EP3464660B1 - Procédé de traitement d'une pièce de fabrication comprenant un métal à base de titane, et objet - Google Patents

Procédé de traitement d'une pièce de fabrication comprenant un métal à base de titane, et objet Download PDF

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Publication number
EP3464660B1
EP3464660B1 EP17727508.8A EP17727508A EP3464660B1 EP 3464660 B1 EP3464660 B1 EP 3464660B1 EP 17727508 A EP17727508 A EP 17727508A EP 3464660 B1 EP3464660 B1 EP 3464660B1
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Prior art keywords
workpiece
grade
titanium
quenching
titanium metal
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German (de)
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EP3464660A1 (fr
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Pär NYMAN
Erik Johansson
Richard Larker
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Sentinabay AB
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Sentinabay AB
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/042—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material including a refractory ceramic layer, e.g. refractory metal oxides, ZrO2, rare earth oxides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/048—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material with layers graded in composition or physical properties
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor

Definitions

  • the present invention generally concerns a method of treating a workpiece comprising titanium metal. More specifically it relates to a method which comprises nitriding at least a portion of the workpiece such that a surface layer of the titanium alloy is converted to titanium nitride.
  • the invention also concerns an object, which has been subjected to such a method.
  • Titanium has found an increasing use in various technical fields such as in the manufacturing of machine parts and other components within the automotive, aerospace, mining, medical and other industries.
  • chemically pure titanium is not utilized industrially but the titanium is alloyed to form various alloys with differing characteristics.
  • examples of some frequently used titanium alloys are so called commercially pure (cp) titanium or Grade 2 titanium (sometimes referred to as unalloyed), Grade 5 titanium (Ti-6Al-4V) and Grade 9 titanium (Ti-3Al-2.5V).
  • cp commercially pure
  • Grade 2 titanium sometimes referred to as unalloyed
  • Grade 5 titanium Ti-6Al-4V
  • Grade 9 titanium Ti-3Al-2.5V
  • alloy so called commercially pure titanium metal is referred to as alloy.
  • the titanium alloys generally have some characteristics that are favourable in many applications. Examples of such characteristics are low density, high specific strength or strength-to-weight ratio, excellent corrosion resistance and ability to withstand high temperatures.
  • the low density and high specific strength e.g. contributes to reduce energy consumption and environmental impact when producing machine parts and other components.
  • Some titanium alloys are also non-toxic which is used e.g. for producing orthopaedic and dental prosthesis and implants.
  • one technical disadvantage of titanium alloys is the risk of adhesive seizure in highly loaded sliding or rolling contacts.
  • PVD Physical Vapour Deposition
  • An emerging method is conversion of the titanium alloy surface by nitriding the titanium alloy.
  • ceramic titanium nitrides such as ⁇ -TiN (face-centered cubic) and ⁇ -Ti 2 N (tetragonal) are formed in an outermost first surface layer portion of the work piece.
  • the nitrides considerably increase the hardness and thereby the load-carrying capacity of the surface layer.
  • the nitriding process also results in a second metallic layer portion where nitrogen is diffused into the titanium alloy just beneath the ceramic layer.
  • the nitrogen concentration in this second layer portion is highest adjacent to the first nitride layer portion and is reduced gradually at increased depth from the surface, thereby forming a nitrogen gradient in the surface layer.
  • the nitrogen gradient results in increased hardness and support of the first nitride layer portion.
  • This method is usually carried out by processing the workpiece in vacuum furnaces.
  • the main limitations of these treatments are long and costly processes, resulting thin nitride layers and shallow penetration of nitrogen into the bulk metal, thereby forming merely a relatively weak support for the hard and brittle nitride layers.
  • Hot Isostatic Pressing is a process that is today mainly used to either eliminate the internal porosity of metal castings of titanium and nickel-based super-alloys or to densify various metallic and ceramic powder bodies to solid materials.
  • the HIP process subjects a workpiece to concurrently elevated temperature and isostatic gas pressure (whereby pressure is applied to the material from all directions) in a high pressure containment vessel.
  • An inert gas such as argon is usually used to prevent chemical reactions, and the pressurizing gas is usually raised to a pressure level between 100-200 MPa by a combination of pumping and electrical heating of the gas surrounding the work pieces.
