EP4263882B1 - Tôle d'acier revêtue, pièce en acier trempé sous presse à haute résistance et leur procédé de fabrication - Google Patents

Tôle d'acier revêtue, pièce en acier trempé sous presse à haute résistance et leur procédé de fabrication

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Publication number
EP4263882B1
EP4263882B1 EP21819985.9A EP21819985A EP4263882B1 EP 4263882 B1 EP4263882 B1 EP 4263882B1 EP 21819985 A EP21819985 A EP 21819985A EP 4263882 B1 EP4263882 B1 EP 4263882B1
Authority
EP
European Patent Office
Prior art keywords
steel sheet
steel
layer
bulk
temperature
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.)
Active
Application number
EP21819985.9A
Other languages
German (de)
English (en)
Other versions
EP4263882A1 (fr
Inventor
Clément PHILIPPOT
Sandra LE GUILLARD
David DUSSAUSSOIS
Matthieu SALIB
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.)
ArcelorMittal SA
Original Assignee
ArcelorMittal SA
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 ArcelorMittal SA filed Critical ArcelorMittal SA
Priority to EP25197585.0A priority Critical patent/EP4628621A3/fr
Priority to MA62604A priority patent/MA62604B1/fr
Publication of EP4263882A1 publication Critical patent/EP4263882A1/fr
Application granted granted Critical
Publication of EP4263882B1 publication Critical patent/EP4263882B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/02—Winding-up or coiling
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment 
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0436—Cold 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/02—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
    • C22C38/12—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • 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
    • C23C2/12—Aluminium 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
    • C23C2/26—After-treatment
    • 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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • 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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • 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
    • 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
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • 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

