to an exemplary embodiment.
• FIG. 30 is a perspective view of a glass or glass-ceramic article or sheet according to an exemplary embodiment.
• FIG. 31 is an architectural window as seen from the outside of a structure according to one embodiment.
• FIGS. 32-33 are cross-sectional views of the peripheral edge of a double-pane window seen along line 1-1 of FIG. 31 according to exemplary embodiments.
• FIG. 34 is a cross-sectional view of the peripheral edge of a triple-pane window seen along line 1-1 of FIG. 31 according to exemplary embodiments.
• FIG. 35 is a front-on view of an example vacuum insulated glass (VIG) window according to an exemplary embodiment.
• VIP vacuum insulated glass
• FIG. 36 is a cross-sectional view of the peripheral edge of a double-pane VIG window seen along line 1-1 of FIG. 35 according to exemplary embodiments.
• FIG. 37 is a close-up cross-sectional view of an example glass-bump spacer.
• FIG. 38 is a cross-sectional view of the peripheral edge of a triple-pane VIG window seen along line 1-1 of FIG. 35 having a middle glass-based layer with glass-bump spacers formed in both surfaces thereof.
• FIG. 39 is a cross-sectional view of the peripheral edge of an example triple-pane VIG window seen along line 1-1 of FIG. 35 having the second set of glass-bump spacers are formed in the back glass-based layer, rather than the middle glass-based layer.
• FIG. 40 is a cross-sectional view of the peripheral edge of an example triple-pane VIG window seen along line 1-1 of FIG. 35 having the first and second sets of glass-bump spacers are formed in the front and back glass-based layers rather than the middle glass-based layer.
• Applicant has recognized a need for improvements in thermal processing of architectural glass, both in methods and systems for thermally strengthening architectural glass and the resulting thermally strengthened architectural glass sheets themselves.
• thinner, but strong optical-quality architectural glass sheet materials e.g., architectural glass pnaes
• products comprising such architectural glass sheets are useful for a number of applications including as layers or panes in single and multi-pane windows, architectural windows, vacuum insulated glass (VIG) windows, etc. both inside and outside buildings, homes, offices, and similar structures.
• VIP vacuum insulated glass
• thermal strengthening of architectural glass is generally cheaper and faster relative to alternative methods of strengthening (e.g., chemical strengthening, lamination-based strengthening)
• traditional thermal strengthening of architectural glass is not known to be effective for strengthening thin architectural glass (e.g., architectural glass sheets of 2-3 mm or less).
• Traditional thermal glass strengthening methods are typically thought to be limited to thicker glass sheets because the level of strengthening depends on the temperature difference created between the surface and the center of the glass sheet during quenching; and because of thermal conduction rate limitations of traditional strengthening methods, it is difficult to achieve significant temperature differences between the surface and the center of a thin architectural glass sheet due to the relatively even cooling that typically occurs throughout a thin glass sheet.
• the present description provides improved methods and systems for utilizing thermal strengthening to produce highly strengthened architectural glass materials, and in particular highly strengthened thin architectural glass sheets.
• the methods and systems solve a variety of the limitations of conventional architectural glass strengthening processes, allowing for high levels of strengthening in architectural glass sheets with thicknesses less than about 3 mm, less than 2 mm, less than 1.5 mm, less than 1.0 mm, less than 0.5 mm, less than about 0.25 mm, and less than about 0.1 mm.
• Applicant has developed a system and method that provides a very high rate of thermal conduction forming a large enough temperature differential between the surface and center of an architectural glass sheet to provide strengthening or tempering even in very thin architectural glass sheets.
• sheet thickness also imposes significant limits on the achievable temperature differential during quenching.
• FIG. 1 shows the power required by air blowers (in kilowatts per square meter of glass sheet area) employed to blow sufficient ambient air to "fully temper" soda- lime glass (“SLG”), as a function of glass thickness in millimeters, based on industry standard thermal strengthening processes developed 35 years ago.
• SSG soda- lime glass
• the performance curves of FIG. 2 were published using state of the art glass thermal strengthening equipment.
• This improved equipment continues to use traditional air blown convective processes to cool the glass, but replaces rollers used to support the glass during heating with a system that utilizes air to support the glass during at least the last stages of heating. Without roller contact, the glass can be heated to higher temperatures (and higher softness / lower viscosity) prior to quenching, reportedly allowing the production of fully tempered glass at 2 mm thickness.
• the reported blower power required to strengthen a 2 mm thick sheet is reduced from 1200 kW/m 2 to 400 kW/m 2 at the higher temperatures enabled by using air to support the glass (curve N) as compared to using rollers (curve O).
• FIG. 3 Prior Art
• FIG. 3 shows that the improvement in performance achieved by the state of the art convective tempering process (shown in FIG. 2) is relatively small and simply an incremental change in the previous understanding of the energy needs in convective strengthening of glass sheets.
• FIG. 3 the old and new curves O and N of FIG. 2 are scaled to match the graph of FIG. 1, and overlaid thereon (with the old curve O truncated at the top at 240 kW/m 2 for easier viewing of the new curve N). From FIG.
• Liquid contact strengthening in the form of immersion in liquid baths or flowing liquids, as well as in the form of spraying, has been used to achieve higher cooling rates than convective gas strengthening, but has the drawback of causing excessive thermal variations across a sheet during the cooling process.
• immersion or immersion-like spraying or flowing of liquids large thermal variations over small areas can occur due to convection currents that arise spontaneously within the liquid bath or liquid flow.
• finer spraying the discrete spray droplets and the effects of nozzle spray patterns also produce significant thermal variations. Excessive thermal variations tend to cause glass breakage during thermal strengthening by liquid contact, which can be mitigated by limiting the cooling rates, but limiting cooling rates also lowers the resulting strengths that can be achieved.
• liquid cooling methods such as high cooling rate quenching by oil immersion and various spraying techniques, can alter the glass surface during such cooling, requiring later removal of glass material from the sheet surface to produce a satisfactory finish.
• Solid contact thermal strengthening involves contacting the surface of the hot glass with a cooler solid surface.
• excessive thermal variations like those seen in liquid contact strengthening, can easily arise during the quenching process. Any imperfection in the surface finish of the glass sheet, in the quenching surfaces, or in the consistency of the thickness of the sheet, results in imperfect contact over some area of the sheet, and this imperfect contact may cause large thermal variations that tend to break the glass during processing and may also cause unwanted birefringence if the sheet survives.
• contacting the hot glass sheet with a solid object can lead to the formation of surface defects, such as chips, checks, cracks, scratches, and the like.
• the present disclosure surpasses the traditional processes described above to effectively, efficiently, and evenly thermally strengthen thin architectural glass sheets at commercial scales without generating various flaws common in conventional processes, e.g., without damaging the surface of the architectural glass, without inducing birefringence, without uneven strengthening, and/or without causing unacceptable breakage, etc.
• Previously unobtainable, thin, thermally tempered/strengthened architectural glass sheets can be produced by one or more of the embodiments disclosed herein.
• the systems and processes discussed herein accomplish this by providing very high heat transfer rates in a precise manner, with good physical control and gentle handling of the architectural glass.
• the processes and systems discussed herein utilize a small-gap, gas bearing in the cooling/quenching section that Applicant has identified as allowing for processing thin architectural glass sheets at higher relative temperatures at the start of cooling, resulting in higher thermal strengthening levels.
• this small-gap, gas bearing cooling/quenching section achieves very high heat transfer rates via conductive heat transfer to heat sink(s) across the gap, rather than using high air flow based convective cooling. This high rate conductive heat transfer is achieved while not contacting the architectural glass with liquid or solid material, by supporting the architectural glass on gas bearings within the gap.
• Applicant has also identified that, in at least some embodiments, the processes and systems discussed herein form thermally strengthened architectural glass, specifically thermally strengthened thin architectural glass, having one or more unique properties.
• Some embodiments of architectural glass sheets treated by methods and/or systems according to the present disclosure have higher levels of permanent thermally induced stresses than previously known. Without wishing to be bound by theory, it is believed that the achieved levels of thermally induced stress are obtainable for a combination of reasons.
• the high uniformity of the heat transfer in the processes detailed herein reduces or removes physical and unwanted thermal stresses in the architectural glass, allowing architectural glass sheets to be tempered at higher heat transfer rates without breaking.
• the present methods can be performed at lower architectural glass sheet viscosities (higher initial temperatures at the start of quench), while still preserving the desired architectural glass flatness and form, which provides a much greater change in temperature in the cooling process, thus increasing the heat strengthening levels achieved.
• thermally strengthened architectural glass sheets particularly thin architectural glass sheets
• the thermally strengthened, thin architectural glass sheets formed as discussed herein have one or more unique properties and/or combinations of properties, previously unachievable through conventional thermal or other tempering methods.
• FIG. 4 shows a perspective view of a thermally strengthened architectural glass sheet having a high surface compressive stress and/or a high central tension according to an exemplary embodiment.
• FIG. 4 shows a perspective view of a thermally strengthened architectural glass sheet having a high surface compressive stress and/or a high central tension.
• FIG. 5 is a diagrammatic partial cross-section of thermally strengthened architectural glass sheet 500 according to one or more embodiments.
• Sheet 500 may also be referred to as pane or as a glass-based layer herein.
• a strengthened architectural glass or glass-ceramic article 500 (e.g., sheet, beam, plate), includes a first major surface 510, a second major surface 520 (dotted line to back side of the sheet 500, which may be translucent as disclosed herein), and a body 522 extending therebetween.
• the second major surface 520 is on an opposite side of the body 522 from the first major surface 510 such that a thickness t of the strengthened architectural glass or glass-ceramic sheet 500 is defined as a distance between the first and second major surfaces 510, 520, where the thickness t is also a dimension of depth.
• a width, w, of the strengthened architectural glass or glass-ceramic sheet 500 is defined as a first dimension of one of the first or second major surfaces 510, 520 orthogonal to the thickness t.
• a length, /, of the strengthened architectural glass or glass-ceramic sheet 500 is defined as a second dimension of one of the first or second major surfaces 510, 520 orthogonal to both the thickness t and the width w.
• thickness t of architectural glass sheet 500 is less than length / of architectural glass sheet 500. In other exemplary embodiments, thickness t of architectural glass sheet 500 is less than width w of architectural glass sheet 500. In yet other exemplary embodiments, thickness t of architectural glass sheet 500 is less than both length / and width w of architectural glass sheet 500. As shown in FIG. 5, architectural glass sheet 500 further has regions of permanent thermally induced compressive stress 530 and 540 at and/or near the first and second major surfaces 510, 520, balanced by a region of permanent thermally induced central tensile stress 550 (i.e., tension) in the central portion of the sheet.
• regions of permanent thermally induced compressive stress 530 and 540 at and/or near the first and second major surfaces 510, 520, balanced by a region of permanent thermally induced central tensile stress 550 (i.e., tension) in the central portion of the sheet.
• thickness t of architectural glass sheet 500 ranges from 0.1 mm to 5.7 or 6.0 mm, including, in addition to the end point values, 0.2 mm, 0.28 mm, 0.4 mm, 0.5 mm, 0.55 mm, 0.7 mm, 1 mm, 1.1 mm, 1.5 mm, 1.8 mm, 2 mm, and 3.2 mm.
• Contemplated embodiments include thermally strengthened architectural glass sheets 500 having thicknesses t in ranges from 0.1 to 20 mm, from 0.1 to 16 mm, from 0.1 to 12 mm, from 0.1 to 8 mm, from 0.1 to 6 mm, from 0.1 to 4 mm, from 0.1 to 3 mm, from 0.1 to 2 mm, from 0.1 to less than 2 mm, from 0.1 to 1.5 mm, from 0.1 to 1 mm, from 0.1 to 0.7 mm, from 0.1 to 0.5 mm and from 0.1 to 0.3 mm.
• architectural glass sheets of 3 mm or less in thickness are used.
• the architectural glass thickness is about (e.g., plus or minus 1%) 8 mm or less, about 6 mm or less, about 3 mm or less, about 2.5 mm or less, about 2 mm or less, about 1.8 mm or less, about 1.6 mm or less, about 1.4 mm or less, about 1.2 mm or less, about 1 mm or less, about 0.8 mm or less, about 0.7 mm or less, about 0.6 mm or less, about 0.5 mm or less, about 0.4 mm or less, about 0.3 mm or less, or about 0.28 mm or less.
• thermally strengthened architectural glass sheets have high aspect ratios - i.e., the length and width to thickness ratios are large. Because the thermal tempering processes discussed herein do not rely on high pressures or large volumes of air, various architectural glass sheet properties, such as surface roughness and flatness, can be maintained after tempering by the use of gas bearings and high thermal transfer rate systems discussed herein. Similarly, the thermal tempering processes discussed herein allow high aspect ratio architectural glass sheets (i.e., architectural glass sheets with high ratio of length to thickness, or of width to thickness, or both) to be thermally strengthened while retaining the desired or necessary shape.
• high aspect ratio architectural glass sheets i.e., architectural glass sheets with high ratio of length to thickness, or of width to thickness, or both
• sheets with length to thickness and/or width to thickness ratios of approximately at least 10: 1, at least 20: 1, and up to and over 1000: 1 can be strengthened.
• sheets with aspect ratios of at least 200: 1, at least 500: 1, at least 1000: 1, at least 2000: 1, at least 4000: 1 can be strengthened.
• the length / of the strengthened architectural glass or glass-ceramic sheet 500 is greater than or equal to the width w, such as greater than twice the width w, greater than five times the width w, and/or no more than fifty times the width w.
• the width w of the strengthened architectural glass or glass- ceramic sheet 500 is greater than or equal to the thickness t, such as greater than twice the thickness t, greater than five times the thickness t, and/or no more than fifty times the thickness t.
• the length / of the architectural glass or glass-ceramic sheet 500 is at least 1 cm, such as at least 3 cm, at least 5 cm, at least 7.5 cm, at least 20 cm, at least 50 cm, and/or no more than 50 m, such as no more than 10 m, no more than 7.5 m, no more than 5 m.
• the width w of the architectural glass or glass-ceramic sheet 500 is at least 1 cm, such as at least 3 cm, at least 5 cm, at least 7.5 cm, at least 20 cm, at least 50 cm, and/or no more than 50 m, such as no more than 10 m, no more than 7.5 m, no more than 5 m.
• architectural glass or glass-ceramic is in the form a sheet 500 has a thickness t that is thinner than 5 cm, such as 2.5 cm or less, 1 cm or less, 5 mm or less, 2.5 mm or less, 2 mm or less, 1.7 mm or less, 1.5 mm or less, 1.2 mm or less, or even 1 mm or less in
• contemplated embodiments such as 0.8 mm or less; and/or the thickness t is at least 10 ⁇ , such as at least 50 ⁇ , at least 100 ⁇ , at least 300 ⁇ .
• the architectural glass or glass-ceramic article may be sized other than as disclosed herein.
• the length /, width w, and/or thickness t of the architectural glass or glass-ceramic articles may vary, such as for more complex geometries (see generally FIG. 30), where dimensions disclosed herein at least apply to aspects of the corresponding architectural glass or glass-ceramic articles having the above- described definitions of length /, width w, and thickness t with respect to one another.
• at least one of the first or second surfaces 510, 520 of architectural glass sheet 500 has a relatively large surface area.
• first and/or second surfaces 510, 520 having areas of at least 100 mm 2 , such as at least 900 mm 2 , at least 2500 mm 2 , at least 5000 mm 2 , at least 100 cm 2 , at least 900 cm 2 , at least 2500 cm 2 , at least 5000 cm 2 , and/or no more than 2500 m 2 , such as no more than 100 m 2 , no more than 5000 cm 2 , no more than 2500 cm 2 , no more than 1000 cm 2 , no more than 500 cm 2 , no more than 100 cm 2 .
• the architectural glass or glass-ceramic sheet 500 may have a relatively large surface area; which, except by methods and systems disclosed herein, may be difficult or impossible to thermally strengthen particularly while having the thicknesses, surface qualities, and/or strain homogeneities of the architectural glass sheets discussed herein. Further, except by methods and systems disclosed herein, it may be difficult or impossible to achieve the stress profile, particularly the negative tensile stress portion of the stress profile (see generally FIG. 6), without relying upon ion-exchange or a change in the type of architectural glass.
• the thermally strengthened architectural glass sheets discussed herein may have surprisingly high surface compressive stresses, e.g., in regions 530, 540 shown in FIG. 5, surprisingly high central tensile stresses, e.g., in region 550 shown in FIG. 5, and/or unique stress profiles (see FIG. 6). This is particularly true considering the low thickness and/or other unique physical properties (e.g., very low roughness, high degree of flatness, various optical properties, fictive temperature properties, etc.) of architectural glass sheet 500 as discussed herein.
• unique physical properties e.g., very low roughness, high degree of flatness, various optical properties, fictive temperature properties, etc.