  • the simultaneous application of heat and pressure eliminates internal porosity through a combination of plastic deformation, creep, and diffusion bonding.
  • US 4,511,411 further discloses a method for increasing the surface hardness of a titanium alloy component.
  • the method comprises; placing a component of titanium alloys in an autoclave, pumping nitrogen gas or ammonia into the autoclave and exposing the component in the autoclave for three hours to a pressure of 900 bar (90 MPa) and a temperature of 1 000°C.
  • An object of the present invention is to provide an enhanced method of treating a workpiece comprising a titanium metal alloy.
  • Another object is to provide such a method by which a surface layer of the titanium metal alloy workpiece is efficiently hardened by nitriding.
  • Yet another object is to provide such a method which allows for an enhanced control of the resulting material properties of the workpiece.
  • Still another object is to provide such a method by which the resulting microstructure of the workpiece may be efficiently and precisely controlled.
  • a further object is to provide such a method which may be carried out in an efficient, time saving manner at a comparatively low cost.
  • the method is used for treating a workpiece comprising at least one titanium metal and involves that a titanium metal surface layer of the workpiece is converted to titanium nitrides.
  • the method comprises the steps of; a) heating the workpiece to an initial nitriding temperature and; b) subjecting said workpiece to one or more nitriding temperatures for predetermined time(s) in a nitrogen containing gas under high pressure at Hot Isostatic Pressing (HIP) conditions for converting the titanium metal surface layer to a first layer portion consisting of ceramic titanium nitrides and a second layer portion comprising a nitrogen gradient in the titanium metal.
  • HIP Hot Isostatic Pressing
  • the method further comprises c) quenching the workpiece in the nitrogen containing gas under high pressure at Hot Isostatic Pressing (HIP) conditions as a first step in a hardening heat treatment, in order to further strengthen the titanium metal below the first ceramic nitride layer portion formed in step b).
  • HIP Hot Isostatic Pressing
  • the method according to the present invention improves the mechanical properties of the workpiece.
  • the high nitrogen gas pressure enhances nitrogen diffusion from the gas into the titanium metal, resulting in conversion to nitrides in the first ceramic layer portion and creating a nitrogen gradient in the second titanium metal layer portion.
  • Nitriding at HIP conditions thus results in thick ceramic ⁇ -TiN and ⁇ -Ti 2 N surface layers and in a deep nitrogen gradient layer which additionally exhibits a high nitrogen content immediately below the nitride layer to improve its load-carrying capacity.
  • these favourable features is combined with an improved heat transfer by the highly pressurized gas during the quenching step. Quenching at HIP conditions not only increases the heat transfer but also promotes equal cooling of all surfaces regardless of their position and orientation on the workpieces and within the pressure vessel.
  • the prior art does not disclose a nitriding method of titanium alloys which subsequently comprises quenching under high isostatic pressure as a first step in a hardening heat treatment, using Hot Isostatic Pressing also for prior nitriding and concurrent elimination of casting porosity and/or residual stresses in the titanium alloys.
  • the present invention is based on the realization that recent developments in HIP equipment makes it possible to utilize the improved heat transfer capability achieved by Hot Isostatic Pressing for quenching and thereby to carry out hardening heat treatments under HIP conditions.
  • Quenching the workpiece at isostatic pressures of up to 200 MPa in a gas such as nitrogen, which at these pressures has a viscosity resembling water provides that the titanium metal comprising both the nitrogen gradient portion and the bulk titanium metal can be subjected to very high cooling rates (delta T/s).
  • the excellent heat transfer capabilities at high isostatic pressures also provide that the cooling rate may be precisely controlled within wide intervals.
  • the resulting material properties after quenching may be precisely controlled by varying and controlling the cooling rate at different stages of the quenching process.
  • the quenching may e.g.
  • the nitrogen gradient layer and the bulk metal may thus be formed to constitute an excellent support for the hard and brittle nitride layers at the surface.
  • the method may be utilized for producing workpieces and components which have excellent properties in regard of e.g. hardness, low friction, ductility, durability, specific strength, temperature resistance and low density.
