EP3724359A1 - Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée, procédé de fabrication d'un tel produit plat en acier - Google Patents

Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée, procédé de fabrication d'un tel produit plat en acier

Info

Publication number
EP3724359A1
EP3724359A1 EP18825919.6A EP18825919A EP3724359A1 EP 3724359 A1 EP3724359 A1 EP 3724359A1 EP 18825919 A EP18825919 A EP 18825919A EP 3724359 A1 EP3724359 A1 EP 3724359A1
Authority
EP
European Patent Office
Prior art keywords
hot
max
flat steel
steel product
strength
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP18825919.6A
Other languages
German (de)
English (en)
Other versions
EP3724359B1 (fr
Inventor
Ingwer Denks
Joachim SCHÖTTLER
Christian PELZ
Patrick WITTELER
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP3724359A1 publication Critical patent/EP3724359A1/fr
Application granted granted Critical
Publication of EP3724359B1 publication Critical patent/EP3724359B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium 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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to a high-strength, hot-rolled steel flat product with high edge crack resistance and at the same time high bake hardening potential.
  • the invention relates to a method for producing such
  • the invention relates to steel flat products of steels having a multiphase structure, which generally contains tempered bainite, and having a yield strength Rp0.2 in the range of 660 to 820 MPa, in particular for the production of components for the automotive industry, in addition to a high tensile strength of at least 760 MPa and an A80 elongation at break of at least 10% must have a high hole widening capacity with a hole widening ratio of over 30% and a high bake hardening potential with a BH2 value of more than 30 MPa.
  • BH bake-hardening effect
  • the bake hardening effect can be described as having a BH2 value defined as the increase in yield strength after a plastic pre-strain of 2% and a subsequent heat treatment.
  • the bake-hardening effect for example, the increase in the buckling strength of a component can be achieved by a suitable heat treatment takes place after shaping the component.
  • Bainitic steels are according to EN 10346 steels, which are characterized by a comparatively high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Due to the chemical composition a good weldability is given.
  • the microstructure typically consists of bainite with proportions of ferrite. Occasionally small proportions of other phases, such as martensite and retained austenite, may be present in the microstructure.
  • Such a steel is disclosed among others, for example, in the published patent application DE 10 2012 002 079 A1. The disadvantage here, however, is not yet sufficiently high Lochetzbergerweitever- to like.
  • the weight of the vehicles can be reduced by simultaneously improving the forming behavior of the steels used and the component behavior during production and operation.
  • High- to ultrahigh-strength steels must therefore meet comparatively high demands in terms of their strength, ductility and energy absorption, in particular during their processing, such as stamping, hot and cold forming, thermal quenching (eg air hardening, press hardening), welding and / or surface treatment , eg a metallic finish, organic coating or varnish.
  • Newly developed steels must therefore, in addition to the required weight reduction due to reduced sheet thicknesses, meet the increasing material requirements for yield strength, tensile strength, hardening behavior and elongation at break with good processing properties, such as formability and weldability.
  • the hole-expanding capacity is a material property that describes the resistance of the material to crack initiation and crack propagation during forming operations in near-edge areas, such as collaring.
  • the Lochetzweite brin is normatively regulated, for example, in ISO 16630. Thereafter, holes punched in a sheet metal are widened by means of a dome. The measured variable is the change in the output diameter of the
  • An improved edge crack resistance means increased forming capacity of the sheet edges and can be described by an increased Lochetzweiteabmögen. This situation is known under the synonyms “Low Edge Crack” (LEC) or “High Hole Expansion” (HHE) and xpand®.
  • the present invention based on the object to provide a high-strength, hot-rolled steel flat product with good forming properties, especially with high edge crack resistance and a high bake hardening potential and a method for producing such a flat steel product, based on the steel a good Combination of strength and forming properties.
  • a high strength hot rolled steel flat product with high edge crack resistance made from a steel with a yield strength Rp0.2 of 660 to 820 MPa, a BH2 value of over 30 MPa and a hole expansion ratio of over 30% and a structure consisting of two main components, wherein a first major component of the structure has a content of at least 50%, consisting of one or more individual components of ferrite, annealed Bainite and tempered martensite, each containing less than 5% of carbides, and wherein a second major constituent of the structure comprises from 5% to at most 50% of one or more constituents of martensite, retained austenite, bainite or perlite having the following chemical composition Steel (in% by weight):
  • Ni + Mo up to 0.5
  • the flat steel product according to the invention preferably also has a high hole expansion ratio of more than 30% with simultaneously high tensile strength of 760 to 960 MPa and high bake hardening potential BH2 of more than 30 MPa.