• Compressive stresses of architectural glasses can vary as a function of thickness t of the architectural glasses.
• architectural glasses e.g., architectural glass sheet 500, having a thickness of 3 mm or less have a compressive stress (e.g., surface
• compressive stress of at least, 45 MPa, of at least 60 MPa, of at least 80 MPa, at least 100 MPa, at least 150 MPa, at least 200 MPa, at least 250 MPa, at least 300 MPa, at least 350 MPa, at least 400 MPa, and/or no more than 1 GPa.
• architectural glasses having a thickness of 2 mm or less have a compressive stress of at least 45 MPa, of at least 60 MPa, of at least 80 MPa, at least 100 MPa, at least 150 MPa, at least 175 MPa, at least 200 MPa, at least 250 MPa, at least 300 MPa, at least 350 MPa, at least 400 MPa, and/or no more than 1 GPa.
• architectural glasses having a thickness of 1.5 mm or less have a compressive stress of at least 45MPa, of at least 60 MPa, of at least 80 MPa, at least 100 MPa, at least 150 MPa, at least 175 MPa, at least 200 MPa, at least 250 MPa, at least 300-MPa, at least 350 MPa, and/or no more than 1 GPa.
• architectural glasses having a thickness of 1 mm or less have a compressive stress of at least 45 MPa, of at least 60 MPa, of at least 80 MPa, at least 100 MPa, at least 150 MPa, at least 175 MPa, at least 200 MPa, at least 250 MPa, at least 300 MPa, and/or no more than 1 GPa.
• architectural glasses having a thickness of 0.5 mm or less have a compressive stress of at least 45 MPa, of at least 60 MPa, of at least 50 MPa, at least 80 MPa, at least 100 MPa, at least 150 MPa, at least 175 MPa, at least 200 MPa, at least 250 MPa, and/or no more than 1 GPa.
• the thermally induced central tension in architectural glasses formed by the processes and systems disclosed herein may be greater than 30 MPa, may be greater than 40 MPa, greater than 50 MPa, greater than 75 MPa, greater than 100 MPa. In other embodiments, the thermally induced central tension may be less than 300 MPa, or less than 400 MPa. In some embodiments, the thermally induced central tension may be from about 30 MPa to about 300 MPa, about 50 MPa to about 300 MPa, about 60 MPa to about 200 MPa, about 70 MPa to about 150 MPa, or about 80 MPa to about 140 MPa.
• the thermally strengthened architectural glass sheets have high thinness i.e., are particularly thin. Because very high-heat transfer rates can be applied via the systems and methods discussed herein, significant thermal effects, for example central tensions of at least 10 or even at least 20 MPa, can be produced in sheets of SLG of less than 0.3 mm thickness. In fact, very thin sheets, sheets at least as thin as 0.1 mm, can be thermal
• a conceptual stress profile 560, at room temperature of 25° C and standard atmospheric pressure, of the strengthened architectural glass or glass-ceramic sheet 500 of FIG. 4, shows an interior portion 550 of the strengthened architectural glass or glass-ceramic sheet 500 under positive tensile stress and portions 530, 540 of the strengthened architectural glass or glass-ceramic sheet 500 exterior to and adjoining the interior portion 550 under negative tensile stress (e.g., positive compressive stress).
• negative tensile stress at least in part fortifies the strengthened architectural glass or glass-ceramic sheet 500 by limiting initiation and/or propagation of cracks therethrough.
• tensile stress in the stress profile 560 sharply transitions between the positive tensile stress of the interior portion 550 and the negative tensile stress of the portions 530, 540 exterior to and adjoining the interior portion 550.
• This sharp transition may be understood as a rate of change (i.e., slope) of the tensile stress which may be expressed as a magnitude of stress
• a distance of thickness over which the change occurs such as a distance of 1 mm, such as a distance of 500 ⁇ , 250 ⁇ , 100 ⁇
• the rate of change of the tensile stress does not exceed 7000 MPa divided by 1 mm, such as no more than 5000 MPa divided by 1 mm.
• the difference in peak values of the positive and negative tensile stresses is at least 50 MPa, such as at least 100 MPa, at least 150 MPa, at least 200 MPa, at least 250 MPa, at least 300 MPa, at least 400 MPa, at least
• the architectural glass or glass-ceramic sheet 500 has a peak negative tensile stress of at least 50 MPa in magnitude, such as at least 100 MPa, at least 150 MPa, at least 200 MPa, at least 250 MPa, at least 300 MPa, at least 400 MPa, at least 500 MPa.
• the steep tensile curve transitions generated by the system and method discussed herein are believed to be indicative of the ability to achieve higher magnitudes of negative tensile stress at a surface of an architectural glass sheet for a given thickness and/or to manufacture thinner architectural glass articles to a higher degree of negative tensile stress, such as to achieve a fragmentation potential for dicing as disclosed herein.
• Conventional thermal tempering approaches may be unable to achieve such steep tensile stress curves.
• the high rate of change of tensile stress is at least one of the above-described magnitudes or greater sustained over a thickness-wise stretch of the stress profile 560 that is at least 2% of the thickness, such as at least 5% of the thickness, at least 10% of the thickness, at least 15% of the thickness, or at least 25% of the thickness of architectural glass sheet 500.
• the strengthening extends deep into the strengthened architectural glass or glass-ceramic sheet 500 such that the thickness-wise stretch with the high rate of change of tensile stress is centered at a depth of between 20% and 80%) into the thickness from the first surface, which may further distinguish chemical tempering for example.
• the strengthened architectural glass or glass- ceramic article includes a change in the composition thereof in terms of ion content, conceptually shown as dotted line 562 in FIG. 6. More specifically, the composition of the strengthened architectural glass or glass-ceramic article 500 in such embodiments includes exchanged or implanted ions that influence the stress profile 560. In some such embodiments, the exchanged or implanted ions do not extend fully through the portions 530, 540 of the strengthened architectural glass or glass-ceramic article 500 under the negative tensile stress because the negative tensile stress is also a result of the thermal tempering as disclosed herein.
• the curve of the tensile stress profile 560 with ion exchange strength augmentation includes a discontinuity or sudden change 564 in direction where tangents of the curve differ from one another on either side of the discontinuity or sudden change 564.
• the sudden change 564 is located within the portions 530, 540 under negative tensile stress such that the tensile stress is negative on either side immediately adjacent to the discontinuity or sudden change 564.
• the discontinuity or sudden change 564 may correspond to the depth of the different ion content, however in some such embodiments other parts of the portions 530, 540 under negative tensile stress still have the same composition in terms of ion content as the portion 550 under positive tensile stress.
• the composition of at least a part of the portions 530, 540 of the strengthened architectural glass or glass-ceramic sheet 500, which is under the negative tensile stress and is exterior to and adjoining the interior portion 550 is the same as the composition of at least a part of the interior portion 550, which is under the positive tensile stress.
• at least some of the negative tensile stress of the stress profile is independent of a change in the composition (e.g., ion composition) of the strengthened architectural glass or glass-ceramic sheet 500.
• Such structure may simplify the composition of the strengthened architectural glass or glass-ceramic sheet 500 at least to a degree by providing sufficient strength without and/or with less chemical tempering. Further, such structure may reduce stress concentrations within the strengthened architectural glass or glass-ceramic sheet 500 due to discontinuity/changes in composition, possibly reducing chances of delamination and/or cracking at the composition discontinuity.
• an architectural glass sheet is considered to dice when an area of the architectural glass sheet 25 cm 2 breaks into 40 or more pieces. In some embodiments, dicing is used as a qualitative measure of showing that the architectural glass sheet is "fully tempered” (i.e., for 2 mm or thicker architectural glass, where the architectural glass sheet has a compressive stress of at least 65 MPa or an edge compression of at least 67 MPa). In various embodiments, architectural glass sheet 500 has sufficient tensile stress in region of tensile stress 550 such that a 25 cm 2 piece of architectural glass sheet 500 breaks into 40 or more pieces.
• an architectural glass or glass-ceramic article 610 having properties as disclosed herein with respect to the architectural glass or glass-ceramic sheets, such as sheet 500, has been fractured, such as using a prick punch or other instrument and/or generally in accordance with American National Standards Institute (ANSI) Z97.1 (impact test) and the ASTM 1048 standard.
• the architectural glass or glass- ceramic article 610 has been strengthened to a degree that dicing has occurred upon the fracture, forming a plurality of small granular chunks 616 (e.g., fragments, pieces).
• the architectural glass or glass-ceramic article 610 has a thermally-induced stress sufficient to produce a number of granular chunks 616 that is not less than 40 within an area of 50-by-50 mm of the architectural glass or glass-ceramic article 610 in a fragmentation test in which an impact is applied with a hammer or a punch to initiate cracking of the architectural glass into granular pieces.
• a standard office thumb tack 612, with a metal pin length 614 of about 1 cm is shown for reference.
• the stress profile (see generally FIG. 6) imparts a high fragmentation potential of the strengthened architectural glass or glass-ceramic article 610 such that when fractured the strengthened architectural glass or glass-ceramic article 610 shatters into particularly small granular chunks 616, those having an area on either the first or second surface of less than 90 mm 2 , such as less than 50 mm 2 , such as less than 20 mm 2 , such as less than 10 mm 2 , such as less than 5 mm 2 , and/or at least 10 ⁇ 2 .
• 90 mm 2 such as less than 50 mm 2 , such as less than 20 mm 2 , such as less than 10 mm 2 , such as less than 5 mm 2 , and/or at least 10 ⁇ 2 .
• the fragmentation potential of the strengthened architectural glass or glass-ceramic article 610 is such that at least 20% (e.g., at least 50%, at least 70%, at least 95%) of the granular chunks 616 have an area of at least one of the first or second surfaces of one of the above- described amounts when the strengthened architectural glass or glass-ceramic article is fractured.
• the fragmentation potential of the strengthened architectural glass or glass-ceramic article 610 is such that, when fractured, the strengthened architectural glass or glass-ceramic article 610 shatters into particularly low- volume granular chunks, those having a volume of less than 50 mm 3 , such as less than 40 mm 3 , such as less than 30 mm 3 , such as less than 25 mm 3 , and/or at least a volume of 50 ⁇ 3 .
• the fragmentation potential of the strengthened architectural glass or glass-ceramic article 610 is such that, when fractured, the strengthened architectural glass or glass-ceramic article 610 shatters into at least 100 granular chunks 616 of at least of 50 ⁇ 3 in volume, such as at least 200, at least 400, at least 1000, at least 4000 granular chunks 616 of at least of 50 ⁇ 3 in volume.
• the thermally strengthened architectural glass sheets formed by the systems and methods discussed herein have high fictive temperatures.
• high fictive temperatures of the architectural glass materials discussed herein relate to the high level of tempering, high central tensile stresses and/or high compressive surface stress of architectural glass sheet 500.
• Surface fictive temperatures may be determined by any suitable method, including differential scanning calorimetry, Brillouin spectroscopy, or Raman spectroscopy.
• the architectural glass or glass-ceramic sheet 500 has a portion thereof, such as at or near the first and/or second surfaces 510, 520, that has a particularly high fictive temperature, such as at least 500° C, such as at least 600° C, or even at least 700° C in some embodiments, such as for soda-lime glass.
• a particularly high fictive temperature such as at least 500° C, such as at least 600° C, or even at least 700° C in some embodiments, such as for soda-lime glass.
• the architectural glass or glass-ceramic sheet 500 has a portion thereof, such as at or near the first and/or second surfaces 510, 520, that has a particularly high fictive temperature relative to annealed glass of the same chemical composition, such as at least 10° C greater, at least 30° C greater, at least 50° C greater, at least 70° C greater, or even at least 100° C greater.
• High fictive temperature may be achieved by the presently disclosed inventive technology at least in part due to the rapid transition from the hot to the cooling zones in the strengthening system (see e.g., FIG. 21, FIG. 22 and FIG. 23). Applicant believes that high fictive temperature may correspond or relate to increased damage resistance of glass.
• the peak near 1090 cm “1 in soda-lime glass and in glass 2 corresponds to the 1050 cm “1 peak observed in silica glass.
• ⁇ is the measured peak wavenumber for the peak near 1090 cm "1
• G c is the surface compressive stress measured by any suitable technique, yielding stress-corrected measurement of fictive temperature in °C.As a demonstration of increased damage resistance related to the determined fictive temperature, four glass sheet samples were prepared, two 6 mm soda-lime glass (SLG) sheets by conventional tempering methods to approximately 70 and 110 MPa surface compressive stress (CS), and two 1.1 mm SLG sheets by the methods and systems disclosed herein to about the same levels of CS. Two additional sheets, one of each thickness were used as controls. The surfaces of each test sheet were subjected to standard Vickers indentation.
• the 50% cracking threshold (defined as the load at which the average number of cracks appearing is two out of the four points of the indenter at which cracks tend to initiate) was determined for each sample.
• the Vickers crack initiation threshold improved to greater than 10 N, a 10-fold increase over the Vickers damage resistance imparted by conventional tempering.
• the ⁇ 3 ⁇ 4 minus T g was at least 50°C, or at least 75°C, or at least 90°C, or in the range of from approximately 75°C to 100°C. Even in embodiments comprising lower levels of heat strengthening, the embodied glasses can still provide increased resistance, at levels such as 5 N, for instance.
• the 50% cracking threshold after a 15 second Vickers crack initiation test may be equal to or greater than 5 N, 10 N, 20 N, or 30 N.
• the following non-dimensional fictive temperature parameter ⁇ can be used to compare the relative performance of a thermal strengthening process in terms of the fictive temperature produced.
• FIG. 10 is a plot of 0s for measured surface fictive temperatures as a function of heat transfer rate, h, applied during thermal strengthening for two different glasses. As shown in FIG. 10, the results for the two different glasses overlie each other fairly closely. This means that parameter ⁇ provides a means to compare the fictive temperatures of different glasses compared directly, in relation to the heat transfer rate h required to produce them. The vertical range of results at each h corresponds to variation in the value of T 0 , the initial temperature at the start of quenching.
• parameter 6s comprises from about (e.g., plus or minus 10%) 0.2 to about 0.9, or 0.21 to 0.09, or 0.22 to 0.09, or 0.23 to 0.09, or 0.24 to 0.09, or 0.25 to 0.09, or 0.30 to 0.09, or 0.40 to 0.09, or 0.5 to 0.9, or 0.51 to 0.9, or 0.52 to 0.9, or 0.53 to 0.9, or 0.54 to 0.9, or 0.54 to 0.9, or 0.55 to 0.9, or 0.6 to 0.9, or even 0.65 to 0.9.
• the thermally strengthened architectural glass sheets formed by the systems and methods discussed herein have a high temperability and/or heat transfer value.
• the "specific thermal stress" of a glass is given by:
• a CTE is the low temperature linear CTE (equivalent to the average linear expansion coefficient from 0-300°C for the glass), expressed in 1/°C (°C _1 )
• L TE is the high temperature linear CTE (equivalent to the high-temperature plateau value which is observed to occur somewhere between the glass transition and softening point), expressed in 1/°C (°C _1 )
• E is the elastic modulus of the glass, expressed in GPa (not MPa) (which allows values of the (non- dimensional) parameter Wto range generally between 0 and 1)
• the thermal strengthening process and resulting surface compressive stresses were modeled for glasses having varying properties to determine the tempering parameter, ⁇ .
• the glasses were modeled at the same starting viscosity of 10 8 2 Poise and at varying heat transfer coefficients.
• the properties of the various glasses are shown in Table II, together with the temperature for each glass at 10 8 2 Poise and the calculated value of the temperability parameter ⁇ for each.
• the constants Pi, P2 are graphed as functions of h in FIGS. 12 and 13, respectively.
• a similar expression may be used to predict the central tension (CT) of a thermally strengthened architectural glass sheet, particularly at a thickness of 6 mm and less, and the thermal transfer coefficient, such as 800 W/m 2 K and up, by simply dividing the compressive stress predicted under the same conductions by 2.
• CT central tension
• expected central tension may be given by
• h and her may have the same value for a given physical instance of thermal strengthening. However, in some embodiments, they may vary, and providing separate variables and allowing variation between them allows for capturing, within descriptive performance curves, instances in which the typical ratio of 2: 1 CS/CT does not hold. [00113]
• One or more embodiments of the currently disclosed processes and systems have produced thermally strengthened SLG sheets at all of the heat transfer rate values (h and her) shown in Table III.
• the heat transfer value rates (h and her) may be from about 0.024 to about 0.15, about 0.026 to about 0.10, or about 0.026 to about 0.075 cal/s cm 2 o C.
• FIG. 14 shows the newly opened performance space in MPa of surface compression of a glass sheet as a function of thickness t (in mm), by a graph of C(h,t) ⁇ W(SLG) for selected values of h according to equations 6-9 above, with W(SLG) corresponding to the value of ⁇ SLG in Table II.