  • the invention also allows for that the cooling rate is further increased by utilizing heat exchangers and fans within the pressure chamber in which the method according to the invention is carried out. This enables even larger cross-sections of a workpiece to be cooled at sufficient rates. Since the workpiece is within a firm isostatic grip, its macroscopic shape is still preserved, and such high cooling rates will therefore not result in large residual stresses, cracks or warpage.
  • the invention further allows for that both nitriding the surface layer and quenching the workpiece is carried out subsequently or even at least partly overlapping in a continuous method step. Irrespective of if the nitriding and quenching operations are carried out overlapping or subsequently, both processes may be carried out in one and the same HIP chamber, thereby eliminating any need for intermediate cooling, transportation, storing, reheating and other handling of the workpiece.
  • the combined nitriding and quenching in a single HIP chamber further eliminates the need for separate chambers, ovens, furnaces and other equipment needed when conducting nitriding and quenching as separate operations.
  • the method according to the present invention therefore provides a cost-effective way of obtaining titanium nitride layers on titanium alloys, which in addition is heat treated for superior properties. Additionally, improved strength and ductility with reduced scatter may be obtained due to the elimination of all internal porosity in the cast work piece. Further, the method offers the possibility of manufacturing work pieces with closer machining tolerances since residual stresses are eliminated from the work piece, and batch-processing time may be decreased.
  • the quenching step c) is carried out under HIP conditions, a rapid cooling, typically greater than or equal to 100 K /min is possible, exceeding the rate of quenching in oils, since the pressurized gas provides efficient heat transfer.
  • the workpiece may, before step c), be subjected to at least one temperature at or above the ⁇ phase transus temperature for the titanium alloy in question for solution treatment of the titanium alloy to convert prior ⁇ phase or ⁇ + ⁇ phase structure to solely or predominantly ⁇ phase.
  • microstructures that are particularly favourable at some applications may be achieved after completing the method.
  • Step c) involves quenching the workpiece at a cooling rate of at least 150 K/min, which is high enough to, at least partly, transform ⁇ phase by a martensitic transformation directly to ⁇ ' phase or ⁇ " phase. This also allows for achieving microstructures that give the workpiece properties which are desirable at various applications.
  • the quenching rate may be chosen to delay the remaining transformation of ⁇ phase to ⁇ phase at lower temperatures, resulting in substantially finer microstructures.
  • the workpiece may, after step c), be subjected to at least one aging temperature at a predetermined time to obtain precipitation hardening of the titanium alloy.
  • the workpiece comprises titanium Grade 5
  • it may e.g. be suitable to carry out the aging step at 400-600 °C.
  • the workpiece may be cooled to room temperature after quenching or after subjecting the workpiece to the at least one aging temperature for a predetermined time.
  • the workpiece may be positioned in one and the same HIP chamber during the entire execution of the method.
  • All intermediate transportation, storing other handling as well as cooling and re-heating of the workpiece is eliminated.
  • the workpiece may be subjected to the nitrogen containing gas under high pressure at Hot Isostatic Pressing (HIP) conditions during the entire execution of the method.
  • HIP Hot Isostatic Pressing
  • the titanium metal may preferably comprise at least one of the following; titanium alloy of Grade 1, Grade 2, Grade 5 or Grade 9. However, several other titanium alloys may also be treated by means of the method.
  • Step c) may be carried out at Hot Isostatic Pressure conditions where the nitrogen gas pressure is, at least initially, above 10 MPa. It may at some instances be suitable to reduce the gas pressure after quenching such that an excessive pressure does not counteract precipitation of particles with higher specific volume (i.e. lower density) during aging. However, the gas pressure should at all instances be maintained at least at or above 5 MPa for achieving sufficient heat transfer and thus temperature control.
  • the workpiece may comprise Grade 2 titanium and step c) may then comprise quenching the workpiece at a quenching rate of at least 900 K / min and preferably at least 1200 K / min.
  • the workpiece may alternatively comprise Grade 5 titanium and step c) may then comprise quenching the workpiece at a quenching rate of at least 210 K / min and preferably at least 420 K/ min.
  • step c) may comprise quenching the workpiece at a quenching rate of at least 300 K / min.
  • all of the steps for nitriding, quenching, aging and cooling to room temperature may be carried out at least partly under HIP conditions in a single HIP chamber.