  • the flat steel product contains, in order to achieve particularly favorable combinations of properties, the following alloy composition in weight%: C: 0.04 to 0.08, Si: 0.03 to 0.4, Mn: 1.4 to 2 , 0, P: max. 0.08, S: max. 0.01, N: max. 0.01, AI: up to 0.1, Ni + Mo: up to 0.5, Nb: up to 0.08, Ti: up to 0.2, Nb + Ti: min. 0.03 and particularly advantageous: C: 0.04 to 0.08, Si: 0.03 to 0.4, Mn: 1, 4 to 2.0, P: max. 0.08, S: max. 0.01, N: max.
  • the comparatively carbon-rich second main constituent is advantageously embedded island-like in the comparatively low-carbon, first matrix constituent, the matrix.
  • the island size is about 1 pm in diameter, but in any case ⁇ 2 pm comparatively small and the islands are advantageously evenly distributed over the strip thickness. The small size of the islands and the homogeneous
  • Distribution of the second main component contribute significantly to achieving the high hole expansion ratio.
  • the proportion of the carbon-rich second main constituent embedded in the matrix in the matrix firstly sets the yield strength in said region and secondly the bake hardening potential.
  • the mechanism is that with the formation of the metastable structural constituents martensite, retained austenite and bainite, a large number of dislocations are produced which produce a low yield strength.
  • dissolved carbon diffuses from the metastable microstructure constituents martensite, retained austenite and bainite into the previously formed dislocations and causes the known increase in strength. Since no dissolved carbon is available in the pearlite, the carbon-rich constituent embedded in the matrix in the matrix contains at least one of the metastable microstructural constituents martensite,
  • the hot-rolled flat steel product according to the invention can be provided with a metallic or non-metallic coating and is particularly suitable for the production of components for vehicle construction in the automotive industry but also applications in the field of shipbuilding, plant construction, infrastructure construction, aerospace and domestic appliance technology are conceivable.
  • the steel has a tensile strength Rm of 760 to 960 MPa, a yield strength Rp0.2 of 660 to 820 MPa, a breaking elongation A80 of more than 10%, preferably more than 12%, along the rolling direction
  • Alloying elements are usually added to the steel in order to specifically influence certain properties.
  • An alloying element in different steels can influence different properties. The effect and interaction generally depends strongly on the amount, the presence of other alloying elements and the dissolution state in the material.
  • Carbon C is required to form carbides, especially in connection with the so-called micro-alloying elements Nb, V and Ti, promotes the formation of martensite and bainite, stabilizes the austenite and generally increases the strength. Higher contents of C deteriorate the welding properties and lead to the deterioration of the elongation and toughness properties, therefore a maximum content of less than 0.12 wt.%, Advantageously less than 0.08 wt.%, Is established. In order to achieve sufficient strength of the material, a minimum addition of 0.04 wt .-% is required.
  • Manganese Mn Stabilizes austenite, increases strength and toughness, and increases the temperature window for hot rolling below the recrystallization stop temperature. Higher contents of> 2.5% by weight of Mn increase the risk of medium segregations, which significantly increases the ductility and thus the product quality to decrease. Lower contents ⁇ 1, 0 wt .-% do not allow the achievement of the required strength and toughness at the desired moderate analysis costs.
  • Aluminum Al Used for deoxidation in the steelworks process. The amount of AI used depends on the process. Therefore, no minimum Al content is indicated. An Al content of greater than 0.1 wt .-% deteriorates the casting behavior in continuous casting significantly. This results in a higher cost when casting.
  • Silicon Si One of the elements that enables the increase in strength of steel by solid solution hardening in a cost-effective manner.
  • Si reduces the surface quality of the hot strip by the promotion of firmly adhering scale on the reheated slabs, which can be removed only at great expense or insufficiently at high Si levels. This is particularly disadvantageous in the subsequent galvanizing. Therefore, the Si content is limited to max. 0.8% limited, favorably to 0.4%. If Si is largely dispensed with on account of the surface issue, a lower limit of 0.03 is to be regarded as meaningful, since with further reduction of the Si content, comparatively high process costs occur on the steelwork side.
  • Chromium Cr Improves strength and reduces corrosion rate, retards ferrite and pearlite formation and forms carbides.
  • the maximum content is set at less than 0.6% by weight because higher contents result in deterioration of ductility.
  • Molybdenum Mo Increases the hardenability or reduces the critical cooling rate, thus promoting the formation of fine, bainitic structures. In addition, even the use of small amounts of Mo delays the coarsening of fine precipitates, which should be made as fine as possible to increase the strength of micro-alloyed structures.
  • Nickel Ni The use of even small amounts of Ni promotes ductility while maintaining strength. Due to the comparatively high cost of the content of Ni + Mo is limited to 0.5 wt .-%.
  • Phosphorus P is a trace element from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphorus increases hardness by solid solution strengthening and improves hardenability. However, it is usually tried to
  • Sulfur S Like phosphorus, it is bound as a trace element in iron ore. It is generally undesirable in steel because it leads to undesirable inclusions of MnS, thereby degrading the elongation and toughness properties. It is therefore an attempt to achieve the lowest possible amounts of sulfur in the melt and possibly to convert the elongated inclusions by a so-called Ca- treatment in a more favorable geometric shape. For the above reasons, the sulfur content is limited to less than 0.01 wt .-%.