• the traces labeled GC represent the estimated range of maximum stresses versus thinness of SLG sheets achievable by gas convective tempering, from 0.02 cal/s cm 2 o C (or 840 W/m 2 K) to 0.03 cal/s cm 2 o C or 1250 W/m 2 K, assuming that these levels of heat transfer coefficient can be employed in that process at a heated glass viscosity of 10 8 2 Poises or about 704°C, a temperature above the capability of convective gas processes.
• Examples of highest reported sheet CS values based on gas convective tempering processes are shown by the triangle markers labeled Gas in the legend.
• the value 601 represents advertised product performance capability of commercial equipment, while the value 602 is based on an oral report at a glass processing conference.
• the trace labeled LC represents the curve of maximum stresses versus thinness of SLG sheets estimated to be achievable by liquid contact tempering, given by a heat transfer rate h of 0.0625 cal/s cm 2 o C (or about 2600
• the trace labeled 704 represents stresses achievable by one or more embodiments of the presently disclosed methods and systems at a heat transfer rate of 0.20 cal/s cm 2 o C (or about 8370 W/m 2 K) and an initial temperature, just before quenching, of 704 °C.
• the level of stress on the architectural glass sheet thus achievable represents almost the same scope of improvement over liquid tempering strength levels as liquid tempering represents over state of the art gas convective tempering.
• the trace labeled 704 is not an upper limit - embodiments have been shown to be viable above this value due to the good control of form and flatness achievable in a small-gap gas bearing thermal strengthening at even higher temperatures (at lower viscosities of the architectural glass).
• the trace labeled 730 shows some of the additional strengthening performance achieved by a heat transfer rate of 0.20 cal/s cm 2 o C (or about 8370 W/m 2 K) at a starting temperature for a SLG sheet of 730°C, very near or above the softening point of the architectural glass.
• a heat transfer rate of 0.20 cal/s cm 2 o C or about 8370 W/m 2 K
• Significant improvements in compressive stress and thus in architectural glass sheet strength are thus achieved particularly by the combination of high heat transfer rate and the use of high initial temperatures enabled by the good handling and control of sheet flatness and form in a tight gas bearing— and the improvements are particularly striking at thickness 2 mm and below.
• FIG. 15 shows the traces of FIG. 14 explained above, at 2 mm and below, but with compressive stress as a function of thickness plotted for selected examples of tempered glass sheets produced by one or more embodiments of the present disclosure, showing the extreme combination of thermal strengthening levels and thinness enabled by the present disclosure.
• thermally strengthened architectural glass sheets disclosed herein such as sheet 500
• the processes and methods disclosed herein can thermally strengthen a sheet of architectural glass without increasing the surface roughness of the as-formed surfaces.
• incoming float architectural glass air-side surfaces and incoming fusion formed architectural glass surfaces were characterized by atomic force microscopy (AFM) before and after processing.
• R a surface roughness was less than 1 nm (0.6-0.7 nm) for incoming 1.1 mm soda-lime float architectural glass, and the Ra surface roughness was not increased by thermal strengthening according to the present processes.
• thermally strengthened architectural glass sheets have a surface roughness on at least a first surface in the range from 0.2 to 1.5 nm R a roughness, 0.2 to 0.7 nm, 0.2 to 0.4 nm or even such as 0.2 to 0.3 nm, over at least an area of 10 x 10 ⁇ .
• Surface roughness may be measured over an area of 10 x 10 ⁇ in exemplary embodiments, or in some embodiments, 15 x 15 ⁇ .
• thermally strengthened architectural glass sheets disclosed herein have both high thermal stresses and low, as-formed surface roughness and/or coated surfaces.
• the processes and methods disclosed herein can thermally strengthen a sheet of architectural glass without increasing the surface roughness of smooth as-formed or as-delivered surfaces of architectural glass sheets, and likewise without damaging sensitive low-E or anti- reflective or other coatings.
• Incoming float architectural glass air-side surfaces, and incoming fusion- formed architectural glass surfaces, were characterized by atomic force microscopy (AFM) before and after processing.
• AFM atomic force microscopy
• R a surface roughness was less than 1 nm (such as 0.6 to 0.7 nm) for incoming on the air side of 1.1 mm soda-lime float architectural glass and was not increased by thermal strengthening according to the present disclosure.
• R a surface roughness was less than 0.3 nm (such as 0.2 to 0.3 nm) incoming on 1.1 mm sheets of fusion-formed architectural glass and likewise was not increased by thermal strengthening according to this disclosure.
• thermally strengthened architectural glass sheets have surface roughness on at least a first surface in the range of at least 0.2 nm and/or no more than 1.5 nm R a roughness, such as no more than 0.7 nm, such as no more than 0.4 nm or even such as no more than 0.3 nm, or have thermally
• strengthened sheets having coatings thereon of the type that may be applied before strengthening, or have combinations of these low roughness values and coatings, are obtained from the present process used with corresponding architectural glass sheets as starting material. It is Applicant's understanding that such preservation of surface quality and/or surface coating(s) previously required use of convective gas tempering or perhaps a low heat transfer liquid tempering process, which produces limited thermal strengthening effects relative to the total range available with the present processes and methods.
• the thermally strengthened architectural glass sheets described herein have high flatness.
• the strengthening system discussed herein utilizes controlled gas bearings to support the architectural glass material during transporting and heating, and in some embodiments, can be used to assist in controlling and/or improving the flatness of the architectural glass sheet, resulting in a higher degree of flatness than previously obtainable, particularly for thin and/or highly strengthened architectural glass sheets.
• sheets at least 0.6 mm can be strengthened with improved post-strengthening flatness.
• thermally strengthened architectural glass sheets embodied herein can comprise
• TIR total indicator run-out
• flatness is measured along any 50 mm or less profile of the architectural glass sheet.
• sheets with thickness disclosed herein have flatness 200 ⁇ TIR or less within a 20 mm length on one of the first or second surfaces, such as flatness 100 ⁇ TIR or less, flatness 70 ⁇ TIR or less, flatness 50 ⁇ TIR or less.
• the strengthened architectural glass or glass- ceramic articles discussed herein have a high-degree of dimensional consistency such that the thickness t thereof along a 1 cm lengthwise stretch of the body 522 does not change by more than 50 ⁇ , such as, by not more than 10 ⁇ , not more than 5 ⁇ , not more than 2 ⁇ .
• Such dimensional consistency may not be achievable for given thicknesses, areas, and/or magnitudes of negative tensile stress, as disclosed herein, by solid quenching due to practical considerations, such as cooling plate alignment and/or surface irregularities that may distort the dimensions.
• the strengthened architectural glass or glass- ceramic articles discussed herein have at least one major surface (e.g., first and second surfaces 510, 520 of the strengthened architectural glass or glass-ceramic sheet 500 in FIG. 4) that is flat such that a 1 cm lengthwise profile therealong stays within 50 ⁇ of a straight line, such as within 20 ⁇ , 10 ⁇ , 5 ⁇ , 2 ⁇ ; and/or a 1 cm widthwise profile therealong stays within 50 ⁇ of a straight line, such as within 20 ⁇ , 10 ⁇ , 5 ⁇ , 2 ⁇ .
• first and second surfaces 510, 520 of the strengthened architectural glass or glass-ceramic sheet 500 in FIG. 4 that is flat such that a 1 cm lengthwise profile therealong stays within 50 ⁇ of a straight line, such as within 20 ⁇ , 10 ⁇ , 5 ⁇ , 2 ⁇ ; and/or a 1 cm widthwise profile therealong stays within 50 ⁇ of a straight line, such as within 20 ⁇ , 10 ⁇ , 5 ⁇ , 2 ⁇
• Such high flatness may not be achievable for given thicknesses, areas, and/or magnitudes of negative tensile stress, as disclosed herein, by liquid quenching due to practical considerations, such as warping or bending of the architectural glass strengthened in these processes due to convective currents and associated forces of the liquid.
• CTE architectural glass sheets Another aspect comprises thermally strengthened low coefficient of thermal expansion (CTE) architectural glass sheets.
• CTE low coefficient of thermal expansion
• thermal strengthening effects are significantly dependent upon the CTE of the architectural glass of which the architectural glass sheet is comprised.
• thermal strengthening of low CTE architectural glasses may provide strengthened architectural glass compositions having advantageous properties, such as increased chemical resistance, or better compatibility with electronic devices due to low alkali content.
• Architectural glass sheets having CTEs of 65, 60, 55, 50, 45, 40, and even SS x lO "6 ⁇ "1 and below are capable of safety-glass like break patterns ("dicing") at thicknesses of less than 4 mm, less than 3.5 mm, less than 3 mm, and even at 2 mm or less.
• the compressive stress of low CTE architectural glasses can comprise at least 50 MPa, at least 100 MPa, at least 125 MPa, at least 150 MPa, at least 200 MP a, at least 250 MPa, at least 300 MPa, or at least 400 MPa for architectural glass sheets having a thickness of no more than 1 cm, no more than 5 mm, no more than 3 mm, no more 2 mm, no more than 1.5 mm, no more than 1 mm, no more than 0.75 mm, no more than 0.5 mm, no more than 0.3 mm, no more than 0.2 mm, or no more than 0.1 mm.
• Architectural glass sheets formed according to the present disclosure have a multitude of applications, for example in single and multi-pane windows, such as architectural glass- interlayer-architectural glass laminates used in architectural glass panes. Stronger and thinner laminates can be produced, resulting in weight and cost savings and fuel efficiency increases. Desirably, a thermally strengthened thin sheet may be cold bent and laminated to a formed thicker architectural glass, providing an easy and reliable manufacturing process not requiring any hot forming of the thin sheet.
• Table IV shows results obtained by the methods of the present disclosure (indicated as “Source of Method” I in the table), and a figure of merit, Alpha, that is a rough measure of the coefficient of heat exchange obtained within the tempering process.
• Alpha is given by:
• CS physical compressive stress (in MPa)
• t thickness in millimeters
• CTE the coefficient of thermal expansion in °C _1
• E the elasticity of the glass in (MPa), and yields units in °C/mm.
• Samples 1 and 3 are repeatable values obtained from the disclosed processes, sample 1 using air and sample 3 using helium as the gas in the process.
• Sample 2 represents a "champion" value using air within the present process, that is, not reliably repeatable to date.
• Glass samples processed by the processes of the present disclosure (samples 1-3) all exceeded an Alpha at 117 °C/mm. Applicant believes that the slope of Alpha with thickness may have an inherent trend lower with lower glass thickness.
• Architectural glass disclosed herein has an Alpha of greater than 20t+77, where t is thickness of the glass, in mm, in some embodiments.
• a process for strengthening an architectural glass sheet comprises supporting or guiding at least a portion of an architectural glass sheet, such as architectural glass sheet 500, into a cool or quenching zone in which the sheet is rapidly cooled creating a strengthened architectural glass sheet having one or more of the properties discussed herein.
• the architectural glass sheet is supported at least in part by a flow or a pressure of a gas delivered to a gap between the surfaces of the architectural glass sheet and one or more heat sinks.
• the temperature of the architectural glass sheet is above the transition temperature of the architectural glass when the sheet is moved into the cool zone, and in various embodiments, the architectural glass sheet is cooled within the cooling zone by thermal conduction more than by convection.
• Conduction is a process of heat transfer where energy is transmitted through interactions between adjacent molecules
• convection is a process of heat transfer where energy is communicated via motion of a fluid (e.g., air, helium, etc.), such as where heated fluid moves away from a heat source and is replaced by cooler fluid.
• a fluid e.g., air, helium, etc.
• an overall process for strengthening an architectural glass sheet comprises heating an architectural glass sheet in a hot zone and then cooling the architectural glass sheet in a cooling zone.
• the architectural glass is heated sufficiently to bring the architectural glass sheet above the transition temperature, and then moved into a cooling zone.
• the architectural glass can be transitioned from the hot zone to a cool zone through a transition zone.
• the surfaces of the architectural glass sheet are positioned adjacent to heat sinks, one on either side of the architectural glass sheet, each with a gap in between one of the architectural glass surfaces and an opposing surface of the heat sink.
• Gas is delivered into the gaps through multiple apertures in the heat sinks, and in some embodiments, this delivered gas forms an air bearing which supports the architectural glass between the heat sinks such that the architectural glass surfaces are not in contact with the heat sinks.
• the architectural glass sheet is cooled by conduction more than by convection and is cooled sufficiently to fix or create a thermally induced surface compression and a thermally induced central tension of the sheet which provides the increased strength as discussed herein.
• primarily cooling via conduction is achieved by having a very low gap size within the cooling zone such that the architectural glass sheet is close to, but not touching, the opposing surfaces of the heat sinks.
• An apparatus for enabling the processes described can include a heating zone for heating an architectural glass sheet to a temperature above the transition temperature and a cooling zone for cooling the heated architectural glass sheet to provide a strengthened architectural glass sheet.
• the apparatus can include an optional transition zone between the heating zone and the cooling zone.
• the cooling zone may include a heat sink having a pair of opposing surfaces defining a gap, within which the heated architectural glass sheet is received.
• the cooling zone can comprise a pair of gas bearings disposed on opposite sides of that gap that acts to support the architectural glass sheet within the gap.
• the gap can be configured to cool the heated architectural glass sheet by conduction more than by convection.
• the gas bearings can include a plurality of apertures for delivering the gas to the gap, and the gas bearing surfaces act as the heat sinks, capable of conducting heat away from the heated architectural glass sheet by conduction more than by convection.
• the thermal tempering processes disclosed herein enable particularly high levels of strengthening in large-area articles (e.g., sheets) that may be too large for strengthening via conventional thermal tempering methods, such as due to alignment limitations of contact quench equipment, cooling rate limitations of conventional convection systems, and/or warping damage associated with liquid quench tempering.
• the processes disclosed herein uniquely allow high levels of strengthening in particularly thin sheets that may be too thin for strengthening via conventional tempering methods, such as due sensitivity to breakage or fracture of the thin architectural glass or glass ceramic articles during the strengthening process and associated contact forces with solid or liquid quenching and/or due to the cooling rate limitations of conventional convection tempering.
• the method or process 100 includes a step 140 of providing an architectural glass sheet that is at a temperature above a transition temperature of the architectural glass sheet.
• the method or process 100 also includes the step 160 of supporting an architectural glass sheet at least in part by a gas (through gas flow and pressure).
• Step 160 includes, while the architectural glass sheet is support by the gas, cooling the sheet: 1) by conduction more than by convection through the gas to a heat sink, and 2) sufficiently to create or fix a thermally-induced surface compression stress and a thermally-induced central tension stress, of the sheet when at ambient temperature.
• the method can include the step 110 of heating an architectural glass sheet sufficiently such that the sheet is above a transition temperature of the architectural glass.
• the method 100' further comprises, in step 120, providing a heat sink (whether as a single piece or in separate pieces) having first and second heat sink surfaces (see generally FIGS. 21-25), each having apertures therein.
• the method further includes positioning a first sheet surface facing a first heat sink surface across a first gap and, in step 130B, positioning the second sheet surface facing a second heat sink surface across a second gap.
• the heat sink surfaces can include apertures and/or can be porous.
• the method 100' can further include, in step 160, cooling the sheet, by conduction more than by convection through a gas to the respective heat sink surfaces, sufficiently to strengthen the architectural glass (e.g., to sufficiently create or fix in the sheet a thermally-induced surface compression stress and a thermally-induced central tension stress).
• the step 160 also can include delivering the gas to the first and second gaps through the apertures or porous heat sink, and in some such embodiments, the gas is delivered to form air bearings that support the architectural glass sheet adjacent the heat sinks. In some embodiments, the gas is delivered only through the apertures of the heat sink or only through the pores or pores and apertures of the porous heat sink.
• gas flow and gap size can be selected, controlled or optimized for other purposes, such as for controlling stiffness of the gas cushion in the gap, for supporting the sheet, for flattening or otherwise shaping a sheet, for optimizing heat conduction, for maintaining sheet flatness and/or shape during thermal strengthening, and/or for balancing ease of sheet handling with high cooling rates.
• helium becomes an economically viable alternative to air in the system of the present disclosure due to the very low gas flow rates that support the gas bearing, and in such embodiments, helium offers thermal conductivity about five times that of air. Even helium with prices assumed at multiples of those available today becomes an economically viable alternative at the low flow rates of the system of the present disclosure.
• the systems and methods discussed herein decrease the potential risk of deformation of hot thin sheets of architectural glass typically caused by the high speed, high volume air flows needed in conventional convection based tempering systems. This also allows softer, higher temperature architectural glass sheets to be handled with no or minimal distortion, further improving the achievable degree of strengthening. Eliminating high air flow rates also eases problems sometimes seen in transporting the sheet into the quenching chamber (moving against the high air flow) and in keeping the high-flow, cooler air from entering into and cooling the adjacent parts of the furnace used to heat the sheet.