  • the entire treatment of the workpiece may be accomplished, without interruptions, in a single work station.
  • all intermediate handling between different works stations and operations is eliminated.
  • the cooling to room temperature of the workpiece is carried out in the HIP chamber, the high pressure may be maintained during the entire process. The temperature however, naturally needs to be decreased, such that this treatment step will not be carried out entirely at the high temperatures normally prevailing at HIP conditions.
  • steps a) through c) need necessarily be carried out under HIP conditions, as most benefits from HIP are gained during steps a) through c), while the aging treatment may take place in another furnace and the cooling to room temperature may be carried out in the aging furnace, another furnace or in the ambient surrounding.
  • the method thus allows for producing objects with extraordinary favourable properties and the invention also relates to such objects.
  • the invention concerns an object comprising a titanium metal alloy of Grade 2, Grade 5 or Grade 9, which object exhibits a surface layer comprising a first nitride layer portion and second titanium metal portion with a nitrogen gradient, which surface layer extends to a depth of at least 50 ⁇ m when the titanium metal alloy is Grade 2 or Grade 9 and at least 75 ⁇ m when the titanium metal alloy is Grade 5.
  • the object may exhibit a hardness of at least 265 HV0,1 at 25 ⁇ m; at least 325 HV0,1 at 25 ⁇ m and at least 420 HV0,1 at 50 ⁇ m, when the titanium metal alloy is Grade 2, Grade 9 and Grade 5 respectively.
  • the titanium alloy of the object may exhibit solely or predominantly ⁇ ' phase or ⁇ " phase structures.
  • the object may constitute or form part of a component chosen from a group of components comprising; automotive, aerospace, mining and medical components.
  • the workpiece thus comprises a nitrided titanium alloy having an improved combination of high strength, ductility and hardness.
  • a workpiece is intended for use particularly, but not exclusively, in applications where high wear resistance is required or in applications in which strict specifications must be consistently met.
  • Fig. 1 is a diagram representing temperature (T) and time (t) and schematically illustrating a method according to an embodiment of the invention.
  • Fig. 2 schematically illustrates a cross section in perspective view of a Hot Isostatic Press containing a work piece.
  • Fig. 1 illustrates a nitriding heat treatment cycle according to an embodiment of the invention.
  • a workpiece 12 consisting of or comprising at least one titanium alloy, such as Grade 2, Grade 5 or Grade 9, has been placed in a hot isostatic press 10 as shown by Fig. 2 .
  • the workpiece may be, for example, engine parts such as wrist pins, hydraulic suspension parts, transmission parts, valves, pumps, orthopaedic or dental implants or prosthesis or the like.
  • the workpiece 12 is surrounded by a nitrogen containing gas 14 inside a chamber of the hot isostatic press 10.
  • the gas is nitrogen gas (N2). It is however possible also to use other nitrogen-containing gases such as ammonium gas.
  • the pressure of the gas 14 is increased, typically to a range between 100 and 200 MPa. The increase of the gas pressure may take place before, simultaneously with or after increasing the temperature in the gas 14. Normally, the increase of the pressure and the temperature of the gas take place at least partly simultaneously.
  • the workpiece 12 is in step a) heated to an initial nitriding temperature (T n1 ).
  • T n1 initial nitriding temperature
  • the workpiece is thereafter subjected to this nitriding temperature T n1 for a first predetermined time.
  • the temperature may during the nitriding step b) be increased or decreased to any further nitriding temperature T n2 and kept at this temperature for any second predetermined time.
  • the nitriding step b) may thus comprise subjecting the workpieces to any number of different nitriding temperatures for any respective desirable times.
  • the titanium alloy surface layer is converted to titanium nitrides.
  • TiN is formed in the outermost layer and Ti2N is formed further in from the outer surface.
  • nitrogen is diffused further into the titanium metal layer beneath the ceramic nitrides. In this metal layer portion the nitrogen content typically varies such that the nitrogen content is higher adjacent the nitrides and gradually decreases with increased material depth from the surface. I.e. the nitriding step b) results in the formation of a ceramic nitride layer portion and nitrogen gradient layer portion in the titanium metal.