Definitions

  • the present invention relates to coated steel sheets and to high strength press hardened steel parts having good bendability properties.
  • High strength press-hardened parts can be used as structural elements in automotive vehicles for anti-intrusion or energy absorption functions. In such type of applications, it is desirable to produce steel parts that combine high mechanical strength, high impact resistance and good corrosion resistance. Moreover, one of major challenges in the automotive industry is to decrease the weight of vehicles in order to improve their fuel efficiency in view of the global environmental conservation, without neglecting the safety requirements.
  • the publication WO2016104881 relates to a hot press forming part used as a structural part of a vehicle or the like, requiring impact resistance characteristics, and more particularly, having a tensile strength of 1300 MPa or greater and a method for manufacturing the same by heating a steel material to a temperature at which an austenite single phase may be formed, and quenching and hot forming thereof using a mold.
  • the base steel sheet comprises a thin ferrite layer lower than 50 ⁇ m at the surface, and the carbides size and density should be controlled. This ferrite layer in the substrate allow to inhibit the propagation of the fine cracks formed on the plating layer to the base but leads to a low bendability with bending angle lower than 70°.
  • the publication WO2018179839 relates to a hot-pressed part obtained by hot pressing a steel sheet having a microstructure changing in the thickness direction, with a soft layer made of at least 90% of ferrite, a transition layer made of ferrite and martensite and a hard layer mainly martensitic and has both high strength and high bendability.
  • the cold rolled steel sheet is annealed in an atmosphere with a dew point temperature comprises from 50°C to 90°C, which could be harmful to aluminium alloy coating.
  • US2017/260599A1 and WO2018/220540A1 is described in US2017/260599A1 and WO2018/220540A1 .
  • the purpose of the invention therefore is to solve the above-mentioned problem and to provide a press hardened steel part having a combination of high mechanical properties with the tensile strength TS above or equal to 1500 MPa and bending angle higher than 70°.
  • the the press hardened steel part according to the invention has yield strength YS above or equal to 1250 MPa.
  • Another purpose of the invention is to obtain a coated steel sheet that can be transformed by hot forming into such a press hardened steel part.
  • the object of the present invention is achieved by providing a steel sheet according to claim 1. Another object is achieved by providing the method according to claim 2. Another object of the present invention is achieved by providing a press hardened steel part according to claim 3. The steel part can also comprise characteristics of claim 4. Another object is achieved by providing the method according to claim 5.
  • composition of the steel according to the invention will now be described, the content being expressed in weight percent.
  • the carbon content is comprised from 0.26% to 0.40 % to ensure a satisfactory strength. Above 0.40% of carbon, weldability and bendability of the steel sheet may be reduced. If the carbon content is lower than 0.26%, the tensile strength will not reach the targeted value.
  • the aluminium content is comprised from 0.01% and 0.1% as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration. Aluminium can protect boron if titanium content is not enough.
  • the aluminium content is lower than 0.1% to avoid oxidation problems and ferrite formation during press hardening. Preferably the aluminium content is comprised from 0.01% to 0.05%.
  • the chromium content is comprised from 0.1% to 1.0 %. Chromium is an element participating in the hardening in solid solution and must be higher than 0.1%. The chromium content is below 1.0% to limit processability issues and cost.
  • the titanium content is comprised from 0.01% to 0.1% in order to protect boron from formation of BN. Titanium content is limited to 0.1% to avoid TiN formation.
  • the boron content is comprised from 0.001% to 0.004%. Boron improves the hardenability of the steel.
  • the boron content is not higher than 0.004% to avoid a risk of breaking the slab during continuous casting.
  • the bulk of the coated steel sheet (2) has a microstructure comprising, in surface fraction, from 60% to 90% of ferrite, the rest being martensite-austenite islands, pearlite or bainite.
  • the decarburized layer present on top of the bulk is obtained during the annealing of the cold rolled steel sheet thanks to the control of the atmosphere in the furnace to set a dew point temperature strictly higher than -10°C and below or equal to 20°C.
  • the hot-rolled steel is then cooled and coiled at a temperature T coil lower than 670°C, and optionally pickled to remove oxidation.
  • the coiled steel sheet is then cold rolled to obtain a cold rolled steel sheet.
  • the cold-rolling reduction ratio is preferably comprised from 20% to 80%. Below 20%, the recrystallization during subsequent heat-treatment is not favored, which may impair the ductility of the steel sheet. Above 80%, there is a risk of edge cracking during cold-rolling.
  • the steel sheet is then annealed in an HNx atmosphere with from 0% to 15% of H2, to an annealing temperature T A comprised from 700°C to 850°C and maintained at said annealing temperature T A for a holding time t A comprised from 10s to 1200s, in order to obtain an annealed steel sheet.
  • a holding time t A comprised from 10s to 1200s, in order to obtain an annealed steel sheet.
  • the holding time t A is above or equal to 10 s to allow the ferrite layer to form, and below or equal to 1200s in order to limit the thickness of this ferrite layer.
  • the atmosphere in the furnace is controlled to have a dew point temperature T DP1 strictly higher than -10°C and below or equal to +20°C in order to form a decarburized layer according to the invention. If T DP1 is below or equal to -10°C, the formation of the decarburized layer is slowed down and the ferrite layer is not formed in its upper part. The bendability of the steel part will be too low.
  • the steel sheet is then coated with an aluminium alloy coating.
  • a section of the press hardened steel part is schematically represented on Fig 3b and Fig 4b .
  • the steel part comprises successively from the bulk to the surface of the steel part:
  • all microstructural elements of the bulk are transformed into austenite, and the ferrite of the decarburized layer is transformed into austenite with wider grain size than the austenite of the bulk.
