WO2024053207A1 - 熱間プレス用鋼板、熱間プレス部材、および熱間プレス部材の製造方法 - Google Patents

熱間プレス用鋼板、熱間プレス部材、および熱間プレス部材の製造方法 Download PDF

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Publication number
WO2024053207A1
WO2024053207A1 PCT/JP2023/023229 JP2023023229W WO2024053207A1 WO 2024053207 A1 WO2024053207 A1 WO 2024053207A1 JP 2023023229 W JP2023023229 W JP 2023023229W WO 2024053207 A1 WO2024053207 A1 WO 2024053207A1
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Prior art keywords
coating layer
hot
steel plate
less
content
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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.)
Ceased
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PCT/JP2023/023229
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English (en)
French (fr)
Japanese (ja)
Inventor
林太 佐藤
洋一 牧水
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 JFE Steel Corp filed Critical JFE Steel Corp
Priority to EP23862752.5A priority Critical patent/EP4541938A4/en
Priority to CN202380059570.5A priority patent/CN119731371A/zh
Priority to JP2023551265A priority patent/JP7683717B2/ja
Priority to KR1020247042929A priority patent/KR20250011698A/ko
Priority to US18/994,758 priority patent/US20260049380A1/en
Publication of WO2024053207A1 publication Critical patent/WO2024053207A1/ja
Priority to MX2025002610A priority patent/MX2025002610A/es
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/12—Electroplating: Baths therefor from solutions of nickel or cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • B32B15/015—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium the said other metal being copper or nickel or an alloy thereof
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    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
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    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • 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 
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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    • 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
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    • C22C—ALLOYS
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    • C22C19/005—Alloys based on nickel or cobalt with Manganese as the next major constituent
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    • C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
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    • C22C19/03—Alloys based on nickel or cobalt based on nickel
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    • C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
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    • 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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • 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
    • C23C2/14—Removing excess of molten coatings; Controlling or regulating the coating thickness
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
    • C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
    • C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
    • C23C28/345—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates with at least one oxide layer
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/56—Electroplating: Baths therefor from solutions of alloys
    • C25D3/562—Electroplating: Baths therefor from solutions of alloys containing more than 50% by weight of iron or nickel or cobalt
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/34—Pretreatment of metallic surfaces to be electroplated
    • C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces
    • C25D5/50—After-treatment of electroplated surfaces by heat-treatment
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D7/00—Electroplating characterised by the article coated
    • C25D7/06—Wires; Strips; Foils
    • C25D7/0614—Strips or foils
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2250/00—Layers arrangement
    • B32B2250/02—2 layers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2307/00—Properties of the layers or laminate
    • B32B2307/70—Other properties
    • B32B2307/732—Dimensional properties
    • B32B2307/737—Dimensions, e.g. volume or area
    • B32B2307/7375—Linear, e.g. length, distance or width
    • B32B2307/7376—Thickness
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2311/00—Metals, their alloys or their compounds
    • B32B2311/22—Nickel or cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2311/00—Metals, their alloys or their compounds
    • B32B2311/30—Iron, e.g. 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material

Definitions

  • the present invention relates to a hot press steel plate, a hot press member, and a method for manufacturing a hot press member.
  • complex-shaped members used in automobiles include suspension members such as chassis and structural members for skeletons such as B-pillars.
  • Hot pressing is a forming method in which a steel plate is heated to an austenite temperature range, then press-formed at a high temperature, and at the same time is rapidly cooled by contact with a mold.
  • press forming is performed in a state where the strength of the material steel plate is relatively low, and the strength is increased by subsequent rapid cooling, so that it is possible to achieve both high strength and ensuring press formability.
  • Patent Document 1 proposes a steel plate for hot pressing that suppresses oxidation of the steel plate during heating by providing an aluminum plating layer on the surface of the steel plate containing 0.15 to 0.5% carbon. There is.
  • One problem is that it has low suitability for high-speed heating.
  • Methods for heating steel sheets for hot pressing include atmospheric furnace heating, direct current heating, induction heating, etc.
  • direct current heating and induction heating are superior in energy efficiency compared to atmosphere furnace heating. Carbon emissions can be reduced.
  • the steel plate for hot pressing can be heated at high speed, so productivity is improved.
  • liquid metal embrittlement cracking Another problem is liquid metal embrittlement cracking.
  • LME liquid metal embrittlement
  • hot pressing steel sheets are generally used in a painted state after hot pressing. Therefore, the hot-pressed steel plate that is finally obtained is also required to have excellent paint adhesion.
  • the present invention has been made in view of the above circumstances, and aims to provide a hot press steel plate and a hot press member that can satisfy the following requirements (1) to (3).
  • the present invention was completed based on solving the above problems, and the gist thereof is as follows.
  • a steel plate for hot pressing comprising a coating layer with a thickness of 0.5 to 6.0 ⁇ m provided on both sides of the base steel plate, A steel sheet for hot pressing, wherein the coating layer is made of Ni or a Ni-based alloy, and the Zn content in the coating layer is 0 to 30% by mass.