  • the initial nitriding temperature T n1 lies above the ⁇ transus temperature of the titanium alloy in question.
  • the workpiece is heated above the ⁇ transus temperature to form the ⁇ structure of the titanium alloy in question, before quenching the workpiece.
  • step c) the workpiece 12 is rapidly cooled during the quenching step of the method.
  • the temperature of the workpiece 12 is decreased from an initial quenching temperature T q1 to a final quenching temperature T q2 .
  • the initial quenching temperature T q2 is equal to the last nitriding temperature (T n1 in the example shown by solid lines in Fig. 1 ).
  • the quenching may be carried out under an essentially constant cooling rate throughout the quenching step. However, it may be advantageous to vary the cooling rate such that the temperature decrease per second is different during the passages of different temperature intervals during the quenching process. Such a varying quenching is indicated by the dashed line c' in Fig. 1 .
  • the quenching process primarily influences the properties of the titanium metal including the nitrogen gradient layer portion below the nitride layers in the work piece.
  • the quenching step of the method may be favourably used for controlling the material properties of the entire workpiece.
  • An important aspect of the invention is that the quenching step is carried out under hot isostatic pressing conditions.
  • the high isostatic pressures prevailing in the chamber greatly contributes to an enhanced heat transfer between the surrounding gas and the workpiece.
  • the efficiency of the quenching process may be further enhanced by introducing heat exchangers, fans and other heat transfer enhancing means in the chamber.
  • the quenching step c) is followed by an aging step d).
  • the workpiece is held at and aging temperature for a predetermined time.
  • the aging temperature is equal to the final quenching temperature T q2 .
  • the aging step d) is carried out immediately subsequent to finalizing the quenching and under high isostatic pressure in the chamber of the hot isostatic press 10.
  • aging may be carried out at any pressure including atmospheric pressure inside or outside the hot isostatic press, e.g. in a conventional furnace. At some embodiments the aging step may even be fully dispensed with.
  • step e the workpiece is cooled to room temperature.
  • cooling may take place under high pressure in the hot isostatic press 10 or under lower, such as atmospheric, pressure in the same press 10. Alternatively, the cooling step may be carried out outside of the hot isostatic press 10.
  • the workpiece may then be directly used in any application in which it is likely to be subjected to stress, strain, impact and/or wear under operation.
  • the workpiece may be machined, either before the heating step a) or after the nitriding, quenching and aging is completed, for example, if some particular surface treatment is required.
  • Carrying out the heating and nitriding step a) under HIP conditions accelerates the heating rate, nitriding rate and deep diffusion of nitrogen into the bulk titanium alloy.
  • Carrying out the quenching step c) under HIP conditions accelerates the cooling rate and concurrently reduces residual stresses due to superplastic conditions during a substantial part of the quenching process.
  • Utilizing HIP conditions during any of the steps a) to d) and particularly steps a), b) and c) also results in the following advantages: elimination of casting porosity, elimination of residual stresses, consistent material properties and consistent machining properties.
  • Fig. 2 shows a hot isostatic press 10 in which one workpiece 12 is subjected to a method according to the embodiment of the invention illustrated in Fig. 1 .
  • one or more workpieces may be placed inside the hot isostatic press 10 and that the work piece(s) can be of any shape and size as long as it/they can fit inside the hot isostatic press 10.
  • the workpiece 12 is radially and axially outwardly surrounded firstly by a pressurized gas 14 acting normally at all surfaces, secondly by furnace walls, thirdly by a heat insulating mantle and fourthly by the water-cooled pressure vessel walls, being held in compression by pre-stressed wire windings 16.
  • All of the surfaces of the workpiece 12 as well as all of the surfaces of the furnace and the heat insulating mantle and the internal surfaces of the pressure vessel may be subjected to high-pressure nitrogen gas 14, such as nitrogen at a pressure of up to approx. 200 MPa.
  • step a) the temperature of the gas was increased until the temperature of the workpiece reached 960°C. Simultaneously, the pressure of the gas was increased to 170 MPa.
  • step b) the same temperature and gas pressure was maintained for 2 hours.
  • step c the workpiece was quenched by cooling nitrogen gas according to the following cooling rates of the gas:
  • the temperature of the gas was measured by thermocouples.