  • Nitrogen N Is also an accompanying element of steelmaking. Steels with free nitrogen tend to have a strong aging effect. The nitrogen diffuses at low temperatures at dislocations and blocks them. It causes an increase in strength combined with a rapid loss of toughness. Curing of the nitrogen in the form of nitrides is possible, for example, by alloying aluminum, niobium or titanium. In the episode stand the mentioned
  • the nitrogen content is limited to less than 0.01 wt .-%.
  • Micro-alloying elements are usually added only in very small amounts ( ⁇ 0.2 wt .-% per element). They act in contrast to the alloying elements mainly by precipitation formation but can also affect the properties in a dissolved state. Despite the small quantity additions, micro-alloying elements influence the targeted ones Production conditions and the processing and final properties of the product.
  • Typical micro-alloying elements are, for example, niobium and titanium. These elements can be dissolved in the iron grid and form carbides, nitrides and carbonitrides with carbon and nitrogen.
  • Niobium Nb The alloying of niobium is particularly effective through the formation of
  • Carbides are grain-refining, which simultaneously improves the strength, toughness and elongation properties. At contents of more than 0.08% by weight, a saturation behavior sets in, which is why a maximum content of less than or equal to 0.08% by weight is provided.
  • Titanium Ti Grain-refining as a carbide former, which simultaneously improves strength, toughness and elongation properties. Contents of Ti exceeding 0.2 wt% deteriorate the ductility and the hole expanding ability by forming very coarse, primary TiN precipitates, therefore, a maximum content of 0.2 wt% is set.
  • a method according to the invention for the production of the above-described hot-rolled flat steel product according to the invention comprises the steps:
  • Ni + Mo up to 0.5
  • Annealing time of at least 1 s, preferably 5 s-40 s, and an average cooling rate between annealing temperature and 500 ° C. of 0.1 K / min to 150 K / s, preferably 5 K / s to 20 K / s,
  • ferritic-bainitic, microalloyed hot-rolled strip substantially retains the mechanical properties, although it is not annealed at temperatures below Ac1 but at Ac1 ⁇ T ⁇ Ac1 + 100 ° C., as usual.
  • the temperature Ac1 describes the beginning of the transformation of the microstructure into austenite with slow heating in accordance with relevant standards.
  • Ac1 is usually determined by dilatometric measurements. According to the invention, it has been recognized that the homogeneity of the ferritic-bainitic microstructure is largely retained with an annealing of T ⁇ Ac.sub.1, and thus, in particular, the comparatively high level of the hole widening ratio is maintained for mainly bainitic structures.
  • a BH2 value of> 30% can not be achieved and a pronounced upper yield strength of ReH> 820 MPa is formed, which is often regarded as problematic for the user.
  • the cause is the blocking of dislocations due to diffusion of atomically dissolved carbon during annealing at T ⁇ Ac1 or galvanizing at T> 400 ° C.
  • Hole expansion ratio of> 30%, as well as a BH2 value of> 30 MPa can be achieved in combination.
  • a reeling temperature HT of less than 650 ° C. advantageously in the range of 450 ° C. to 600 ° C., since the set predominantly bainitic structure has a high number of nucleation sites for the transformation into austenite at T> Ac1 and thus allows the island diameter of the stored second phase an average value of ⁇ 1 pm.
  • Below 450 ° C is with a comparatively high proportion of
  • Martensite which is disadvantageous after the heat treatment in terms of ductility and Lochetzweiteabmögens due to the internal structure.
  • the hot rolling end temperature in this steel according to the invention is between 950 ° C and Ar1 + 50 K, where Ar1 describes the beginning of the conversion of austenite into the ferrite during cooling.
  • Typical thickness ranges for slabs and thin slabs are between 35 mm to 450 mm. It is envisaged that the slab or thin slab to a
  • the hot strip is after the hot rolling according to the invention at a reel temperature of preferably 450 ° C to 650 ° C reeled.
  • a reel temperature of preferably 450 ° C to 650 ° C reeled.
  • this is hot rolled
  • a heat treatment according to the invention in the temperature range Ac1 ⁇ T ⁇ Ac1 subjected to a flat steel product in the temperature range + 100 ° C and held usually in this temperature range for 10 seconds to 10 minutes, possibly up to 48h, with higher temperatures being associated with shorter treatment times and vice versa.
  • the annealing is usually in a continuous annealing (shorter annealing times), but can also be done for example in a Haubenglühe (longer annealing times).
  • the flat steel product is hot-dip or electrolytically galvanized or metallic, inorganic or organic coated.
  • the annealing is preferably carried out in one of
  • Hot dip coating system upstream continuous annealing.
  • Flat steel product has a tensile strength Rm of the flat steel product of 760 to 960 MPa and an elongation at break A80 of more than 10%, preferably more than 12%. In this case, high strengths and small sheet thicknesses tend to be associated with lower elongations at break and vice versa.
  • Table 2 shows the results for an annealing of the hot strip according to the invention at Ac1 ⁇ T ⁇ Ac1 + 100 ° C. (invention) in comparison to annealing below an Ac1 annealing temperature (comparison) in a radiant tube furnace (RTF).
  • inventive annealing all required characteristics are achieved safely.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