• conduction through a gas
• a gas may mitigate contact damage, warping, shaping, etc. associated with conventional liquid contact or solid contact quench tempering.
• Use of a gas as an intermediate conductor preserves the surface quality of the processed articles by avoiding solid-to-solid contact. Mediating the high conduction rates through a gas also avoids liquid contact.
• Some types of liquid quenching can introduce unwanted distortions, spatial variation in tempering and contamination of the architectural glass surfaces.
• solid- or liquid- contact may be included.
• Points A and B of FIG. 18 and FIG. 19 represent a high-end estimate of peak power use of the air bearing, per square meter of architectural glass sheet, by a compressed air supply at relatively high flow. Practical low-end peak power use of compressed air could be as little as 1/16 of the values shown. Points A and B do not include active cooling of the heat sink, however, which can be included in some embodiments, especially where a machine is in continuous, quasi-continuous or high frequency operation.
• points A and B' represent the conservatively estimated peak power levels for operation of the air bearing at points A and B when active cooling of the heat sink surfaces is factored in, assuming the thermal load equivalent of a 300 °C drop in architectural glass sheet temperature is accomplished by an active cooling system having a thermal-to-mechanical (or electrical) efficiency ratio of 7.5 to 1, within a time limit of 2.1 seconds for point A and within 1 second for point B'. (These points correspond approximately to architectural glass sheets actually tempered in the apparatus described herein.) [00139] Although the four points within region R of FIG. 18 and FIG.
• the difference in total energy demands would tend to be greater than the difference for peak power demand, which is represented in the figure.
• the processes described herein have peak powers of less than 120 KW/m 2 , less than 100 KW/m 2 , less than 80 KW/m 2 to thermally strengthen an architectural glass sheet of 2 mm thickness or less.
• heat transfer from the thin architectural glass sheet in the system and process of the present disclosure includes a conduction component, a convection component and a radiant component.
• the thermal tempering system of the present disclosure provides for thin architectural glass tempering by utilizing conductive heat transfer as the primary mechanism for quenching the thin architectural glass sheets.
• the thermal conductivity of the gas within the gap must be evaluated in the direction of conduction, which is along a thermal slope.
• Air at high temperature, at or near the surface of the sheet being cooled has significantly higher thermal conductivity than air at a lower temperature, such as air at or near room temperature at or near the surface of the heat sink (the nominal thermal conductivity of (dry) room temperature air (25°C) is approximately 0.026 W/m K).
• the nominal thermal conductivity of (dry) room temperature air (25°C) is approximately 0.026 W/m K.
• An approximation that assumes air over the whole gap to be at the average temperature of the two facing surfaces at the start of cooling is used.
• an architectural glass sheet may be at a temperature of 670°C, for example, while the heat sink surface may start at 30°C, for example. Accordingly, the average temperature of the air in the gap would be 350°C, at which dry air has a thermal conductivity of about 0.047 W/m K; more than 75% higher than its thermal conductivity at room
• Q CO nd the conductive component of the rate of heat transfer through a gap of distance g which gap has an area A g (in a direction everywhere perpendicular to the direction of the gap distance g) may be given by:
• Ts is the temperature of the architectural glass surface
• T H s is the temperature of the heat sink surface (or the heat source surface, for other embodiments).
• the effective heat transfer coefficient for conduction across the gap is the thermal conductivity of the medium in the gap (air in this case) (in units of W/mK) divided by the length of the gap (in meters), giving a value of Watts per meter squared per degree of temperature difference.
• Table V shows the heat transfer coefficients (k/g), due to conduction alone, for air and helium filled gaps of gap sizes from 10 ⁇ up to 200 ⁇ in steps of 10 ⁇ each.
• FIG. 20 shows an industry-standard curve from about 35 years ago (with reference line at 2 mm added) showing the heat transfer coefficient required to fully temper a sheet of glass, as a function of thickness in mm, under certain assumed conditions.
• Table V shows an air-filled gap of approximately 40 ⁇ can allow full tempering of 2 mm thick architectural glass by conduction. While slightly less than 40 micrometers is a rather small gap, planar porous air bearings in conveyor applications may generally be reliably run with gaps of as low as 20 micrometers. Thus 37 micrometers is achievable for an air gap fed by pores in the heat sink surface.
• helium or hydrogen, with similar thermal conductivity
• a gap of about 200 ⁇ can be used to fully temper 2 mm thick architectural glass.
• helium or hydrogen as the gas allows for a gap size about 5 times larger for the same heat transfer coefficient.
• using helium or hydrogen as the gas in the gap increases the heat transfer coefficient available for quenching by about 5 times at the same gap size. So even with air the spacing is not impractical, and with high conductivity gases, the gap spacing is relatively easy to achieve, even for sheet thicknesses smaller than 2 millimeters.
• another embodiment includes heating (or heating and/or cooling) through a gas by conduction more than by convection.
• the convective Q CO nv component of the rate of heat transfer across the gap (or gaps) may be given by:
• m is the mass flow rate of the gas
• Cp is the specific heat capacity of the gas
• T is the inlet temperature of the gas as it flows into the gap
• e is the effectiveness of the heat exchange between the gas flowing in the gap, the sheet surface and the surface of the heat sink/source (the "walls" of the gap).
• the value of e varies from 0 (representing zero surface-to-gas heat exchange) to 1 (representing the gas fully reaching the temperature of the surfaces).
• the value of e can be computed by those skilled in the art of heat transfer using, for example, the e-NTU method.
• the mass flow rate m of the gas should be less than 2kA g /gC p , or 2k/gC p per square meter of gap area.
• B is a positive constant less than one and greater than zero, specifically having a value of 2/3 or less, or even
• m should be kept as low as possible, consistent with the needs of using the gas flow to control the position of the architectural glass sheet (e.g., sheet 200 shown in
• FIG. 21 relative to the heat sink surface(s)) (e.g., heat sink surfaces 201b, 202b, shown in FIG.
• the ratio of convective cooling to conductive cooling can be any value from less than one to lxl 0 "8 .
• B is less than 0.9, 0.8, 0.7, 0.6, 0.5, 0.4, 0.1, 5xl0 "2 , lxlO "2 , 5xlO "3 , lxlO "3 , 5xl0 "4 , lxlO "4 , 5xl0 "5 , 5 6 6 7 7 8 8
• m is minimized, consistent with the needs of using the gas flow to support and control the sheet position relative to the heat sink surface(s). In other embodiments, m should be selected to control the position of the heat exchange surfaces themselves, relative to the sheet.
• the mass flow rate m of the gas within the conductive-based cooling system of the present disclosure is substantially lower as compared to the conventional convection-based tempering systems.
• This substantially lower gas flow rate allows the conductive system to be operated at substantially reduced power usage, as discussed herein.
• the reduced gas flow rate also results in a substantially quieter cooling system as compared to a conventional convective cooling system.
• the decrease in noise may increase operator safety by reducing the potential for hearing damage and even reducing or eliminating the need for operators to use hearing protection.
• the architectural glass sheet has first and second sheet surfaces, and cooling of the architectural glass sheet is performed by positioning the first sheet surface (e.g., a lower surface of the architectural glass sheet) adjacent to a first heat sink surface (e.g., a surface of a lower heat sink) such that a first gap is located between the first sheet surface and the first heat sink surface and by positioning the second sheet surface (e.g., an upper surface of the architectural glass sheet) adjacent to a second heat sink surface (e.g., a surface of an upper heat sink) such that a second gap is located between the second sheet surface and the second heat sink surface.
• first sheet surface e.g., a lower surface of the architectural glass sheet
• a first heat sink surface e.g., a surface of a lower heat sink
• second sheet surface e.g., an upper surface of the architectural glass sheet
• a second heat sink surface e.g., a surface of an upper heat sink
• the first gap has a length across the first gap of g ⁇ and an area of the first gap of A g i
• the second gap has a length across the second gap of g 2 and an area of the second gap of A g2 .
• a first flow of a first gas to the first gap is provided, and a second flow of a second gas to the second gap is provided.
• the first gas has a heat capacity C p i and a thermal conductivity k ⁇ , and the first flow is provided at a mass flow rate rh ⁇ .
• fh ⁇ is greater than zero and less than ⁇ 2k 1 A g i)l ⁇ g 1 C p i).
• the second gas has a heat capacity C P2 and a thermal conductivity k 2 , and the second flow is provided at a mass flow rate m 2 .
• m 2 is greater than zero and less than ⁇ 2k 2 A gl g 2 C P2 ).
• the first and second flows contact the architectural glass sheet such that the architectural glass sheet is supported without touching the heat sink surfaces.
• the sheet is cooled by conduction more than by convection in a manner to create a surface compressive stress and a central tension of the sheet.
• a hot glass sheet 200 has its first and second (major) surfaces 200a, 200b each facing a respective first and second surface 201b, 202b of respective first and second heat sinks 201a, 202a across respective gaps 204a and 204b.
• Gas 230 is fed through the first and second surfaces 201b, 202b as represented by the arrows, to supply the gaps 204a, 204b, and to assist in keeping the architectural glass sheet centered or otherwise positioned between the heat sinks 201a, 202a.
• the air or other gas may leave passing by the edges of the heat sinks 201a, 202a as shown by arrows 240.
• the architectural glass sheet 200 will be cooled more by conduction than convection.
• architectural glass sheet 200 is cooled by heat sinks 201a and 202a such that more than 20%, specifically more than 50%, and more specifically more than 80%, of the thermal energy leaving a heated article, such as architectural glass sheet 200, crosses the gaps, such as gaps 204a and 204b, and is received by the heat sink 201a and 202a.
• the gaps 204a, 204b are configured to have a thickness or distance across the gap sufficient such that the heated architectural glass sheet is cooled by conduction more than by convention.
• size of gaps 204a, 204b generally is the distance between the major architectural glass surfaces and the opposing heat sink surfaces.
• gaps 204a and 204b may have a thicknesses of about (e.g., plus or minus 1%) 100 ⁇ or greater (e.g., in the ranges from about 100 ⁇ to about 200 ⁇ , from about 100 ⁇ to about 190 ⁇ , from about 100 ⁇ to about 180 ⁇ , from about 100 ⁇ to about 170 ⁇ , from about 100 ⁇ to about 160 ⁇ , from about 100 ⁇ to about 150 ⁇ , from about 110 ⁇ to about 200 ⁇ , from about 120 ⁇ to about 200 ⁇ , from about 130 ⁇ to about 200 ⁇ , or from about 140 ⁇ to about 200 ⁇ ).
• gaps 204a and 204b may have a thicknesses of about (e.g., plus or minus 1%) 100 ⁇ or less (e.g., in the ranges from about 10 ⁇ to about 100 ⁇ , from about 20 ⁇ to about 100 ⁇ , from about 30 ⁇ to about 100 ⁇ , from about 40 ⁇ to about 100 ⁇ , from about 10 ⁇ to about 90 ⁇ , from about 10 ⁇ to about 80 ⁇ , from about 10 ⁇ to about 70 ⁇ , from about 10 ⁇ to about 60 ⁇ , or from about 10 ⁇ to about 50 ⁇ ).
• Heat sinks 201a, 202a may be solid or porous configurations. Suitable materials include, but are not limited to, aluminum, bronze, carbon or graphite, stainless steel, etc. Heat sink dimensions may be designed to be sufficient to address the size of the architectural glass sheet and to efficiently and effectively transfer heat without changing the heat sink temperature significantly. In the case where heat sinks 201a and/or 202a are porous, they may still include additional apertures or holes for flowing gas or may use the porous structure to provide flow, or both. In some embodiments, the heat sinks further comprise passages to allow fluid flow for controlling the temperature of the heat sink, described in more detail in FIGS. 23-25 and below.
• apertures may be less than 2 mm, less than 1.5 mm, less than 1 mm, less than 0.5 mm, less than 0.25 mm, or less than or equal to 200, 150, 100, 50, 30, 20, or 10 ⁇ , when measured in the smallest direction (e.g., diameter in the case of circular apertures).
• the apertures are from about (e.g., plus or minus 1%) 10 ⁇ to about 1 mm, about
• Spacing between adjacent apertures 206 can be from about (e.g., plus or minus 1%) 10 ⁇ to about 3 mm, about 20 ⁇ to about 2 mm, or about 50 ⁇ to about 1 mm, measured edge- to-edge of apertures.
• Small apertures or pores may function as individual flow restrictors, providing high-performance, gas-bearing-type dynamics, such as high levels of stiffness and consistency of support of the sheet to position the sheet and control gap size, allowing for high homogeneity of thermal strengthening effects to avoid or reduce stress birefringence. Further, because very small pores or apertures may be used, the relative amount of solid matter at the surface of the heat sink facing the sheet surface across the gap(s) can be maximized, thereby increasing conductive heat flow.
• apertures 206 as the only path for providing gas to the gaps 204a, 204b, and desirably using apertures 206 that lie in directions close to normal to the heat sink surface 201b, 202b, ensures that air-bearing type dynamics are optimized, and not compromised by gas flows from larger apertures, or from sources other than through the heat sink surface(s) 201b, 202b adjacent to the sheet 200, or by other excessive lateral flow.
• gas may be provided to the gaps 204a, 204b via other sources, such as in addition to the apertures 206 or pores. Accordingly, aspects of the present disclosure allow for power and energy savings by use of low gas flows and solid-gas-solid conduction, such as relative to conventional convective tempering processes.
• FIGS. 22-25 show an exemplary embodiment of an architectural glass strengthening system 300 according to this disclosure.
• FIG. 22 shows a schematic cross-sectional diagram of the system 300, in which an architectural glass sheet can be cooled via conduction of heat from the architectural glass sheet, through a gas into a conductive heat sink.
• the apparatus includes a hot zone 310, a cold zone 330, and a transition gas bearing 320.
• Transition gas bearing 320 moves or directs an architectural glass article (e.g., architectural glass sheet 400a) from the hot zone 310 to the cold zone 330 such that no contact or substantially no contact occurs between the architectural glass and the bearings.
• the hot zone 310 has gas bearings 312 each fed from a hot zone plenum 318, and the bearings 312 have cartridge heaters 314 inserted into holes through the bearings 312, which serve to heat the hot zone gas bearings 312 to a desired starting process temperature.
• An architectural glass sheet (hot zone) 400a is kept between the hot zone gas bearings 312 for a duration long enough to bring it to a desired pre-cooling temperature (e.g., above the transition temperature).
• heating the sheet in the hot zone may be done predominantly via conduction of heat from a heat sink through a thin gas barrier.
• the conductive heating processes used in the hot zone can be similar to, but the reverse of the cooling processes described herein (e.g., pushing heat into the architectural glass sheet).
• gaps 316, between the hot zone gas bearings 312 and the architectural glass sheet 400a may be relatively large, on the order of 0.05" (1.27 mm) to 0.125" (3.175 mm) or greater, since the architectural glass sheet 400a may be heated up relatively slowly and thermal radiation from the hot gas bearings 312 into the architectural glass sheet 400a is adequate for this purpose.
• hot zone gap size may be as small as 150 microns per side or 500 microns per side. Smaller gaps may be advantageous, in some embodiments, because they enable the bearings to have better "stiffness" - i.e., ability to centralize the architectural glass and therefore flatten it while it is in its softened state.
• the process may re-form the architectural glass sheets - flattening them - in the initial heating step, for example via the pressure supplied by the gas bearings 312.
• the top and bottom hot zone bearings may be on actuators, allowing for changing the gap width in a continuous manner or, alternatively, allowing the architectural glass to be brought into the hot zone when the gap is large and then compressing the gap to flatten the architectural glass while it is still soft.
• Process temperatures are dependent on a number of factors, including architectural glass composition, architectural glass thickness, architectural glass properties (CTE, etc.), and desired level of strengthening.
• the starting process temperature may be any value between the architectural glass transition temperature and the Littleton softening point, or in some embodiments, even higher.
• system 300 heats the architectural glass sheet 400a to a temperature between about (e.g., plus or minus 1%) 640 to about 730°C or between about 690 to about 730°C.
• system 300 heats the architectural glass sheet 400a to a temperature from about (e.g., plus or minus 1%) 620 to about 800°C, about 640 to about 770°C, about 660 to about 750°C, about 680 to about 750°C, about 690 to about 740°C, or about 690 to about 730°C.
• the architectural glass sheet 400a is heated to its desired starting process temperature (e.g., above the architectural glass transition temperature), and it is then moved from the hot zone 310 to the cold zone 330 using any suitable means.
• moving the architectural glass sheet 400a from the hot zone 310 to the cold zone 330 may be accomplished by, for example (1) tilting the entire assembly such that gravity acting on the architectural glass sheet forces it to move to the cold zone, (2) blocking off the gas flow from the leftmost exit of the hot zone 310 (the sides are enclosed in this embodiment), thereby forcing all of the gas emanating from all of the gas bearings to exit from the rightmost exit of the cold zone, causing fluid forces to be exerted on the architectural glass sheet 400a and causing it to move to the cold zone 330, or (3) by a combination of (1) and (2))
• the transition gas bearings 320 may be supplied with gas by transition bearing plenums 328.