  • step e the work pieces were cooled to room temperature.
  • the thin-walled tubes were then analysed by microstructural determination and it was found that the material comprised a Widmann Toon structure with non-continuous ⁇ -phase.
  • the microstructural analyse further determined the material of thin-walled tubes to have been cooled at >1200 K/min (>20 K/s) through the 888-868°C interval for ⁇ + ⁇ structure formation at this cooling rate, corresponding to a water quench (WQ) rate. Since the cooling rate of the nitrogen gas was more than twice as high through at this temperature interval and since the heat transfer coefficient (>1000 W/m 2 ⁇ K) is high between the dense gas and the thin-walled titanium tube, it is reasonable that the metal core could indeed be cooled by 20 K/s.
  • Microstructural evaluation further showed a formation of a 20 ⁇ m layer of ⁇ -TiN + ⁇ -Ti 2 N with hardness up to 1068 ⁇ 22 HV0.05 at 1 ⁇ m depth and 519 HV0.025 at 10 ⁇ m depth, followed by a sloping decrease in hardness 30 ⁇ m further into the titanium metal to the bulk level of 230-250 HV0.1.

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  • Mechanical Engineering (AREA)
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Claims (16)

  1. Procédé de traitement d'une pièce de fabrication (12) comprenant un métal à base de titane, dans lequel une couche de surface métallique en titane de la pièce de fabrication est convertie en nitrures de titane, ledit procédé comprenant les étapes suivantes :
    a) chauffage de la pièce de fabrication (12) à une température de nitruration initiale (Tn1) ;
    b) soumission de ladite pièce de fabrication à une ou plusieurs températures de nitruration (Tn1, Tn2) pour une/des durée(s) prédéterminée(s) dans un gaz contenant de l'azote (14) sous haute pression dans des conditions de pression isostatique à chaud (HIP) pour convertir la couche de surface métallique en titane en une première partie de couche constituée de nitrures de titane et une deuxième partie de couche constituée d'un gradient d'azote dans le métal à base de titane ;
    le procédé étant caractérisé en ce que
    c) trempe de la pièce de fabrication (12) dans le gaz contenant de l'azote (14) sous haute pression dans des conditions de pression isostatique à chaud (HIP) à une vitesse de trempe d'au moins 150 K/min, pour renforcer le métal à base de titane en dessous de la première partie de couche de nitrures, formée à l'étape b).
  2. Procédé selon la revendication 1, dans lequel la pièce de fabrication (12) est, avant l'étape c), soumise à au moins une température (Tn1) à la température de transition de phase β ou au-dessus pour l'alliage de titane en question pour un traitement de solution de l'alliage de titane, pour convertir une structure de phase α ou de phase α+β préalable en une structure de phase essentiellement β uniquement.
  3. Procédé selon la revendication 1 ou 2, dans lequel l'étape c) comprend la trempe de la pièce de fabrication (12) à une vitesse de refroidissement suffisamment élevée pour transformer au moins partiellement la phase β par une transformation martensitique directement en une phase α' ou en une phase α".
  4. Procédé selon l'une quelconque des revendications 1 à 3, dans lequel ladite vitesse de trempe est sélectionnée pour retarder la transformation restante de phase β en phase α à des températures moins élevées, résultant dans des microstructures substantiellement plus fines.
  5. Procédé selon l'une quelconque des revendications 1 à 4, dans lequel la pièce de fabrication (12), après l'étape c), est soumise à au moins une température de vieillissement (Tq2) pour une durée prédéterminée pour obtenir un durcissement de précipitation du métal à base de titane.
  6. Procédé selon l'une quelconque des revendications 1 à 5, dans lequel la pièce de fabrication (12) est refroidie à une température ambiante après la trempe ou après soumission de la pièce de fabrication à l'au moins une température de vieillissement pour la durée prédéterminée.
  7. Procédé selon l'une quelconque des revendications 1 à 6, dans lequel la pièce de fabrication (12) est positionnée dans une seule et même chambre de pression isostatique à chaud pendant toute l'exécution du procédé.
  8. Procédé selon l'une quelconque des revendications 1 à 7, dans lequel la pièce de fabrication (12) est soumise au gaz contenant de l'azote sous haute pression dans des conditions de pression isostatique à chaud (HIP) pendant toute l'exécution du procédé.