  • the steel part is then die-quenched.
  • the interdiffusion layer grows from the former wide grain size austenite layer, thus having larger grain width than prior austenitic grain size in the bulk.
  • the ratio between the ferritic grain width in the interdiffusion layer GW int over prior austenite grain size in the bulk PAGS bulk satisfies following equation: GW int / PAGS bulk ⁇ 1 ⁇ 30 % in order to improve bendability of the steel sheet, without deteriorating mechanical properties.
  • the ferritic grain width is the average distance between two parallel grain boundaries of the interdiffusion layer, grain boundaries being oriented in the direction of the thickness of the sheet.
  • the combination of annealing temperature T A , annealing time t A and dew point temperature T DP1 according to the invention promotes the formation of large grain width GW int in the interdiffusion layer.
  • the thermal treatment of the steel blank before the press forming rules the austenitic grain growth and so the PAGS in the bulk.
  • the press hardened steel part may further comprise a martensite layer with a carbon gradient between the bulk and the interdiffusion layer, as represented by (8) in Fig 4b .
  • a martensite layer with a carbon gradient between the bulk and the interdiffusion layer, as represented by (8) in Fig 4b .
  • carbon diffuses from the bulk to the surface.
  • the ferrite upper part of the decarburized layer is then transformed in a layer of austenite with a gradient of carbon.
  • this layer of austenite with a gradient of carbon is transformed in a layer of martensite with a carbon gradient.
  • the press hardened steel part according to the invention has a tensile strength TS above or equal to 1500 MPa and a bending angle higher than 70°.
  • the bending angle has been determined on press hardened parts according to the method VDA238-100 bending Standard (with normalizing to a thickness of 1.5 mm).
  • the yield strength YS is above or equal to 1250 MPa.
  • TS and YS are measured according to ISO standard ISO 6892-1.
  • the press hardened steel part according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the following steps: A coated steel sheet according to the invention is cut to a predetermined shape to obtain a steel blank. The steel blank is then heated to a temperature comprised from 880°C to 950°C during 10s to 900s to obtain a heated steel blank.
  • Figure 3a represents a schematic section of the coated steel sheet of trial 2.
  • the combination of process parameters of the invention, annealing temperature T A , annealing time t A and dew point temperature T DP1 allow to obtain a decarburized layer (3), in which a layer of ferrite is formed in the upper part (4).
  • Fig 3b represents a schematic section of the press hardened steel part of trial 2.
  • the grain width of ferrite formed in the interdiffusion layer (5) is a heritage of the pure ferrite layer in which austenite formation takes place during heating, with larger grain size.
  • the interdiffusion layer grows on this large austenite grain size.
  • the grain width of ferrite in the interdiffusion layer (6) is then larger than prior austenite grain size in the bulk (7), leading to good bendability with bending angle higher than 70°.
  • Figure 4a represents a schematic section of the coated steel sheet of trial 1.
  • the combination of process parameters of the invention, annealing temperature T A , annealing time t A and dew point temperature T DP1 allow to obtain a decarburized layer (3), in which a layer of ferrite is formed in the upper part (4), thicker than in trial 1 due to the higher C content.
  • Fig 4b represents a schematic section of the press hardened steel part of trial 1.
  • the grain width of ferrite formed in the interdiffusion layer (6) is a heritage of the pure ferrite layer in which austenite formation takes place during heating, with larger grain size.
  • the interdiffusion layer grows on this large austenite grain size .
  • the grain width of ferrite in the interdiffusion layer (6) is then larger than prior austenite grain size in the bulk (7), leading to good bendability with bending angle higher than 70°.
  • a layer of martensite with a carbon gradient is formed between the bulk and the interdiffusion layer in the press hardened steel part, leading to tensile strength higher than 1500 MPa.
  • the coated steel sheet has a decarburized layer, without ferrite layer in its upper part, as represented schematically in Fig 2a .
  • the absence of ferrite layer is due to the low dew point temperature T DP1 of -10°C, which slow down the kinetics of the decarburization.
  • Figure 2b represents a schematic section of the press hardened steel part from trial 3. Due to the absence of the ferrite layer, the ferritic grain width in the interdiffusion layer (6) is then equivalent to prior austenite grain size in the bulk (7), leading to a low bending angle below 70°.
  • the low dew point temperature T DP1 of -40°C implies an absence of the decarburized layer and ferrite layer in the coated steel sheet.
  • Fig 1a represents a schematic section of the coated steel sheet of this trial, with the coating layer (1) and the bulk (2).
  • Figure 1b represents a schematic section of the press hardened steel part from trial 4. Due to the absence of the ferrite layer, the ferritic grain width in the interdiffusion layer (6) is then equivalent to prior austenite grain size in the bulk (7), leading to a low bending angle below 70°.
  • Fig 5a represents a schematic section of the coated steel sheet of trial 5, with the coating layer (1) the decarburized layer (3), the thicker ferrite layer (4) with coarser grain size, and the bulk (2).
  • Fig 5b represents a schematic section of the press hardened steel part from trial 5.
  • the microstructure of the bulk is austenitic, and the thick ferrite layer is transformed in a layer of austenite with gradient of carbon. But due to the thickness of the ferrite layer higher than 100 ⁇ m, a layer of ferrite remains present between the interdiffusion layer and the layer of austenite with gradient of carbon.
  • the ferrite layer is still present and the layer of austenite with carbon gradient transforms into a martensite layer with gradient of carbon, leading to a multi-phased layer. This triggers a decrease of yield strength.
  • the steel sheet has a low carbon level of 0.21%. This low carbon content combined to the process parameters, leads to a decarburized layer in the coated steel sheet with the ferrite layer. Nevertheless, the yield strength and tensile strength of the press hardened steel part are not achieved because of the low level of carbon.