• the solid material thickness behind the surfaces of the transition gas bearings 320 may be thin, of low thermal mass and/or low thermal conductivity, allowing for reduced heat conduction from the hot zone 310 to the cold zone 330.
• the transition gas bearings 320 may serve as a thermal break or transition between the two zones 310 and 330 and may serve to transition from the larger gaps 316 of the hot zone down to small gaps 336 of the cold zone 330. Further, the low thermal mass and/or low thermal conductivity of transition gas bearings 320 limit(s) the amount of heat transfer and therefore cooling experienced by architectural glass sheet 400a while passing past transition gas bearings 320.
• stop gate 3421 a mechanical stop or any other suitable blocking mechanism, shown as stop gate 341.
• the stop gate 341 may be moved, unblocking cold zone channel 330a, and then the architectural glass sheet 400b may be removed from the system 300. If desired, the architectural glass sheet 400b may be left in the cold zone 330 until somewhere near room temperature before removal.
• the cold zone 330 includes a channel 330a for receiving heated architectural glass sheet 400b through an opening 330b, conveying the architectural glass sheet 400b, and cooling the architectural glass sheet 400b in the cold zone.
• the channel 330a includes a conveyance system that may include gas bearings, roller wheels, conveyor belt, or other means to physically transport the architectural glass sheet through the cold zone.
• cold zone 330 includes gas bearings 332 which are fed plenums 338 that are separate from hot zone plenums 318 and transition plenums 328.
• the cold zone 330 includes one or more heat sinks 331 disposed adjacent to the channel 330a. Where two heat sinks are utilized, such heat sinks may be disposed on opposite sides of the channel 330a, facing each other across a channel gap 330a.
• the heat sinks include a plurality of apertures 33 la which form part of the gas bearing 332, and the surfaces of the cold gas bearings 332 of the cold zone 330 serve as the two heat sink surfaces.
• architectural glass sheet 400b is cooled within cold zone 330 primarily by conduction of heat from the architectural glass sheet across the gap and into the solid heat sinks 331, without the architectural glass sheet 400b touching the heat sink surfaces.
• the heat sinks and/or the surfaces thereof may be segmented.
• the heat sinks may be porous, and in such embodiments, the apertures through which the gas for gas bearings 332 is delivered are the pores of the porous heat sinks.
• the plurality of apertures 332b, a gas source and the channel gap 330a may be in fluid communication.
• the gas flows through the apertures 33 la to form gas cushions, layers or bearings in the channel gap 330a.
• inventions prevent the architectural glass sheet 400b from contacting the heat sink 331 surfaces.
• the gas also serves as the gas through which the architectural glass sheet 400b is cooled by conduction more than by convection.
• the sheet may be (1) introduced quickly into the cold zone, optionally at higher speeds than those typically used in convection-based quenching and/or (2) the process is operated in a quasi-continuous mode, in which multiple sheets are heated and cooled one after the other in a continuous stream with little space between them, and where the heat sink is actively cooled such that it reaches a thermal equilibrium so that the front and trailing edges of the large sheets have similar thermal history.
• the gas flowed through the apertures 331a cools the heat sinks.
• the gas flowed through the apertures both facilitates heat conduction, from the architectural glass, across the gap, into the heat sinks, and also cools the heat sinks 331.
• a separate gas or fluid may be used to cool the heat sinks 331.
• the heat sinks 331 may include passages 334, for flowing a cooling fluid therethrough to cool the heat sinks 331, as is more fully described with respect to FIG. 23.
• the passages 334 can be enclosed.
• one or more gas sources may be used to provide a gas to the channel gap 330a.
• the gas sources may include the same gas as one another or different gases.
• the channel gap 330a may, therefore, include one gas, a mixture of gases from different gas sources, or the same gas source.
• Exemplary gases include air, nitrogen, carbon dioxide, helium or other noble gases, hydrogen and various combinations thereof.
• the gas may be described by its thermal conductivity when it enters the channel 330a just before it begins to conductively cool the architectural glass sheet 400b.
• the gas may have a thermal conductivity of about (e.g., plus or minus 1%) 0.02 W/(m K) or greater, about 0.025 W/(m K) or greater, about 0.03 W/(m K) or greater, about 0.035 W/(m K) or greater, about 0.04 W/(m K) or greater, about 0.045 W/(m K) or greater, about 0.05 W/(m K) or greater, about 0.06 W/(m K) or greater, about 0.07 W/(m K) or greater, about 0.08 W/(m K) or greater, about 0.09 W/(m K) or greater, about 0.1 W/(m K) or greater, about 0.15 W/(m K) or greater, or about 0.2 W/(m K
• the heat sinks 331 of one or more embodiments may be stationary or may be movable to modify the thickness of the channel gap 330a.
• the thickness of the architectural glass sheet 400b may be in a range from about 0.4 times the thickness to about 0.6 times the thickness of channel gap 300a, which is defined as the distance between the opposing surfaces of the heat sinks 331 (e.g., upper and lower surface of heat sinks 331 in the arrangement of FIG. 22).
• the channel gap is configured to have a thickness sufficient such that the heated architectural glass sheet is cooled by conduction more than by convection.
• the channel gap may have a thickness such that when architectural glass sheet 400b is being conveyed through or located within the channel 330a, the distance between the major surfaces of the architectural glass sheet 400b and the heat sink surface (e.g., the gap size discussed above) is about (e.g., plus or minus 1%) 100 ⁇ or greater (e.g., in the range from about 100 ⁇ to about 200 ⁇ , from about 100 ⁇ to about 190 ⁇ , from about 100 ⁇ to about 180 ⁇ , from about 100 ⁇ to about 170 ⁇ , from about 100 ⁇ to about 160 ⁇ , from about 100 ⁇ to about 150 ⁇ , from about 1 10 ⁇ to about 200 ⁇ , from about 120 ⁇ to about 200 ⁇ , from about 130 ⁇ to about 200 ⁇ , or from about 140 ⁇ to about 200 ⁇ ).
• the channel gap may have a thickness such that when architectural glass sheet 400b is being conveyed through the channel, the distance between the architectural glass sheet and the heat sink surface (the gap or gaps 336) is about (e.g., plus or minus 1%) 100 ⁇ or less (e.g., in the range from about 10 ⁇ to about 100 ⁇ , from about 20 ⁇ to about 100 ⁇ , from about 30 ⁇ to about 100 ⁇ , from about 40 ⁇ to about 100 ⁇ , from about 10 ⁇ to about 90 ⁇ , from about 10 ⁇ to about 80 ⁇ , from about 10 ⁇ to about 70 ⁇ , from about 10 ⁇ to about 60 ⁇ , or from about 10 ⁇ to about 50 ⁇ ).
• the gap or gaps 336 is about (e.g., plus or minus 1%) 100 ⁇ or less (e.g., in the range from about 10 ⁇ to about 100 ⁇ , from about 20 ⁇ to about 100 ⁇ , from about 30 ⁇ to about 100 ⁇ , from about 40 ⁇ to about 100 ⁇ , from about
• the total thickness of the channel gap 330a is dependent on the thickness of the architectural glass sheet 400b, but can be generally characterized as 2 times the distance between the heat sink surface and the architectural glass sheet, plus the thickness of the architectural glass sheet. In some embodiments, the distance or gaps 336 between the architectural glass sheet and the heat sinks may not be equal. In such embodiments, the total thickness of the channel gap 330a may be characterized as the sum of the distances between the architectural glass sheet and each heat sink surface, plus the thickness of the architectural glass sheet.
• the total thickness of the channel gap may be less than about (e.g., plus or minus 1%) 2500 ⁇ (e.g., in the range from about 120 ⁇ to about 2500 ⁇ , about 150 ⁇ to about 2500 ⁇ , about 200 ⁇ to about 2500 ⁇ , about 300 ⁇ to about 2500 ⁇ , about 400 ⁇ to about 2500 ⁇ , about 500 ⁇ to about 2500 ⁇ , about 600 ⁇ to about 2500 ⁇ , about 700 ⁇ to about 2500 ⁇ , about 800 ⁇ to about 2500 ⁇ , about 900 ⁇ to about 2500 ⁇ , about 1000 ⁇ to about 2500 ⁇ , about 120 ⁇ to about 2250 ⁇ , about 120 ⁇ to about 2000 ⁇ , about 120 ⁇ to about 1800 ⁇ , about 120 ⁇ to about 1600 ⁇ , about 120 ⁇ to about 1500 ⁇ , about 120 ⁇ to about 1400 ⁇ , about 120 ⁇ to about 1300 ⁇ , about 120 ⁇ to about 1200 ⁇ , or about 120
• the total thickness of the channel gap may be about 2500 ⁇ or more (e.g., in the range from about 2500 ⁇ to about 10,000 ⁇ , about 2500 ⁇ to about 9,000 ⁇ , about 2500 ⁇ to about 8,000 ⁇ , about 2500 ⁇ to about 7,000 ⁇ , about 2500 ⁇ to about 6,000 ⁇ , about 2500 ⁇ to about 5,000 ⁇ , about 2500 ⁇ to about 4,000 ⁇ , about 2750 ⁇ to about 10,000 ⁇ , about 3000 ⁇ to about 10,000 ⁇ , about 3500 ⁇ to about 10,000 ⁇ , about 4000 ⁇ to about 10,000 ⁇ , about 4500 ⁇ to about 10,000 ⁇ , or about 5000 ⁇ to about 10,000 ⁇ ).
• the apertures 33 la in the heat sink 331 may be positioned to be perpendicular to the heat sink surface or may be positioned at an angle of 20 degrees or less, such as about (e.g., plus or minus 1%) 15 degrees or less, about 10 degrees or less or about 5 degrees or less) from perpendicular to the heat sink surface.
• the material behind the heat sink (cold bearing 332) surfaces can be any suitable material having high heat transfer rates, including metals (e.g., stainless steel, copper, aluminum), ceramics, carbon, etc. This material may be relatively thick compared to the material behind the surfaces of the transition bearings 320, as shown in FIG. 22, such that heat sink can easily accept relatively large amounts of thermal energy.
• the material of the heat sinks 331 is stainless steel.
• FIG. 23 is a cut-away perspective cross-section of an apparatus similar to that of FIG. 22, albeit reversed from right to left, and comprising additionally a load/unload zone 340, next to cold zone 330 of system 300, including a load/unload gas bearing 342 with an architectural glass sheet 400c positioned thereon. Also, the apparatus of FIG. 23 uses tight channel gaps (not indicated on the figure) in hot zone 310, transition bearing 320, and cold zone 330.
• FIG. 23 shows an alternative embodiment of a cold zone gas bearing 332a, in which the gas bearing 322a is actively cooled by coolant channels 334, between gas bearing feed holes 333, where the feed holes feed the apertures in the surface of the bearing 322a.
• the cooling channels 334 are defined between heat sink segments 333b, which are assembled together to form the heat sink 331 and the surface thereof facing the architectural glass sheet 400b.
• the cooling channels 334 may be positioned very near the surface of the heat sink 331, in the solid material of the gas bearing 332, with a region of solid bearing material between the heat sink/gas bearing surface and the nearest-the-surface edge of the coolant channel 334, having the same width as the nearest-the-surface edge of the coolant channel 334. Accordingly, in some embodiments there is no region of reduced cross section in the solid material of the heat sink 331/gas bearing 332a between a coolant channel 334 and the surface facing the architectural glass 400b. This differs from the typical convective gas cooling equipment, because the high gas flow rates mandate that significant space be provided in the middle of the array of gas nozzles for the gas flows to escape.
• heat sink 331/gas bearing 332a has a region of reduced cross section in the solid material of the gas nozzle design, relative to the solid material nearest the architectural glass surface.
• the reduced cross section region is generally positioned between the active cooling fluid and architectural glass sheet under treatment, in order to give a high-volume path for the large volume of heated gas returning from the sheet.
• FIG. 24 shows yet another alternative embodiment of a cold zone gas bearing 332, like that of the inset of FIG. 23.
• coolant channels 334 are formed between a gas bearing feed member 335, containing gas bearing feed holes 333, and a gas bearing face member 337a, which provides the architectural glass sheet 400b facing surface of the gas bearing 332.
• FIG. 25 shows yet another alternative cold zone gas bearing 332c having a similar structure to the embodiment of FIG. 24, but having a porous member 339 between a bearing plate member 337b and architectural glass sheet 400b, such that porous member 339 forms the surface facing the architectural glass sheet 400b.
• the architectural glass strengthening processes and systems described herein in relation to FIGS. 16-26 may be used or operated to form an architectural glass or glass ceramic article (such as architectural glass sheet 500) having any combination of features, characteristics, dimensions, physical properties, etc. of any of the architectural glass article embodiments discussed herein.
• FIG. 1 Architectural glass sheets having undergone the thermal strengthening processes described herein may be further processed by undergoing ion exchange to further enhance their strength.
• Ion-exchanging the surface of architectural glasses heat strengthened as described herein may increase the above-described compressive stresses by at least 20 MPa, such as at least 50 MPa, such as at least 70 MPa, such as at least 80 MPa, such as at least 100 MPa, such as at least 150 MPa, such as at least 200 MPa, such as at least 300 MPa, such as at least 400 MPa, such as at least 500 MPa, such as at least 600 MPa and/or no more than 1 GPa, in some such contemplated embodiments.
• the processes and systems described herein can be used for additional thermal conditioning processes as well. While cooling is specifically discussed herein, the systems and processes can be used to transfer heat into the architectural glass sheet via a conductive method. Accordingly, additional embodiments of the processes of the current disclosure, including heating through a gas by conduction more than convection. Such a process or method 700 is illustrated in the flow chart of FIG. 26.
• the method 700 includes two main steps.
• the first step, step 710 involves providing an article, such as an architectural glass sheet, having at least one surface.
• the second step, step 720 involves heating or cooling a portion of the surface of the article, up to and including the entire surface of the article.
• Step 720 is performed by conduction more than by convection through a gas from or to a heat source or a heat sink source as shown in sub-part 720a, and is performed sufficiently to complete thermal conditioning of the article or the portion of the surface of the article in sub-part 720b, and the conduction of the cooling/heating of step 720 is performed at a high rate of heat transfer, at least 450 kW/m 2 of the area of the portion in sub-part 720b.
• an article can be thermally conditioned - i.e., either heated or cooled - by cooling or heating a portion of the surface of the article, up to and including the entire surface of the article(the portion having an area), by conduction more than by convection, the conduction mediated through a gas to or from a heat sink or a heat source and not through solid-to-solid contact, sufficiently to complete a thermal conditioning of the article or of the portion of the surface of the article, and the conduction being performed, during at least some time of the heating or cooling, at a rate of at least 450, 550, 650, 750, 800, 900, 1000, 1100, 1200, 1500, 2000, 3000, 4000 or even 5000 or more kW per square meter.
• the high rates of thermal power transfer allow for thermal processing or conditioning of all kinds, including heating and cooling during tempering, edge strengthening of architectural glass, firing or sintering of ceramics, glasses, or other materials, and so forth. Additionally, since the heat is extracted or delivered primarily by conduction, tight control is provided over the thermal history and the heat distribution in the treated article while preserving surface smoothness and quality. Accordingly, in yet another aspect of the present disclosure, tight control is provided over the thermal history and the heat distribution in the treated article, since the heat is extracted or delivered primarily by conduction, yet surface smoothness and quality are preserved.
• the strengthened architectural glass or glass-ceramic articles and sheets discussed herein have a wide range of uses in a wide range of articles, devices, products, structures, etc.
• the strengthened architectural glass or glass-ceramic articles and sheets discussed herein make up a part of or the whole pane in single-pane, multi-pane, and vacuum insulated glass (VIG) windows.
• VIP vacuum insulated glass
• a structure 1010 such as a building, house, office, vehicle, etc., includes an architectural glass or glass-ceramic article 1012 in the form of a window, portion of walls (e.g., surfaces), dividers, decorated panels, mirrors, etc.
• architectural glass or glass-ceramic article 1012 may be included in a cooler door, an oven door, similar appliances, or other indoor applications.
• the architectural glass or ceramic article 1012 may be strengthened such that the architectural glass or ceramic article 1012 has a negative tensile stress on or near surfaces thereof, balanced by a positive tensile stress internal thereto, as disclosed herein.
• the architectural glass or glass- ceramic article 1012 may have a composition that resists chemicals and/or corrosion as may be present in outdoor environments by having a relatively high silicon dioxide content, such as at least 70% silicon dioxide by weight, such as at least 75% by weight.