  • the coating layer contains a total of 50% by mass or less of at least one selected from the group consisting of Al, Ti, V, Cr, Mn, Fe, Co, Mo, and W. steel plate for hot pressing.
  • a hot press member having a coating layer with a thickness of 0.5 to 6.0 ⁇ m provided on both sides of the base steel plate,
  • the hot press member wherein the coating layer is made of Ni or a Ni-based alloy, and the Zn content in the coating layer is 0 to 30% by mass.
  • the coating layer contains a total of 50% by mass or less of at least one selected from the group consisting of Al, Ti, V, Cr, Mn, Fe, Co, Mo, and W. hot pressed parts.
  • an oxide layer containing one or both of Mn and Fe and having a thickness of 0.1 to 5 ⁇ m 7.
  • a method for producing a hot press member comprising hot pressing the hot press steel plate according to any one of 1 to 3 above to obtain a hot press member.
  • the hot press steel sheet of the present invention has excellent suitability for high-speed heating, and even when heated at high speed by direct current heating or induction heating, variations in the thickness of the coating layer are suppressed. Further, in the hot press steel sheet of the present invention, liquid metal embrittlement cracking during hot press forming is suppressed. Furthermore, the hot-pressed member obtained by hot-pressing the hot-pressed steel plate of the present invention has excellent paint adhesion.
  • the present invention is not limited to this embodiment.
  • the unit of content "%" in the composition of the coating layer and the steel plate represents “mass %” unless otherwise specified.
  • a hot press steel plate in an embodiment of the present invention includes a base steel plate and a coating layer with a thickness of 0.5 to 6.0 ⁇ m provided on both sides of the base steel plate.
  • the coating layer is made of Ni or a Ni-based alloy, and the Zn concentration in the coating layer is 0 to 30%.
  • the coating layer may be a coating layer made of Ni (Ni coating layer) or a coating layer made of a Ni-based alloy (Ni-based alloy coating layer).
  • Ni-based alloy refers to an alloy having a Ni content of 50% or more.
  • the coating layer of the present invention has a Ni content of 50% or more.
  • the surface layer of the steel sheet is oxidized by oxygen and water vapor in the atmosphere.
  • the steel sheet for hot pressing of the present invention has a Ni-based coating layer on the surface that has a high melting point and oxidation resistance, the coating layer does not melt during heating and a thick oxide layer is formed on the surface. You can prevent this from happening. As a result, excellent paint adhesion can be obtained.
  • the Ni content in the coating layer is preferably 60% or more, more preferably 70% or more, and even more preferably 80% or more.
  • the upper limit of the Ni content in the coating layer is not particularly limited, and may be 100%.
  • the Zn content in the coating layer is 30% or less, preferably 20% or less, more preferably 10% or less, even more preferably 5% or less.
  • the lower limit of the Zn content is set to 0%.
  • the chemical conversion coating formed in the chemical conversion treatment step which is a pre-painting treatment step, becomes denser and the coating adhesion is further improved. Therefore, the Zn content in the coating layer is preferably 0.5% or more, more preferably 1% or more, and still more preferably 2% or more.
  • the coating layer may optionally contain at least one selected from the group consisting of Al, Ti, V, Cr, Mn, Fe, Co, Mo, and W in a total amount of 50% or less. Even better oxidation resistance can be obtained by adding at least one of Al, Ti, V, Cr, Mn, Co, Mo, and W. Since these elements can be added arbitrarily, the lower limit of the total content may be 0%. However, in order to strengthen the oxidation resistance of the coating layer, the coating layer preferably contains 1% or more of these elements in total. Furthermore, when the coating layer is formed by electroplating, Fe eluted from the base steel plate into the plating bath may be incorporated into the coating layer.
  • the total content of the elements is 50% or less, preferably 40% or less, more preferably 30% or less, even more preferably 20% or less.
  • the Fe content in the coating layer is preferably 20% or less, more preferably 5% or less, and even more preferably 1% or less.
  • the coating layer has, in mass %, Zn: 0-30%, At least one selected from the group consisting of Al, Ti, V, Cr, Mn, Fe, Co, Mo, and W: 0 to 50% in total, The remainder has a component composition consisting of Ni and unavoidable impurities.
  • the preferred ranges for the content of each component described above are applied.
  • the Zn content is preferably 0.5% or more, more preferably 1% or more, and even more preferably 2% or more.
  • Thickness 0.5-6.0 ⁇ m Note that when the hot-pressed steel plate is heated, Ni in the coating layer and Fe in the base steel plate interdiffuse, and a Ni-based alloy layer with an increased Fe concentration is generated in the surface layer of the hot-pressed member. If the thickness of the coating layer of a steel plate for hot pressing is less than 0.5 ⁇ m, when heated at a high temperature exceeding 1000°C, Fe that has diffused and reached the surface layer will be oxidized, resulting in a thick and brittle Fe-containing oxide layer. is formed. The presence of thick and brittle Fe-containing oxides reduces paint adhesion. Therefore, the thickness of the coating layer is set to 0.5 ⁇ m or more.