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Claims (5)

  1. Tôle d'acier revêtue constituée d'un acier ayant une composition comprenant, en pourcentage en poids :
    C : 0,26-0,40 %
    Mn : 0,5-1,8 %
    Si : 0,1-1,25 %
    AI : 0,01-0,1 %
    Cr : 0,1-1,0 %
    Ti : 0,01-0,1 %
    B : 0,001-0,004 % P ≤ 0 , 020 % , S ≤ 0 , 010 % N ≤ 0 , 010 % ,
    et comprenant éventuellement un ou plusieurs des éléments suivants, en pourcentage en poids : Ni ≤ 0 , 5 % Mo ≤ 0 , 40 % Nb ≤ 0 , 08 % Ca ≤ 0 , 1 %
    le reste de la composition étant du fer et des impuretés inévitables résultant de la fusion,
    ladite tôle d'acier revêtue comprenant de la masse à la surface de la tôle d'acier revêtue :
    - une masse avec une microstructure comprenant, en fraction de surface, de 60 % à 90 % de ferrite, le reste étant des îlots de martensite-austénite, de la perlite ou de la bainite,
    - une telle masse étant surmontée par une couche décarburée comprenant dans la partie supérieure une couche de ferrite ayant une épaisseur de 1 µm à 100 µm
    - une couche de revêtement constituée d'aluminium ou d'alliage d'aluminium.
  2. Procédé de production d'une tôle d'acier revêtue selon la revendication 1, ledit procédé comprenant les étapes successives suivantes :
    - coulage d'un acier pour obtenir une brame, ledit acier ayant une composition selon la revendication 1,
    - réchauffage de la brame à une température Tréchauffage comprise entre 1100 °C et 1300 °C,
    - laminage à chaud de la brame réchauffée à une température de laminage à chaud de finition comprise entre 800 °C et 950 °C
    - enroulement de la tôle d'acier laminée à chaud à une température d'enroulement Tenroulement inférieure à 670 °C pour obtenir une tôle d'acier enroulée,
    - décapage chimique éventuel de la tôle d'acier enroulée,
    - laminage à froid de la tôle d'acier enroulée pour obtenir une tôle d'acier laminée à froid
    - chauffage de la tôle d'acier laminée à froid à une température de recuit TA comprise entre 700 °C et 850 °C et maintien de la tôle d'acier à ladite température TA pendant un temps de maintien tA compris entre 10 s et 1200 s, pour obtenir une tôle d'acier recuite, l'atmosphère comprenant de 0 % à 15 % de H2 et ayant un point de rosée TDP1 strictement supérieur à -10 °C et inférieur ou égal à +20 °C
    - refroidissement de ladite tôle d'acier recuite à une plage de températures de 560 °C à 700 °C,
    - revêtement de la tôle d'acier recuite avec de l'aluminium ou avec un revêtement d'alliage d'aluminium
    - refroidissement de la tôle d'acier revêtue à température ambiante pour obtenir une tôle d'acier ayant une microstructure selon la revendication 1.
  3. Pièce en acier trempé sous presse, la pièce en acier ayant une composition comprenant, en pourcentage en poids :
    C : 0,26-0,40 %
    Mn : 0,5-1,8 %
    Si : 0,1-1,25 %
    Al : 0,01-0,1 %
    Cr : 0,1-1,0 %
    Ti : 0,01-0,1 %
    B : 0,001-0,004 % P ≤ 0 , 020 % , S ≤ 0 , 010 % N ≤ 0 , 010 %
    et comprenant éventuellement un ou plusieurs des éléments suivants, en pourcentage en poids : Ni ≤ 0 , 5 % Mo ≤ 0 , 40 % Nb ≤ 0 , 08 % Ca ≤ 0 , 1 %
    le reste de la composition étant du fer et des impuretés inévitables résultant de la fusion,
    ladite pièce d'acier comprenant successivement de la masse à la surface de la pièce d'acier :
    - une masse ayant une microstructure comprenant, en fraction de surface, plus de 95 % de martensite et moins de 5 % de bainite,
    - une couche d'interdiffusion ferritique,
    - une couche de revêtement à base d'aluminium,
    dans laquelle le rapport entre la largeur de grain ferritique dans ladite couche d'interdiffusion GWint à la taille de grain d'austénite antérieure dans la masse PAGSmasse satisfait l'équation suivante : GW int / PAGS masse − 1 ≥ 30 %
    et ayant une résistance à la traction TS supérieure ou égale à 1500 MPa, une limite d'élasticité YS supérieure ou égale à 1250MPa et un angle de cintrage supérieur à 70°, TS et YS étant mesurés selon la norme ISO 6892-1, et l'angle de cintrage selon la norme de cintrage du procédé VDA238-100 (avec normalisation à une épaisseur de 1,5 mm).
  4. Pièce en acier trempé sous presse selon la revendication 3, dans laquelle la pièce en acier trempé sous presse comprend une couche de martensite avec un gradient de carbone entre ladite masse et ladite couche d'interdiffusion ferritique.
  5. Processus de fabrication d'une pièce en acier trempé sous presse selon l'une quelconque des revendications 3 à 4, comprenant les étapes successives suivantes :
    - fourniture d'une tôle d'acier selon la revendication 1, ou produite au moyen d'un procédé selon la revendication 2,
    - découpe de ladite tôle d'acier selon une forme prédéterminée, de sorte à obtenir une ébauche d'acier,
    - chauffage de l'ébauche d'acier à une température comprise entre 880 °C et 950 °C pendant 10 s à 900 s pour obtenir une ébauche d'acier chauffée,
    - transfert de l'ébauche chauffée vers une presse de formage,
    - formage à chaud de l'ébauche chauffée dans la presse de formage pour obtenir une pièce formée,
    - trempe en matrice de la pièce formée.
EP21819985.9A 2020-12-16 2021-12-03 Tôle d'acier revêtue, pièce en acier trempé sous presse à haute résistance et leur procédé de fabrication Active EP4263882B1 (fr)