• the architectural glass or glass-ceramic article 1012 has major surfaces orthogonal to a thickness thereof (see generally sheet 500 as shown in FIG. 4), where the major surfaces have a large area (e.g., at least 5 cm 2 , at least 9 cm 2 , at least 15 cm 2 , at least 50 cm 2 , at least 250 cm 2 ) relative to architectural glass or glass-ceramic articles used in other applications (e.g., lenses, battery components, etc.).
• a large area e.g., at least 5 cm 2 , at least 9 cm 2 , at least 15 cm 2 , at least 50 cm 2 , at least 250 cm 2
• total light transmission through the architectural glass or glass-ceramic articles 1012 is at least about 50% (e.g., at least 65%, at least 75%) from wavelengths of about 300 nm to about 800 nm, when the architectural glass or glass ceramic article 1012 has thicknesses t as disclosed herein, such as a thickness of less than 5 cm, less than 3 cm, less than 2 cm, less than 1.75 cm, less than 1.5 cm, less than 1 cm, less than 5 mm, less than 3 mm, less than 2 mm, less than 1.75 mm, less than 1.5 mm, less than 1 mm, less than 0.8 mm, less than 0.6 mm, less than 0.5 mm, less than 0.4 mm, less than 0.2 mm, and/or at least 10 micrometers, such as at least 50 micrometers.
• window 1400 is shown from the outside of a structure (e.g., building, home, office, automobile, train, etc.).
• a structure e.g., building, home, office, automobile, train, etc.
• window 1400 may be installed in a structure 1010 as shown in FIG. 27.
• Window 1400 may be a single-pane, double-pane, triple-pane window, or even quadruple pane window.
• At least one of the panes in window 1400 may be an architectural glass or glass- ceramic article manufactured as disclosed herein and/or with any combination of stress profiles, structures, surface roughness, and/or other physical properties discussed herein.
• all of the panes in window 1400 include the architectural glass or glass-ceramic sheet (e.g., FIG. 4) manufactured as disclosed herein.
• one or more of the panes in window 1400 may include an architectural glass-based layer (i.e., a thermally strengthened glass or glass-ceramic article) manufactured as disclosed herein and/or with any combination of stress profiles, structures, surface roughness, and/or other physical properties discussed herein.
• window 1400 includes a first glass-based layer 4102 and a second glass-based layer 4202 with a space or sealed interior region 4401 there between.
• first glass-based layer 4102 and second glass-based layer 4202 face each other and are spaced apart from and disposed substantially parallel to each other.
• first glass-based layer 4102 includes a body 4101 with an outside surface 4104 opposite an inside surface 4106, and an outer edge 4108. Outside and inside surface 4104, 4106 may be referred to as major surfaces herein.
• first glass-based layer 4102 includes an interior region defining thickness t between major surfaces 4104, 4106.
• second glass-based layer 4202 includes a body 4201 with an outside surface 4206 opposite an inside surface 4204, and an outer edge 4208. Outside and inside surface 4206, 4204 may be referred to as major surfaces herein.
• second glass-based layer 4202 includes an interior region defining thickness t between major surfaces 4204, 4206. Glass-based layers 4102, 4202 may both act as the inside or outside pane of a structure.
• first and second glass-based layers 4102, 4202 is a thermally strengthened architectural glass or glass-ceramic sheet manufactured according to systems and methods disclosed herein and/or with any combination of stress profiles, structures, glass composition, surface roughness, etc. and/or physical properties as disclosed herein.
• second glass-based layer 4202 is a thermally strengthened architectural glass or glass-ceramic sheet according to the present disclosure (e.g., FIG. 4) while first glass-based layer 4102 is a thermally strengthened glass layer, a chemically strengthened glass layer, a mechanically strengthened glass layer, a thermally and chemically strengthened glass layer, a thermally and mechanically strengthened glass layer or a chemically and mechanically strengthened glass layer.
• First and second glass-based layers 4102, 4202 may the same or different glass material compositions as disclosed herein.
• the compressive stress (CS) region is generated by a mismatch of the coefficient of thermal expansion between portions of the glass layer.
• the CS region is formed by heating the glass layer to an elevated temperature above the glass transition temperature, near the glass softening point, and then cooling the glass surface regions more rapidly than the inner regions of the glass layer. The differential cooling rates between the surface regions and the inner regions generates a residual surface CS.
• Chemically- strengthened glass substrates may include a compressive stress (CS) region and a central tension (CT) region generated by an ion exchange process.
• CS and DOL are determined by surface stress meter (FSM) using commercially available instruments such as the FSM-6000, manufactured by Luceo Co., Ltd. (Tokyo, Japan), or the like, and methods of measuring CS and depth of layer are described in ASTM 1422C-99, entitled "Standard
• a glass layer that is chemically strengthened may have a surface CS of 250 MPa or greater, 300 MPa or greater, e.g., 400 MPa or greater, 450 MPa or greater, 500 MPa or greater, 550 MPa or greater, 600 MPa or greater, 650 MPa or greater, 700 MPa or greater, 750 MPa or greater or 800 MPa or greater.
• a glass layer that is chemically strengthened may have a DOL of ⁇ or greater, 15 ⁇ or greater, 20 ⁇ or greater (e.g., 25 ⁇ , 30 ⁇ , 35 ⁇ , 40 ⁇ , 45 ⁇ , 50 ⁇ or greater) and/or a CT of 10 MPa or greater, 20 MPa or greater, 30 MPa or greater, 40 MPa or greater (e.g., 42 MPa, 45 MPa, or 50 MPa or greater) but less than 100 MPa (e.g., 95, 90, 85, 80, 75, 70, 65, 60, 55 MPa or less).
• a glass layer that is chemically strengthened has one or more of the following: a surface CS greater than 500 MPa, a DOL greater than 10 ⁇ , and a CT greater than 18 MPa.
• Window 1400 may further include a member 4421 between its panes.
• Member 4421 may be an edge seal (e.g., glass frit, laser edge seal, solder, rubber) formed around respective edges of glass panes 4102, 4202 (forming a hermetic or non-hermetic seal), a metallic pillar between the surfaces of glass panes 4102, 4202, a low thermal conduction material, or a glass- bump spacer 50 attached to or formed integral with one or both glass panes.
• Member 4421 may assist in creating a space between one or both distances 4001, 4002 between its glass panes.
• Window 1400 may further include a frame 4420 around the edges of its glass panes.
• Space 4401 includes a distance 4001 between glass-based layers 4102 and 4202.
• Distance 4001 may be from about 50 microns to about 50 mm, or from about 0.1 mm to about 25 mm, or from about 0.1 mm to about 23 mm, or from about 0.2 mm to about 22 mm, or from about 0.3 mm to about 21 mm, or from about 0.4 mm to about 20 mm, or from about 0.5 mm to about 19 mm, or from about 0.6 mm to about 18 mm, or from about 0.7 mm or about 17 mm, or from about 2 mm to about 15 mm.
• Space 4401 may be sealed and include an insulating gas such as air or a noble gas (e.g., argon, krypton, xenon). Alternatively, space 4401 may be sealed and include a vacuum pressure less than atmospheric pressure (e.g., 10 "4 torr).
• first and second glass-based layers 4102, 4202 may include a low emissivity layer 4110 on any of its major surfaces.
• Low emissivity layer 4110 may be a film, a coating, or a layer on a major surface or within the body of glass-based layers 4102 and 4202. As shown in FIG. 32, low emissivity layer 4110 is on inside surface 4106 of first glass-based layer 4102 adjacent the outside of a structure.
• first and second glass-based layers 4102, 4202 may include an indium tin oxide layer or film for use in active smart windows such as electrochromic windows.
• first and second glass-based layers 4102, 4202 may also include reflective coatings, transparent coating, a polymer coating, an electrically conductive coating, a frosting film, or combinations thereof.
• FIG. 33 illustrates an example embodiment of window 1400 where one of the panes is a laminate including glass-based layer 4202 laminated to a glass pane 4300 with an interlay er 4250 there between.
• interlayer 4250 is at least partially coextensive with the glass-based layer 4202 and coupled directly and/or indirectly to a side of glass pane 4300.
• interlayer 4250 may include a polymer material.
• the polymer material may include poly vinyl butyral (PVB), polycarbonate, acoustic PVB, ethylene vinyl acetate (EVA), thermoplastic polyurethane (TPU), ionomer, a thermoplastic material, and combinations thereof.
• Glass-based layer 4102 may alternatively or additionally be configured as a laminate.
• window 1400 includes a third glass-based layer 4302.
• third glass-based layer 4302 includes a body 4301 with an outside surface 4304 opposite an inside surface 4306, and an outer edge 4308. Outside and inside surface 4304, 4306 may be referred to as major surfaces herein.
• third glass-based layer 4302 includes an interior region defining the thickness t between major surfaces 4304, 4306.
• third glass-based layer 4302 is facing, spaced apart from, and disposed substantially parallel to first and/or second glass-based layers 4102, 4202 with a second space or sealed interior region 4402 there between.
• third glass-based layer 4302 is spaced apart from second glass-based layer 4202 by a second spaced apart distance 4002. Accordingly, glass-based layer 4302 may both act as the inside or outside pane of a structure.
• Third glass-based layer 4302 may also be the middle pane between first and/or second glass-based layers 4102, 4202 of triple-pane window 1400.
• Third glass-based layer may be a thermally strengthened architectural glass or glass- ceramic sheet manufactured according to systems and methods disclosed herein and/or with any combination of stress profiles, glass compositions, structures, surface roughness attributes, and/or physical properties as disclosed herein.
• third glass-based layer 4302 is a thermally strengthened glass layer, a chemically strengthened glass layer, a mechanically strengthened glass layer, a thermally and chemically strengthened glass layer, a thermally and mechanically strengthened glass layer or a chemically and mechanically strengthened glass layer.
• Third glass-based layer 4302 may be any glass composition as disclosed herein or similar glass materials.
• First, second, and third glass-based layers 4102, 4202, 4302 may be all the same or all different glass material compositions as disclosed herein.
• Third glass-based layers 4302 may include a low emissivity layer 4110 on any of its major surfaces.
• Low emissivity layer 4110 may be a film, a coating, or a layer on a major surface or within the body of glass-based layer 4302.
• third glass-based layer 4302 is laminated to a glass pane 4300 with an interlayer 4250 there between.
• interlayer 4250 is at least partially coextensive with the glass-based layer 4302 and coupled directly and/or indirectly to a side of glass pane 4300.
• Third glass-based layer 4302 may include an indium tin oxide layer or film for use in active smart windows such as electrochromic windows.
• Third glass-based layer 4302 may also include reflective coatings, transparent coating, a polymer coating, an electrically conductive coating, a frosting film, or combinations thereof.
• First, second, third glass-based layers 4102, 4202, 4302 may also be configured as a double or triple-pane vacuum insulated glass (VIG) window.
• FIG. 35 is a front-on view of an example embodiment of a VIG window 1500.
• the configuration of VIG window 1500 may be similar to that of double or triple-pane window 1400.
• VIG window 1500 may contain two panes or three panes.
• FIG. 36 is a cross-sectional view of the example two-pane VIG window 1500 of
• VIG window 1500 includes first glass-based layer 4102 (i.e., a thermally strengthened glass or glass-ceramic article) spaced apart from and positioned substantially parallel to second glass-based layer 4202.
• the first and second glass panes 4102, 4202 each include an inner surface 4106, 4204 opposite an outer surface 4104,
• VIG window 1500 may include third glass-based layer 4302 including an inner surface 4304 opposite an outer surface 4306, and at least one outer edge 4308.
• Third glass-based layer 4302 may be positioned between and substantially parallel the first and second glass pane 4102, 4202, or opposite a major surface of either the first or second glass pane 4102, 4202.
• First, second, and third glass-based layers 4102, 4202, 4302 may include any glass or glass-ceramic composition disclosed herein.
• One, two, or all of the glass-based layers 4102, 4202, 4302 may include thermally strengthened architectural glass or glass-ceramic sheet manufactured according to systems and methods disclosed herein and/or with any combination of stress profiles, glass compositions, structures, surface roughness attributes, and/or physical properties as disclosed herein.
• at least one of glass-based layers 4102, 4202, 4302 is configured as a laminate and laminated to a glass pane 4300 with an interlayer 4250 there between (similar to that shown in FIG. 33).
• interlayer 4250 is at least partially coextensive with the applicable glass-based layer (4102, 4202, 4302) and coupled directly and/or indirectly to a side of glass pane 4300.
• interlayer 4250 may include a polymer material.
• One, two, or all of the glass- based layers 4102, 4202, 4302 in window 1500 may be configured as a laminate.
• One, two, or all of the glass-based layers 4102, 4202, 4302 in window 1500 may include a low emissivity layer 4110 within its body or on one or both major surfaces in window 1500.
• One, two, or all of the glass-based layers 4102, 4202, 4302 in window 1500 may include an indium tin oxide layer or film for use in active smart windows such as electrochromic windows.
• One, two, or all of the glass-based layers 4102, 4202, 4302 (including a fourth glass-based layer) in window 1500 may include may also include reflective coatings, transparent coating, a polymer coating, an electrically conductive coating, a frosting film, or combinations thereof.
• Frosting films of the present disclosure may be partially transparent or opaque. Further, frosting films may be decorative and/or functional.
• VIG window 1500 further includes spacers 50.
• spacers 50 are a plurality of glass-bump spacers 50 integrally formed in inner surface 4204 of second glass-based layer 4202. Glass-bump spacers 50 may also be formed on inner surface 4106 of glass-based layer 4102.
• FIG. 3 is a close-up view of an example glass-bump spacer 50. Glass-bump spacers
• glass-bumps 50 may be integrally formed in first or second glass-based layer 4102, 4202 or added as separate or discrete elements to VIG window 1500.
• glass-bumps 50 are formed from (and thus consist of) the same material as the glass-based layer.
• Example methods of forming glass-bumps 50 are discussed in U.S. Patent No. 8,679,599 and 8,821,999, the entire contents of which is incorporate by reference herein.
• Example methods of etching glass-bumps 50 from glass pane 20B, for example, are provided in U.S. Patent Application No. 62/248,715 entitled "VACUUM INSULATED GLASS UNITS AND METHODOLOGY FOR
• Glass-bumps spacers 50 may be provided or grown from glass-based layers 4102, 4202, 4302 before or after the thermally strengthening techniques are applied to the architectural glass or glass-ceramic sheet as disclosed herein. Spacers 50 may also be discrete metal, ceramic, aluminum, plastic, or glass spacers between panes 20B and 20F.
• glass-bump spacers 50 are regularly spaced with respect to one another. Because glass-bump spacers 50 are integrally formed in body 4101, 4201, 4301, they are substantially invisible when the VIG window 1500 is viewed at regular (i.e.,
• glass-bumps 50 are shown in phantom (dotted lines) in FIG. 35.
• Glass-bump 50 has a "tip" or "top portion” 51, as shown in FIG. 3.
• top portion 51 need not be rounded as is shown in FIG. 37.
• top portion 51 may have a large radius of curvature or even a flat top portion.
• Glass- bump geometries according to the present disclosure are provided in U.S. Patent Application No. 14/808,790 entitled "GLASS BUMPS ON GLASS ARTICLES AND METHODS OF LASER- INDUCED GROWTH" (Attorney Docket No. SP15-169PZ) the entire content of which is incorporated by reference herein.
• glass-based layers 4102, 4202, 4302 are transmissive at 420 nm to 750 nm.
• glass-bump spacers 50 have a height ("bump height") H in the range from 50 ⁇ to 300 ⁇ , or from 75 ⁇ to 150 ⁇ , and or even from 100 ⁇ to 120 ⁇ .
• the height H of glass-bump spacers 50 may define spaced distances 4001, 4002.
• glass-bump spacers 50 contact front glass-based layer 4101 (at surface 4106) to maintain the first distance 4001 between front and back glass panes 4102, 4202.
• the glass-based layer contacted by the glass-bump spacers 50 in window 1500 is thermally strengthened architectural glass or glass-ceramic sheet manufactured according to systems and methods disclosed herein. The compressive stress of the major surface thereon may help minimize damage caused by the point stress at top portion 51 of each glass- bump spacer 50 caused by vacuum force in space 4401 and thermal contraction and expansion of the opposing panes.
• Member 4421 may be provided at respective outer edges 4108 and 4208 between at least a portion of each outer edge to provide a hermetic seal.
• Edge seal between front and back glass-based layers 4102, 4202 defines a sealed interior region 4401.
• the edge seal is at least partially laser-induced.
• Edge seal may be a seal by glass frit, a seal directly between glass-based layers 4102, 4202, or a seal with a shim or glass segment there between glass-based layers 4102, 4202.
• Space 4401 may be at least partially evacuated so that it has a vacuum pressure of less than one atmosphere or less than atmospheric pressure (e.g., 10 "4 torr, or even less than 10 "6 torr), which provides VIG window 1500 with desirable thermal and acoustic insulation properties.