L'invention concerne un produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée et, simultanément, d'une capacité de durcissement à la cuisson élevée, composé d'un acier doté d'une limite d'élasticité Rp0,2 de 660 à 820 MPa, d'une valeur BH2 supérieure à 30 MPa et d'un rapport d'élargissement de trou supérieur à 30 %, ainsi que d'une structure constituée de deux constituants principaux, un premier constituant principal de la structure étant présent dans une proportion d'au moins 50 %, constituée d'un ou de plusieurs constituants individuels parmi la ferrite, la bainite revenue et la martensite revenue, dotés respectivement de moins de 5 % de carbures, et un second constituant principal de la structure étant présent dans une proportion de 5 % à 50 %, constituée d'un ou de plusieurs constituants individuels parmi la martensite, l'austénite résiduelle, la bainite ou la perlite, doté de la composition chimique suivante de l'acier (en % en poids) : C : 0,04 à 0,12 ; Si : 0,03 à 0,8 ; Mn : 1 à 2,5 ; P : max. 0,08 ; S : max. 0,01 ; N : max. 0,01 ; AI : jusqu'à 0,1 ; Ni + Mo : jusqu'à 0,5 ; Nb : jusqu'à 0,08 ; Ti : jusqu'à 0,2 ; Nb + Ti : min. 0,03 ; Cr : jusqu'à 0,6 ; le reste étant du fer, y compris des éléments concomitants à l'acier inévitables. En outre, l'invention concerne un procédé de fabrication d'un tel produit plat en acier.
EP18825919.6A 2017-12-15 2018-12-11 Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée et procédé de fabrication d'un tel produit plat en acier Active EP3724359B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102017130237.9A DE102017130237A1 (de) 2017-12-15 2017-12-15 Hochfestes, warmgewalztes Stahlflachprodukt mit hohem Kantenrisswiderstand und gleichzeitig hohem Bake-Hardening Potential, ein Verfahren zur Herstellung eines solchen Stahlflachprodukts
PCT/EP2018/084406 WO2019115551A1 (fr) 2017-12-15 2018-12-11 Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée, procédé de fabrication d'un tel produit plat en acier