  9. Procédé selon l'une quelconque des revendications 1 à 8, dans lequel le métal à base de titane comprend l'un au moins parmi les suivants : alliage de titane de Grade 1, de Grade 2, de Grade 5 ou de Grade 9.
  10. Procédé selon l'une quelconque des revendications 1 à 9, dans lequel ladite pièce de fabrication (12), à l'étape b), est trempée à une vitesse de trempe suffisante pour empêcher la formation de la structure de phase a.
  11. Procédé selon l'une quelconque des revendications 1 à 10, dans lequel l'étape c) est exécutée dans des conditions de pression isostatique à chaud, où la pression du gaz d'azote est au moins initialement supérieure à 10 MPa.
  12. Procédé selon l'une quelconque des revendications 1 à 11, dans lequel la pièce de fabrication comprend un alliage de titane de Grade 2, de Grade 5 ou de Grade 9, et dans lequel l'étape c) comprend la trempe de la pièce de fabrication à une vitesse de trempe de :
    au moins 900 K/min et de préférence au moins 1200 K/min pour le Grade 2 ;
    au moins 210 K/min et de préférence au moins 420 K/min pour le Grade 5 ; ou
    au moins 300 K/min pour le Grade 9.
  13. Objet comprenant un alliage de métal à base de titane de Grade 2, de Grade 5 ou de Grade 9, caractérisé en ce que l'objet présente une couche de surface comprenant une première partie de couche de nitrures et une deuxième partie de métal à base de titane présentant uniquement ou essentiellement des structures de phase α' ou de phase α" et un gradient d'azote, ladite couche de surface s'étendant à une profondeur d'au moins 50 µm lorsque l'alliage de métal à base de titane est de Grade 2 ou de Grade 9 et d'au moins 75 µm lorsque l'alliage de métal à base de titane est de Grade 5.
  14. Objet selon la revendication 13, dans lequel l'objet présente une dureté d'au moins 265 HV0,1 à 25 µm ; d'au moins 325 HV0,1 à 25 µm et d'au moins 420 HV0,1 à 50 µm, lorsque l'alliage de métal à base de titane est de Grade 2, de Grade 9 et de Grade 5, respectivement.
  15. Objet selon l'une quelconque des revendications 13 ou 14, ledit objet constituant ou faisant partie d'un composant sélectionné parmi un groupe de composants comprenant : des composants automobiles, aéronautiques, miniers et médicaux.
  16. Objet selon l'une quelconque des revendications 13 à 15, ledit objet ayant été soumis à un procédé selon l'une quelconque des revendications 1 à 13.
EP17727508.8A 2016-05-23 2017-05-19 Procédé de traitement d'une pièce de fabrication comprenant un métal à base de titane, et objet Active EP3464660B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE1650705A SE540497C2 (en) 2016-05-23 2016-05-23 Method of treating a workpiece comprising a titanium metal and object
PCT/EP2017/062155 WO2017202728A1 (fr) 2016-05-23 2017-05-19 Procédé de traitement d'une pièce de fabrication comprenant un métal à base de titane, et objet

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EP3464660A1 EP3464660A1 (fr) 2019-04-10
EP3464660B1 true EP3464660B1 (fr) 2020-07-08

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US (1) US20190292641A1 (fr)
EP (1) EP3464660B1 (fr)
CN (1) CN109154040B (fr)
SE (1) SE540497C2 (fr)
WO (1) WO2017202728A1 (fr)

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CN114182196B (zh) * 2021-12-02 2024-01-19 贵州师范大学 钛合金真空气体阶梯渗氮方法

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CN103643243B (zh) * 2013-12-11 2016-04-06 江苏大学 一种金属材料高强韧化表面改性方法

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Publication number Publication date
CN109154040A (zh) 2019-01-04
SE540497C2 (en) 2018-09-25
SE1650705A1 (en) 2017-11-24
EP3464660A1 (fr) 2019-04-10
CN109154040B (zh) 2019-12-10
WO2017202728A1 (fr) 2017-11-30
US20190292641A1 (en) 2019-09-26

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