• member 4421 around the respective outer edges 4108, 4208 of front and back glass-based layers 4102, 4202 creates a hermetically sealed space 4401 between surfaces 4106 and 4204 of front and back glass-based layers 4102 and 4202.
• FIG. 38 is a cross-sectional view similar to FIG. 36 and illustrates an example embodiment of a three-pane VIG window 1500.
• First and second sets of glass-bump spacers 50 are respectively formed in both the front and back surfaces 4204 and 4206 of second glass-based layer 4202 to maintain distance 4001 from first glass-based layer 4102, and distance 4002 from third glass-based layer 4302.
• multiple edge seals may be used, where one edge seal serves to seal at least respective portions of edges 4108 and 4208, and the other edge seal serves to seal at least respective portions of edges 4208 and 4308.
• a single edge seal 4421 serves to seal edges 4108, 4208, and 4308 to define both sealed interior regions 4401 and 4402.
• the glass-bumps spacers may be formed on any surface of any of the two of three glass-based layers 4102, 4202, 4302 in VIG window 1500.
• Glass-based layers 4102, 4202, 4302 may be referred to as front, middle, and back glass-based layers herein.
• FIG. 39 is similar to FIG. 38, and illustrates an alternate example embodiment of a three-pane VIG window 1500 FIG. 35 as viewed in the direction 1-1.
• the second set of glass-bump spacers 50 are on third glass-based layer 4302 rather than in the middle glass-based layer 4202.
• FIG. 39 also illustrates an example embodiment where multiple members 4421 (e.g., edge seals) are used, as described above.
• FIG. 40 is similar to FIG.
• the glass-bump spacers 50 are formed in the inner and outer glass-based-layers, while in the embodiment illustrated in FIG. 38, the glass- bump spacers are formed in the middle glass-based layer.
• One, two, or all of glass-based layers 4102, 4202, 4302 (including a fourth glass-based layer) in VIG window 1500 may be a thermally strengthened architectural glass or glass-ceramic sheet manufactured according to systems and methods disclosed herein and/or with any combination of stress profiles, glass compositions, structures, surface roughness attributes, and/or physical properties as disclosed herein.
• one, two, or all of glass- based layers 4102, 4202, 4302 may be a thermally strengthened glass layer, a chemically strengthened glass layer, a mechanically strengthened glass layer, a thermally and chemically strengthened glass layer, a thermally and mechanically strengthened glass layer or a chemically and mechanically strengthened glass layer.
• Thin thicknesses of the architectural glass or glass-ceramic article 1012 may not harm the function of the architectural glass or glass-ceramic article 1012 in architectural, window, automotive, or other applications relative to conventional articles because the high level of strength of the architectural glass or glass-ceramic article 1012 provided by the inventive processes disclosed herein.
• Thin architectural glass or glass-ceramic articles 1012 may be particularly useful as layers or panes in architectural windows, or other applications because the architectural glass or glass ceramic article 1012 may be lighter than conventional such articles, reducing the weight of the corresponding overall structure. For automobiles, a result may be greater fuel efficiency. For buildings, a result may be lighter, sturdier or less resource-intensive structures.
• architectural glass or glass-ceramic articles disclosed herein may have areas of lesser magnitude, greater thicknesses, transmit less light, and/or may be used in different applications, such as those disclosed with regard to FIGS. 27-30, for example.
• a surface 1 1 10 includes a glass or glass ceramic article 1 1 12, manufactured as disclosed herein and/or with any combination of stress profiles, structures and/or physical properties discussed herein, that functions as a countertop and/or as a portion of a display.
• total transmission through the glass or glass ceramic articles 1012 is at least about 30% (e.g., at least 50%) from infrared wavelengths of about 800 nm to about 1500 nm, facilitating use of the surface 11 10 as a cooktop.
• the glass or glass-ceramic article 11 12 has a coefficient of thermal expansion (CTE) from about lO lO "7 0 C _1 to about 14 about 20 10 "7 °C A to about 12 about 30x 10 " 7 0 C _1 to about lOOx lO "7 40 ⁇ 10 "7 °C A to about ⁇ ⁇ ⁇ "7 50 ⁇ 10 "7 °C A to about lOOx lO "7 °C _1 , or about 60 ⁇ 10 "7 °C _1 to about 120 ⁇ 10 "7 0 C " ⁇
• the processes are ideally suited for glass compositions having moderate to high CTEs.
• Example glasses that work well with the processes described herein include alkali aluminosilicates, such as Coming' s® Gorilla® Glasses, boroaluminosilicates, and soda-lime glasses.
• the glasses used have CTEs greater than 40, greater than 50, greater than 60, greater than 70, greater than 80, or greater than 90 ⁇ 10 "7 /°C.
• Some such CTEs may be particularly low for thermal tempering as disclosed herein, where the degree of negative tensile stress is no more than 50 MPa and/or at least 10 MPa.
• a device 1210 e.g., handheld computer, tablet, portable computer, cellular phone, television, display board, etc.
• a device 1210 includes one or more glass or glass-ceramic articles 1212, 1214, 1216, manufactured as disclosed herein and/or with any combination of stress profiles, structures and/or physical properties as disclosed herein, and further includes electronic components 1218 and a housing 1220.
• the housing 1220 may be or include a glass or glass-ceramic article as disclosed herein.
• a substrate 1222 for the electronic components 1218 may be a glass or glass-ceramic article as disclosed herein.
• the glass or glass ceramic articles 1212, 1214 may function as frontplane and backplane substrates, and the glass or glass ceramic article 1216 may function as a cover glass in the device 1210.
• the glass or glass-ceramic article 1216 of the device 1210 is an alkali-aluminosilicate glass.
• composition may allow the glass or glass-ceramic article 1216 to be strengthened by thermal tempering, as disclosed herein, and may be additionally strengthened by ion-exchange, providing a particularly high degree of negative tensile stress (e.g., at least 200 MPa, at least 250 MPa) at or near surfaces thereof.
• the glass or glass-ceramic article 1216 may include sodium carbonate, calcium oxide, calcium magnesium carbonate, silicon dioxide (e.g., at least 70% by weight), aluminum oxide, and/or other constituents; and may be strengthened by the inventive processes disclosed herein.
• the glass or glass ceramic article 1216 may be particularly thin or otherwise structured, such as having any of the dimensions as disclosed herein.
• an architectural glass or glass-ceramic article 1310 manufactured according to processes disclosed herein and/or with any combination of stress profiles, structures and/or physical properties as disclosed herein, has curvature and/or a variable cross-sectional dimension D.
• Such articles may have thicknesses disclosed herein as an average of dimension D or as a maximum value of dimension D.
• the architectural glass or glass- ceramic article 1310 is shown as a curved sheet, other shapes, such as more complex shapes, may be strengthened by processes disclosed herein.
• the architectural glass or glass ceramic article 1310 may be used as a window for an automobile (e.g., sunroof) or for a building, as a skylight, or for other applications.
• glass material manufactured according to processes disclosed herein, and/or with any combination of stress profiles, structures and/or physical properties as disclosed herein is useful to form at least one sheet of an architectural glass-interlayer- architectural glass laminate. Stronger and thinner laminates can be produced, resulting in weight and cost savings. Desirably, a thermally strengthened thin sheet may be cold bent (see generally FIG. 30) and laminated to a formed thicker glass, providing an easy and reliable manufacturing process not requiring any hot forming/shaping of the thin sheet. Glass and Glass Ceramic Materials for Thermally Strengthened Architectural Glass Sheets
• the processes and systems described herein may generally be used with almost any architectural glass composition, and some embodiments can be used with architectural glass laminates, architectural glass ceramics, and/or ceramics. In various embodiments, the processes can be used with architectural glass compositions having high CTEs.
• architectural glasses strengthened via the processes and systems discussed herein include alkali aluminosilicates, such as Coming's® Gorilla® Glasses, SLG, soda- or alkali-free glasses and the like.
• architectural glasses strengthened via the processes and systems discussed herein have CTEs of greater than 40xl0 "7 /°C, greater than 50xl0 "7 /°C, greater than 60x10 "7 /°C, greater than 70x10 "7 /°C, greater than 80x10 "7 /°C, or greater than 90x10 "7 /°C.
• architectural glasses strengthened via the processes and systems discussed herein may have a composition configured for chemical durability.
• the composition comprises at least 70% silicon dioxide by weight, and/or at least 10% sodium oxide by weight, and/or at least 7% calcium oxide by weight.
• Conventional articles of such compositions may be difficult to chemically temper to a deep depth, and/or may be difficult, if not impossible, to thermally temper by conventional processes to a sufficient magnitude of negative surface tensile stress for thin thicknesses, such as due to fragility and forces of conventional processes.
• inventive processes disclosed herein allow a strengthened architectural glass or glass-ceramic article or sheet, such as architectural glass sheet 500, with such a composition, where negative tensile stress extends into the respective strengthened architectural glass or glass-ceramic sheet to a distance of at least 10% of the thickness of the strengthened architectural glass or glass-ceramic sheet from at least one of the first and second surfaces (e.g., surfaces 510, 520 of architectural glass sheet 500), such as at least 12%) of the thickness, 15%> of the thickness, 18%> of the thickness, 20%> of the thickness.
• first and second surfaces e.g., surfaces 510, 520 of architectural glass sheet 500
• the architectural glass or glass-ceramic sheets and articles strengthened as discussed herein have one or more coatings that are placed on the architectural glass prior to the thermal strengthening of the architectural glass sheet.
• the processes discussed herein can be used to produce strengthened architectural glass sheets having one or more coatings, and, in some such embodiments, the coating is placed on the architectural glass prior to thermal strengthening and is unaffected by the thermal strengthening process.
• Specific coatings that are advantageously preserved on architectural glass sheets of the present disclosure include low E coatings, reflective coatings, antireflective coatings, anti-fingerprint coatings, cut-off filters, pyrolytic coatings, etc.
• glass or glass-ceramic sheets or articles discussed herein are boro- aluminosilicate glasses.
• glass or glass-ceramic sheets or articles discussed herein, for example articles 1212, 1214 of the device 1210 shown in FIG. 29, are generally non-alkali glasses, yet still have stress profiles and structures as disclosed herein. Such composition may reduce the degree of relaxation of the architectural glass, facilitating coupling of electronics thereto (for electrochromic windows for example).
• the architectural glass sheets/articles discussed herein are flexible architectural glass sheets.
• the architectural glass sheets/articles discussed herein comprise a laminate of two or more architectural glass sheets.
• architectural glasses strengthened via the processes and systems discussed herein may include an amorphous substrate, a crystalline substrate or a combination thereof, such as an architectural glass-ceramic substrate.
• Architectural glasses strengthened via the processes and systems discussed herein may include an alkali alumino silicate glass, alkali containing borosilicate glass, alkali aluminophosphosilicate glass or alkali aluminoborosilicate glass, photochromic glass, electrochromic glass, or thermochromic glass.
• architectural glasses strengthened via the processes and systems discussed herein may include an architectural glass having a composition, in mole percent (mol%), including: Si0 2 in the range from about (e.g., plus or minus 1%) 40 to about 80 mol%, A1 2 0 3 in the range from about 10 to about 30 mol%, B 2 0 3 in the range from about 0 to about 10 mol%, R 2 0 in the range from about 0 to about 20 mol%, and/or RO in the range from about 0 to about 15 mol%.
• Si0 2 in the range from about (e.g., plus or minus 1%) 40 to about 80 mol%
• A1 2 0 3 in the range from about 10 to about 30 mol%
• B 2 0 3 in the range from about 0 to about 10 mol%
• R 2 0 in the range from about 0 to about 20 mol%
• RO in the range from about 0 to about 15 mol%.
• the composition may include either one or both of Zr0 2 in the range from about 0 to about 5 mol% and P 2 0 5 in the range from about 0 to about 15 mol%.
• Ti0 2 can be present from about 0 to about 2 mol%.
• compositions used for the strengthened architectural glass or glass-ceramic sheet or article discussed herein may be batched with 0-2 mol% of at least one fining agent selected from a group that includes Na 2 S0 4 , NaCl, NaF, NaBr, K 2 S0 4 , KC1, KF, KBr, and Sn0 2 .
• the architectural glass composition according to one or more embodiments may further include Sn0 2 in the range from about 0 to about 2 mol%, from about 0 to about 1 mol%, from about 0.1 to about 2 mol%, from about 0.1 to about 1 mol%, or from about 1 to about 2 mol%.
• Architectural glass compositions disclosed herein for the strengthened architectural glass or glass-ceramic sheet 500 may be substantially free of As 2 0 3 and/or Sb 2 0 3 , in some embodiments.
• the strengthened architectural glass or glass-ceramic sheet or article discussed herein may include alkali aluminosilicate architectural glass compositions or alkali aluminoborosilicate architectural glass compositions that are further strengthened via an ion exchange process.
• One example architectural glass composition comprises Si0 2 , B 2 0 3 and Na 2 0, where (Si0 2 + B 2 0 3 ) > 66 mol. %, and/or Na 2 0 > 9 mol. %.
• the architectural glass composition includes at least 6 wt.% aluminum oxide.
• the strengthened architectural glass or glass-ceramic sheet or article discussed herein may include an architectural glass composition with one or more alkaline earth oxides, such that a content of alkaline earth oxides is at least 5 wt.%.
• Suitable architectural glass compositions in some embodiments, further comprise at least one of K 2 0, MgO and CaO.
• the architectural glass compositions used in the strengthened architectural glass or glass-ceramic sheet or article discussed herein may include an architectural glass composition with one or more alkaline earth oxides, such that a content of alkaline earth oxides is at least 5 wt.%.
• Suitable architectural glass compositions in some embodiments, further comprise at least one of K 2 0, MgO and CaO.
• architectural glass or glass-ceramic sheet or article discussed herein can comprise 61-75 mol.% Si02; 7-15 mol.% A1 2 0 3 ; 0-12 mol.% B 2 0 3 ; 9-21 mol.% Na 2 0; 0-4 mol.% K 2 0; 0-7 mol.% MgO; and/or 0-3 mol.% CaO.
• a further example glass composition suitable for the strengthened architectural glass or glass-ceramic sheet or article discussed herein comprises: 60-70 mol.% Si0 2 ; 6- 14 mol.% A1 2 0 3 ; 0-15 mol.% B 2 0 3 ; 0-15 mol.% Li 2 0; 0-20 mol.% Na 2 0; 0- 10 mol.% K 2 0; 0-8 mol.% MgO; 0-10 mol.% CaO; 0-5 mol.% Zr0 2 ; 0- 1 mol.% Sn0 2 ; 0- 1 mol.% Ce0 2 ; less than 50 ppm As 2 0 3 ; and less than 50 ppm Sb 2 0 3 ; where 12 mol.% ⁇ (Li 2 0 + Na 2 0 + K 2 0) ⁇ 20 mol.% and/or 0 mol.%) ⁇ (MgO + CaO) ⁇ 10 mol.%.
• a still further example glass composition suitable for the strengthened architectural glass or glass-ceramic sheet or article discussed herein comprises: 63.5-66.5 mol.% Si0 2 ; 8- 12 mol.% A1 2 0 3 ; 0-3 mol.% B 2 0 3 ; 0-5 mol.% Li 2 0; 8- 18 mol.% Na 2 0; 0-5 mol.% K 2 0; 1-7 mol.% MgO; 0-2.5 mol.% CaO; 0-3 mol.% Zr0 2 ; 0.05-0.25 mol.% Sn0 2 ;
• an alkali aluminosilicate glass composition suitable for the strengthened architectural glass or glass-ceramic sheet or article discussed herein comprises alumina, at least one alkali metal and, in some embodiments, greater than 50 mol.% Si0 2 , in other embodiments at least 58 mol.% Si0 2 , and in still other embodiments at least 60 mol.%) Si0 2 , wherein the ratio (A1 2 0 3 + B 2 0 3 )/ ⁇ modifiers (i.e., sum of modifiers) is greater than
• This architectural glass composition in particular embodiments, comprises: 58-72 mol.% Si0 2 ; 9- 17 mol.% A1 2 0 3 ; 2- 12 mol.% B 2 0 3 ; 8- 16 mol.% Na 2 0; and/or 0-4 mol.% K 2 0, wherein the ratio (A1 2 0 3 + B 2 0 3 )/ ⁇ modifiers (i.e., sum of modifiers) is greater than 1.