Publications (2)

Publication Number Publication Date
EP3724359A1 true EP3724359A1 (fr) 2020-10-21
EP3724359B1 EP3724359B1 (fr) 2021-12-01

Family

ID=64870429

Family Applications (1)

Application Number Title Priority Date Filing Date
EP18825919.6A Active EP3724359B1 (fr) 2017-12-15 2018-12-11 Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée et procédé de fabrication d'un tel produit plat en acier

Country Status (7)

Country Link
US (1) US11584971B2 (fr)
EP (1) EP3724359B1 (fr)
KR (1) KR102447567B1 (fr)
CN (1) CN111373060B (fr)
DE (1) DE102017130237A1 (fr)
RU (1) RU2743041C1 (fr)
WO (1) WO2019115551A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102021104584A1 (de) * 2021-02-25 2022-08-25 Salzgitter Flachstahl Gmbh Hochfestes, warmgewalztes Stahlflachprodukt mit hoher lokaler Kaltumformbarkeit sowie ein Verfahren zur Herstellung eines solchen Stahlflachprodukts
DE102021108448A1 (de) 2021-04-01 2022-10-06 Salzgitter Flachstahl Gmbh Stahlband aus einem hochfesten Mehrphasenstahl und Verfahren zur Herstellung eines derartigen Stahlbandes
CN113667894B (zh) * 2021-08-13 2022-07-15 北京首钢冷轧薄板有限公司 一种具有优良扩孔性能800MPa级双相钢及其制备方法
DE102022125128A1 (de) 2022-09-29 2024-04-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes aus einem hochfesten Mehrphasenstahl und entsprechendes Stahlband

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5332453A (en) * 1992-03-06 1994-07-26 Kawasaki Steel Corporation High tensile steel sheet having excellent stretch flanging formability
KR100498214B1 (ko) * 1997-09-11 2005-07-01 제이에프이 스틸 가부시키가이샤 초미세 입자를 함유하는 가공용 열간 압연 강판과 이의 제조방법, 및 냉간 압연 강판의 제조 방법
WO2001053554A1 (fr) * 2000-01-24 2001-07-26 Nkk Corporation Tole d'acier zingue par immersion a chaud et procede de production correspondant
JP4062118B2 (ja) * 2002-03-22 2008-03-19 Ｊｆｅスチール株式会社 伸び特性および伸びフランジ特性に優れた高張力熱延鋼板とその製造方法
FR2849864B1 (fr) 2003-01-15 2005-02-18 Usinor Acier lamine a chaud a tres haute resistance et procede de fabrication de bandes
US7981224B2 (en) * 2003-12-18 2011-07-19 Nippon Steel Corporation Multi-phase steel sheet excellent in hole expandability and method of producing the same
JP4445365B2 (ja) * 2004-10-06 2010-04-07 新日本製鐵株式会社 伸びと穴拡げ性に優れた高強度薄鋼板の製造方法
US8337643B2 (en) * 2004-11-24 2012-12-25 Nucor Corporation Hot rolled dual phase steel sheet
JP5709151B2 (ja) * 2009-03-10 2015-04-30 Ｊｆｅスチール株式会社 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP5333298B2 (ja) * 2010-03-09 2013-11-06 Ｊｆｅスチール株式会社 高強度鋼板の製造方法
DE102011000089A1 (de) 2011-01-11 2012-07-12 Thyssenkrupp Steel Europe Ag Verfahren zum Herstellen eines warmgewalzten Stahlflachprodukts
EP2524970A1 (fr) * 2011-05-18 2012-11-21 ThyssenKrupp Steel Europe AG Produit plat en acier hautement résistant et son procédé de fabrication
DE102012002079B4 (de) 2012-01-30 2015-05-13 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines kalt- oder warmgewalzten Stahlbandes aus einem höchstfesten Mehrphasenstahl
JP6374864B2 (ja) * 2012-06-05 2018-08-15 ティッセンクルップ スチール ヨーロッパ アーゲーＴｈｙｓｓｅｎｋｒｕｐｐ Ｓｔｅｅｌ Ｅｕｒｏｐｅ Ａｇ 鋼、平鋼材及び平鋼材の製造方法
DE102014017275A1 (de) * 2014-11-18 2016-05-19 Salzgitter Flachstahl Gmbh Hochfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
US20180209011A1 (en) * 2015-07-17 2018-07-26 Salzgitter Flachstahl Gmbh Method of producing a hot strip of a bainitic multi-phase steel having a zn-mg-al coating, and a corresponding hot strip
CN106591696B (zh) * 2016-10-31 2018-03-06 首钢总公司 一种翻边性能优良的热轧钢及其生产方法