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PCT/IB2021/061291 WO2022130101A1 (fr) 2020-12-16 2021-12-03 Tôle d'acier revêtue, pièce en acier trempé sous presse à haute résistance et leur procédé de fabrication

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CN116219271B (zh) * 2022-07-22 2024-01-09 宝山钢铁股份有限公司 一种铝硅镀层钢板、热成形部件及其制造方法
WO2024105428A1 (fr) * 2022-11-14 2024-05-23 Arcelormittal Pièce en acier durcie à la presse à ténacité élevée et son procédé de fabrication

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WO2018220412A1 (fr) 2017-06-01 2018-12-06 Arcelormittal Procede de fabrication de pieces d'acier a haute resistance mecanique et ductilite amelioree, et pieces obtenues par ce procede
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KR102165223B1 (ko) 2018-12-19 2020-10-13 주식회사 포스코 열간성형 후 충격특성이 우수한 열간성형용 도금강판, 열간성형 부재 및 이들의 제조방법
WO2022129994A1 (fr) * 2020-12-16 2022-06-23 Arcelormittal Tôle d'acier revêtue et pièce en acier trempé à la presse à haute résistance et son procédé de fabrication

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US20240102138A1 (en) 2024-03-28
ZA202305067B (en) 2024-06-26
HUE073352T2 (hu) 2026-01-28
FI4263882T3 (fi) 2025-11-13
JP2023553672A (ja) 2023-12-25
JP2025108506A (ja) 2025-07-23
BR112023008984A2 (pt) 2024-02-06
CN116568828A (zh) 2023-08-08
PL4263882T3 (pl) 2025-12-22
WO2022130101A1 (fr) 2022-06-23
EP4628621A2 (fr) 2025-10-08
EP4263882A1 (fr) 2023-10-25
MA62604B1 (fr) 2025-10-31
CA3200721A1 (fr) 2022-06-23
KR20230100737A (ko) 2023-07-05
WO2022129995A1 (fr) 2022-06-23
ES3055855T3 (en) 2026-02-16

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