• the strengthened architectural glass or glass-ceramic sheet 500 may include an alkali aluminosilicate glass composition comprising: 64-68 mol.% Si0 2 ; 12-16 mol.% Na 2 0; 8- 12 mol.% A1 2 0 3 ; 0-3 mol.% B 2 0 3 ; 2-5 mol.% K 2 0; 4-6 mol.% MgO; and 0-5 mol.% CaO, wherein: 66 mol.% ⁇ Si0 2 + B 2 0 3 + CaO ⁇ 69 mol.%; Na 2 0 + K 2 0 + B 2 0 3 + MgO + CaO + SrO > 10 mol.%; 5 mol.% ⁇ MgO + CaO + SrO ⁇ 8 mol.%; (Na 2 0 + B 2 0 3 ) - A1 2 0 3 ⁇ 2 mol.%; 2 mol.% ⁇ Na 2 0 - A1 2 0 ⁇
• the strengthened architectural glass or glass-ceramic sheet or articles discussed herein may comprise an alkali aluminosilicate glass composition comprising: 2 mol.% or more of A1 2 0 3 and/or Zr0 2 , or 4 mol.% or more of A1 2 0 3 and/or Zr0 2 .
• suitable glass ceramics for the strengthened architectural glass or glass-ceramic sheet or articles discussed herein may include Li 2 0-Al 2 0 3 -Si0 2 system (i.e. LAS-System) glass ceramics, MgO-Al 2 0 3 -Si0 2 system (i.e.
• the strengthened architectural glass or glass-ceramic sheet or article discussed herein may be characterized by the manner in which it is formed.
• the strengthened architectural glass or glass-ceramic sheet or article discussed herein may be characterized as float-formable (i.e., formed by a float process), down-drawable and, in particular, fusion-formable or slot-drawable (i.e., formed by a down draw process such as a fusion draw process or a slot draw process).
• a float-formable strengthened architectural glass or glass-ceramic sheet or article may be characterized by smooth surfaces and consistent thickness, and is made by floating molten architectural glass on a bed of molten metal, typically tin.
• molten architectural glass or glass-ceramic that is fed onto the surface of the molten tin bed forms a floating architectural glass or glass-ceramic ribbon.
• the temperature is gradually decreased until the architectural glass or glass-ceramic ribbon solidifies into a solid architectural glass or glass-ceramic article that can be lifted from the tin onto rollers.
• the architectural glass or glass-ceramic article can be cooled further and annealed to reduce internal stress.
• the architectural glass or glass-ceramic article formed from the float process may be subjected to a ceramming process by which one or more crystalline phases are generated.
• Down-draw processes produce architectural glass or glass-ceramic articles having a consistent thickness that possess relatively pristine surfaces. Because the average flexural strength of the architectural glass or glass-ceramic article is controlled by the amount and size of surface flaws, a pristine surface that has had minimal contact has a higher initial strength. When this high strength architectural glass or glass-ceramic article is then further strengthened (e.g., chemically), the resultant strength can be higher than that of an architectural glass or glass- ceramic article with a surface that has been lapped and polished. Down-drawn architectural glass or glass-ceramic articles may be drawn to a thickness of less than about 2 mm.
• down-drawn architectural glass or glass-ceramic articles have a very flat, smooth surface that can be used in its final application without costly grinding and polishing.
• the architectural glass or glass-ceramic article is a glass ceramic
• the architectural glass or glass-ceramic article formed from the down-draw process may be subjected to a ceramming process by which one or more crystalline phases are generated.
• the fusion draw process uses a drawing tank that has a channel for accepting molten architectural glass raw material.
• the channel has weirs that are open at the top along the length of the channel on both sides of the channel.
• the molten architectural glass overflows the weirs. Due to gravity, the molten architectural glass flows down the outside surfaces of the drawing tank as two flowing architectural glass films. These outside surfaces of the drawing tank extend down and inwardly so that they join at an edge below the drawing tank. The two flowing architectural glass films join at this edge to fuse and form a single flowing architectural glass article.
• the fusion draw method offers the advantage that, because the two architectural glass films flowing over the channel fuse together, neither of the outside surfaces of the resulting architectural glass article comes in contact with any part of the apparatus. Thus, the surface properties of the fusion drawn architectural glass article are not affected by such contact.
• the architectural glass or glass- ceramic article is a glass ceramic
• the architectural glass or glass-ceramic article formed from the fusion process may be subjected to a ceramming process by which one or more crystalline phases are generated.
• the slot draw process is distinct from the fusion draw method.
• the molten raw material glass is provided to a drawing tank.
• the bottom of the drawing tank has an open slot with a nozzle that extends the length of the slot.
• the molten glass flows through the slot/nozzle and is drawn downward as a continuous glass article and into an annealing region.
• the architectural glass or glass-ceramic article is a glass ceramic
• the architectural glass article formed from the slot draw process may be subjected to a ceramming process by which one or more crystalline phases are generated.
• the architectural glass article may be formed using a thin rolling process, as described in U.S. Patent No. 8,713,972, U.S. Patent No.
• the architectural glass or glass-ceramic article may be formed by supplying a vertical stream of molten glass, forming the supplied stream of molten glass or glass-ceramic with a pair of forming rolls, maintained at a surface temperature of about 500° C or higher or about 600° C or higher, to form a formed architectural glass ribbon having a formed thickness, sizing the formed ribbon of glass with a pair of sizing rolls, maintained at a surface temperature of about 400° C or lower to produce a sized glass ribbon having a desired thickness less than the formed thickness and a desired thickness consistency.
• the apparatus used to form the glass ribbon may include a glass feed device for supplying a supplied stream of molten glass; a pair of forming rolls maintained at a surface temperature of about 500° C or higher, the forming rolls being spaced closely adjacent each other, defining a glass forming gap between the forming rolls with the glass forming gap located vertically below the glass feed device for receiving the supplied stream of molten glass and thinning the supplied stream of molten glass between the forming rolls to form a formed glass ribbon having a formed thickness; and a pair of sizing rolls maintained at a surface temperature of about 400° C or lower, the sizing rolls being spaced closely adjacent each other, defining a glass sizing gap between the sizing rolls with the glass sizing gap located vertically below the forming rolls for receiving the formed architectural glass ribbon and thinning the formed architectural glass ribbon to produce a sized architectural glass ribbon having a desired thickness and a desired thickness consistency.
• the thin rolling process may be utilized where the viscosity of the architectural glass does not permit use of fusion or slot draw methods.
• thin rolling can be utilized to form the architectural glass or glass-ceramic articles when the glass exhibits a liquidus viscosity less than 100 kP.
• the architectural glass or glass-ceramic article may be acid polished or otherwise treated to remove or reduce the effect of surface flaws.
• the architectural glass or glass-ceramic sheet or article discussed herein has a composition that differs by side surface.
• an exemplary composition is: 69-75 wt.% Si0 2 , 0-1.5 wt.% A1 2 0 3 , 8-12 wt.% CaO, 0-0.1 wt.% CI, 0-500 ppm Fe, 0-500 ppm K , 0.0-4.5 wt.% MgO, 12-15 wt.% Na 2 0, 0-0.5 wt.% S0 3 , 0-0.5 wt.% Sn0 2 , 0-0.1 wt.% SrO, 0-0.1 wt.% Ti0 2 , 0-0.1 wt.% ZnO, and/or 0-0.1 wt.% Zr0 2 .
• an exemplary composition is: 73.16 wt.% Si0 2 , 0.076 wt.% Al 2 0 3 , 9.91 wt.% CaO, 0.014 wt.% CI, 0.1 wt.% Fe 2 0 3 , 0.029 wt.% K 2 0, 2.792 wt.% MgO, 13.054 wt.% Na 2 0, 0.174 wt.% S0 3 , 0.001 Sn0 2 , 0.01 wt.% SrO, 0.01 wt.% Ti0 2 , 0.002 wt.% ZnO, and/or 0.005 wt.% Zr0 2 .
• composition of the architectural glass or glass- ceramic sheet or article discussed herein includes Si0 2 55-85 wt.%, Al 2 0 3 0-30 wt.%, B 2 0 3 0-20 wt.%, Na 2 0 0-25 wt.%, CaO 0-20 wt.%, K 2 0 0-20 wt.%, MgO 0-15 wt.%, BaO 5-20 wt.%, Fe 2 0 3 0.002-0.06 wt.%, and/or Cr 2 0 3 0.0001-0.06 wt.%.
• composition of the architectural glass or glass-ceramic sheet or article discussed herein includes Si0 2 60-72 mol.%, A1 2 0 3 3.4-8 mol.%, Na 2 0 13- 16 mol.%, K 2 0 0-1 mol.%, MgO 3.3-6 mol.%, Ti0 2 0-0.2 mol.%, Fe 2 0 3 0.01-0.15 mol.%, CaO 6.5-9 mol.%, and/or S0 3 0.02-0.4 mol.%.
• the apparatus comprises three zones - a hot zone, a transition zone, and a cool or quench zone.
• the gaps between the top and bottom thermal bearings (heat sinks) in the hot zone and the quench zone are set to the desired spacings.
• Gas flow rates in the hot zone, transition zone, and quench zone are set to ensure centering of the architectural glass material, sheet or part on the air-bearing.
• the hot zone is pre-heated to the desired T 0 , the temperature from which the architectural glass article will be subsequently quenched.
• a separate preheating apparatus such as a batch or continuous furnace.
• architectural glass sheets are pre-heated for greater than 5 minutes prior to loading in the hot zone.
• preheating is done around 450°C.
• the architectural glass article is loaded into the hot zone and allowed to equilibrate, where equilibration is where the architectural glass is uniformly at T 0 .
• T 0 can be determined by the level of strengthening/tempering desired, but is generally kept in the range between the softening point and the glass transition temperature.
• the time to equilibration is dependent at least on the thickness of the architectural glass. For example, for architectural glass sheets of approximately 1.1 mm or less, equilibration occurs in approximately 10 seconds.
• equilibration occurs in approximately 10 seconds to 30 seconds. For thicker sheets, up to approximately 6 mm, the equilibration time may be on the order of 60 seconds.
• T 0 Once the architectural glass has equilibrated to T 0 , it is rapidly transferred through the transition zone on air bearings and into the cool or quench zone.
• the architectural glass article rapidly quenches in the quench zone to a temperature below the glass transition temperature, Tg.
• the architectural glass sheet can be maintained in the quench zone for any period of time from 1 second, 10 seconds, or to several minutes or more, depending on the degree of quench desired and/or the desired temperature of the architectural glass at removal. Upon removal the architectural glass is optionally allowed to cool before handling.
• Example 1 A soda-lime silicate glass plate (e.g., glass comprising at least 70% silicon dioxide by weight, and/or at least 10% sodium oxide by weight, and/or at least 7% calcium oxide by weight) of 5.7 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 690°C for 60 seconds. After equilibrating to To, it is rapidly transferred to the quench zone filled with helium, which has a gap of 91 ⁇ (wherein the gap is the distance between the surface of the glass sheet and the nearest heat sink), where it is held for 10 seconds.
• the resulting article has a surface compression of -312 MPa, a central tension of 127 MPa, and a flatness of 83 ⁇ .
• Example 2 A soda-lime silicate glass plate of 5.7 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 690°C for 60 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 91 ⁇ , where it is held for 10 seconds.
• the resulting article has a surface compression of -317 MPa, a central tension of 133 MPa, and a flatness of about 89.7 micrometers.
• Example 3 A soda-lime silicate glass plate of 1.1 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a To of 700°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone filled with helium, which has a gap of 56 ⁇ , where it is held for 10 seconds.
• the resulting article has a surface fictive temperature measured to be 661°C, a surface compression of -176 MPa, a central tension of 89 MPa, a flatness of 190 ⁇ , and a Vicker's cracking threshold of 10-20 N.
• Example 4 A soda-lime silicate glass plate of 0.55 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 720°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 25 ⁇ , where it is held for 10 seconds, resulting in an effective heat transfer rate of 0.184 cal/(cm 2 - s-°C). The resulting article has a surface compression of -176 MPa and a central tension of 63 MPa. Also, the resulting strengthened articles had a flatness of about 168 (for the initial 710° C temperature sample) and 125 micrometers (for the initial 720° C temperature sample).
• Example 5 A CORNING® GORILLA® Glass plate of 1.5 mm thickness is pre-heated for 10 minutes at 550°C before transferring to the hot zone where it is held at a T 0 of 790°C for 30 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 226 ⁇ , where it is held for 10 seconds.
• the glass article has an improvement in flatness measured to be 113 ⁇ pre-processing and 58 ⁇ post-processing.
• Example 6 A soda-lime silicate glass plate of 0.7 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 730°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone filled with helium, which has a gap of 31 ⁇ , where it is held for 10 seconds, resulting in an effective heat transfer rate of 0.149 cal/(cm 2 -s-°C). The resulting article has a surface compression of -206 MPa, a central tension of 100 MPa, and a flatness of 82 ⁇ . Upon fracture, the glass sheet is observed to "dice" (using standard terminology for 2 mm thickness or greater sheet dicing - i.e., a 5x5 cm square of glass sheet breaks into 40 or more pieces) suggesting that the sheet is fully tempered.
• "dice" using standard terminology for 2 mm thickness or greater sheet dicing - i.e., a 5x5 cm
• Example 7 A Borofloat-33 glass plate of 3.3 mm thickness is pre-heated for 10 minutes at 550°C before transferring to the hot zone where it is held at a T 0 of 800°C for 30 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 119 ⁇ , where it is held for 10 seconds. The resulting article has a flatness of 120 ⁇ . Upon fracture of the part it is observed to "dice" (using standard terminology for 2 mm or greater thickness sheet dicing - i.e., a 5x5 cm square of glass sheet breaks into 40 or more pieces) showing that the sheet is fully tempered.
• "dice" using standard terminology for 2 mm or greater thickness sheet dicing - i.e., a 5x5 cm square of glass sheet breaks into 40 or more pieces
• Example 8 A soda-lime silicate glass plate of 3.2 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 690°C for 30 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 84 ⁇ , where it is held for 10 seconds.
• the resulting article has a surface compression of -218 MPa, a central tension of 105 MPa, and a flatness of 84 ⁇ .
• Example 9 A soda-lime silicate glass plate of 0.3 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 630°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 159 ⁇ , where it is held for 10 seconds. The resulting article has membrane stresses which are observable by gray field polarimetry, suggesting the glass has incorporated the thermal stress.
• Example 10 - A CORNING® GORILLA® Glass plate of 0.1 mm thickness is pre-heated for 10 minutes at 550°C before transferring to the hot zone where it is held at a T 0 of 820°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 141 ⁇ , where it is held for 10 seconds, resulting in an effective heat transfer rate of 0.033 cal/(cm 2 -s-°C). Upon fracture, the resulting article displays behavior consistent with a residually stressed glass.
• Example 11 A soda-lime silicate glass plate of 1.1 mm thickness is pre-heated for 10 minutes at 450°C before transferring to the hot zone where it is held at a T 0 of 700°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 65 ⁇ , where it is held for 10 seconds, resulting in an effective heat transfer rate of 0.07 cal/(cm 2 -s- °C).
• the resulting article has a surface Active temperature measured to be 657°C, a surface compression of -201 MPa, a central tension of 98 MPa, a flatness of 158 ⁇ , and a Vicker's cracking threshold of 10-20 N.
• Example 12 - A CORNING® GORILLA® Glass plate of 1.1 mm thickness is pre-heated for 10 minutes at 550°C before transferring to the hot zone where it is held at a To of 810°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone which has a gap of 86 ⁇ , where it is held for 10 seconds, resulting in an effective heat transfer rate of 0.058 cal/(cm 2 - s-°C).
• the resulting article has a surface fictive temperature measured to be 711°C, a surface compression of -201 MPa, a central tension of 67 MPa, and a Vicker's cracking threshold of 20- 30 N.
• Example 13 - A CORNING® GORILLA® Glass plate of 1.1 mm thickness is pre-heated for 10 minutes at 550°C before transferring to the hot zone where it is held at a T 0 of 800°C for 10 seconds. After equilibrating it is rapidly transferred to the quench zone, which has a gap of 91 ⁇ , where it is held for 10 seconds.
• the resulting article has a surface fictive temperature measured to be 747°C, a surface compression of -138 MPa, a central tension of 53 MPa, a flatness of 66 ⁇ , and a Vicker's cracking threshold of 20-30 N.
• Example - a 5.7 mm thick sheet of glass comprising at least 70% silicon dioxide by weight, and/or at least 10% sodium oxide by weight, and/or at least 7% calcium oxide by weight was run with helium gas and gaps 204a, 204b (FIG. 21) of about 90 micrometers.
• the glass was heated to an initial temperature of about 690° C and quickly cooled.
• the resulting strengthened article had a negative tensile stress of about 300 MPa on surfaces thereof and a positive tensile stress of about 121 MPa in the center. Also, the resulting strengthened article had a flatness of about 106.9 micrometers.
• the strengthening process also flattened the strengthened glass or glass ceramic article.

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• 2016
  • 2016-07-28 EP EP16751079.1A patent/EP3328807A1/de not_active Withdrawn
  • 2016-07-28 KR KR1020187005875A patent/KR20180035862A/ko unknown
  • 2016-07-28 CA CA2994236A patent/CA2994236A1/en not_active Abandoned
  • 2016-07-28 CN CN201680055008.5A patent/CN108883977A/zh not_active Withdrawn
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