Also Published As

Publication number Publication date
DE102017130237A1 (de) 2019-06-19
KR102447567B1 (ko) 2022-09-26
CN111373060A (zh) 2020-07-03
WO2019115551A1 (fr) 2019-06-20
KR20200096810A (ko) 2020-08-13
US11584971B2 (en) 2023-02-21
CN111373060B (zh) 2022-07-12
RU2743041C1 (ru) 2021-02-12
EP3724359B1 (fr) 2021-12-01
US20200399727A1 (en) 2020-12-24

Similar Documents

Publication Publication Date Title
EP3504349B1 (fr) Procédé de fabrication d'une bande d'acier à résistance très élevée présentant des propriétés améliorées lors du traitement ultérieur et une telle bande d'acier
EP2836614B1 (fr) Acier polyphasé à haute résistance et procédé de fabrication d'une bande à partir dudit acier
EP3221484B1 (fr) Procédé de production d'une bande en acier polyphasé, durcissant à l'air, ayant une haute résistance et ayant d'excellentes propriétés de mise en oeuvre
EP3535431B1 (fr) Produit d'acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication
WO2013182621A1 (fr) Acier, produit en acier plat et procédé de fabrication d'un produit en acier plat
WO2017009192A1 (fr) Acier multiphase à haute résistance et procédé de fabrication d'une bande d'acier laminée à froid composée dudit acier
EP3027784A2 (fr) Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier
EP3332046B1 (fr) Acier au manganèse à haute résistance contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci
EP3724359B1 (fr) Produit plat en acier laminé à chaud, à rigidité élevée, doté d'une résistance à la fissuration de bords élevée ainsi que d'une capacité de durcissement à la cuisson élevée et procédé de fabrication d'un tel produit plat en acier
DE102015112889A1 (de) Hochfester manganhaltiger Stahl, Verwendung des Stahls für flexibel gewalzte Stahlflachprodukte und Herstellverfahren nebst Stahlflachprodukt hierzu
EP3692178B1 (fr) Procede de fabrication d'une bande d'acier a partir d'un acier multiphase a tres haute resistance
DE102018132860A1 (de) Verfahren zur Herstellung von konventionell warmgewalzten, profilierten Warmbanderzeugnissen
EP0796928A1 (fr) Acier à plusieurs phases et procédé pour sa fabrication
EP3221483A1 (fr) Acier polyphasé, trempé à l'air et à haute résistance, ayant d'excellentes propriétés de mise en oeuvre et procédé de production d'une bande avec cet acier
EP3512968B1 (fr) Procédé pour fabriquer un produit plat en acier à partir d'un acier au manganèse et produit plat en acier résultant
EP3924526A1 (fr) Procédé de fabrication de produits de type feuillard à chaud obtenus par voie thermomécanique
EP3551776A1 (fr) Procédé de fabrication d'une bande laminée à chaud ou à froid et/ou d'un produit plat en acier laminé de manière flexible constitué par un acier contenant du manganèse, hautement solide et produit plat en acier ainsi obtenu
EP3469108B1 (fr) Procédé de fabrication d'une bande d'acier laminée à froid présentant des propriétés trip à partir d'un acier à résistance élevée contenant du manganèse
DE102018132901A1 (de) Verfahren zur Herstellung von konventionell warmgewalzten Warmbanderzeugnissen
DE102018132816A1 (de) Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: UNKNOWN

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20200703

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 8/02 20060101AFI20210709BHEP

Ipc: C22C 38/02 20060101ALI20210709BHEP

Ipc: C22C 38/04 20060101ALI20210709BHEP

Ipc: C22C 38/12 20060101ALI20210709BHEP

Ipc: C22C 38/14 20060101ALI20210709BHEP

Ipc: C21D 6/00 20060101ALI20210709BHEP

Ipc: C23C 2/02 20060101ALI20210709BHEP

Ipc: C23C 2/06 20060101ALI20210709BHEP

Ipc: C23C 2/40 20060101ALI20210709BHEP

INTG Intention to grant announced

Effective date: 20210729

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1451812

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211215

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502018008079

Country of ref document: DE

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20211201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220301

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220301

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220302

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220401

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502018008079

Country of ref document: DE

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220401

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211211

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211211

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

26N No opposition filed

Effective date: 20220902

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230513

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20181211

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20221211

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221211

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20231222

Year of fee payment: 6

Ref country code: DE

Payment date: 20231214

Year of fee payment: 6

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211201