  • the thickness of the coating layer is preferably 1.0 ⁇ m or more, more preferably 2.0 ⁇ m or more, since the thicker the coating layer remains after heating, the better the corrosion resistance can be obtained.
  • the thickness of the coating layer is 6.0 ⁇ m or less, preferably 5.0 ⁇ m or less, more preferably 4.0 ⁇ m or less.
  • the steel plate for hot pressing of the present invention is provided with a coating layer on both sides thereof, the thickness of the coating layer on one side may be the same as the thickness of the coating layer on the other side, They may be different as long as the thickness of the coating layer on each surface satisfies the above conditions.
  • the base steel plate any steel plate can be used without particular limitation.
  • the base steel plate may be either a hot-rolled steel plate or a cold-rolled steel plate.
  • the base material steel plate has the following properties in mass%: C: 0.05-0.50%, Si: 0.1-1.0%, Mn: 0.5-3.0%, P: 0.1% or less, S: 0.01% or less, Contains Al: 0.10% or less, and N: 0.01% or less, It is preferable to use a steel plate having a composition in which the balance consists of Fe and unavoidable impurities. The reason why the above component composition is preferable will be explained below.
  • the C content in the base steel plate is preferably 0.05% or more, more preferably 0.10% or more.
  • the C content is preferably 0.50% or less, more preferably 0.45% or less, even more preferably 0.43% or less, and even more preferably 0.40% or less. Most preferred.
  • Si 0.1-1.0%
  • Si is an effective element for strengthening steel and obtaining good material quality.
  • the Si content is preferably 0.1% or more, more preferably 0.2% or more.
  • the Si content is preferably 1.0% or less, more preferably 0.4% or less, and even more preferably 0.3% or less.
  • Mn 0.5-3.0%
  • Mn is an element that contributes to improving the strength of steel sheets over a wide cooling rate range.
  • the Mn content is preferably 0.5% or more, more preferably 0.7% or more, and even more preferably 1.0% or more.
  • the Mn content is preferably 3.0% or less, more preferably 2.5% or less, even more preferably 2.0% or less, and 1.5% or less. Most preferred.
  • the P content is preferably 0.1% or less.
  • the lower limit of the P content is not particularly limited, but from the viewpoint of refining cost, the P content is preferably 0.01% or more.
  • S 0.01% or less S forms inclusions such as MnS, which causes deterioration of impact resistance and cracking along the metal flow of the welded part. Therefore, it is desirable to reduce the S content as much as possible, preferably 0.01% or less. Further, from the viewpoint of ensuring good stretch flangeability, the content is more preferably 0.005% or less, and even more preferably 0.001% or less. On the other hand, the lower limit of the S content is not particularly limited, but from the viewpoint of refining cost, the S content is preferably 0.0002% or more.
  • the Al content is preferably 0.10% or less, more preferably 0.07% or less, and even more preferably 0.04% or less.
  • the lower limit of the Al content is not particularly limited, but from the viewpoint of ensuring the effect as a deoxidizer, the Al content is preferably 0.01% or more.
  • the N content is preferably 0.01% or less.
  • the lower limit of the N content is not particularly limited, but from the viewpoint of refining cost, the N content is preferably 0.001% or more.
  • the composition of the base steel plate is as follows: Nb: 0.10% or less, Ti: 0.10% or less, B: 0.0002-0.010%, Cr: 0.1-0. 1.0%, and at least one selected from the group consisting of Sb: 0.003 to 0.10%.
  • Nb 0.10% or less
  • Nb is an effective element for strengthening steel, but if it is included in excess, rolling load increases. Therefore, when Nb is contained, the Nb content is set to 0.10% or less, preferably 0.06% or less, and more preferably 0.03% or less.
  • the lower limit of the Nb content is not particularly limited and may be 0%, but from the viewpoint of refining cost, it is preferably 0.005% or more.
  • Ti 0.10% or less Like Nb, Ti is also an effective element for strengthening steel. However, if Ti is included excessively, the shape fixability will be reduced. Therefore, when containing Ti, the Ti content is set to 0.10% or less, preferably 0.06% or less. On the other hand, the lower limit of the Ti content is not particularly limited and may be 0%, but from the viewpoint of refining cost, it is preferably 0.003% or more.
  • B 0.0002-0.010%
  • B is an element that has the effect of suppressing the production and growth of ferrite from austenite grain boundaries.
  • the B content is preferably 0.0002% or more, more preferably 0.0010% or more.
  • excessive B content significantly impairs moldability. Therefore, when B is contained, the amount of B is 0.010% or less, preferably 0.005% or less.
  • Cr 0.1-1.0% Cr is an element that improves hardenability and contributes to improving the strength of the steel plate.
  • the Cr content is set to 0.1% or more, preferably 0.2% or more in order to obtain the above effects.
  • the Cr content is set to 1.0% or less, preferably 0.5% or less, and more preferably 0.3% or less.
  • Sb 0.003-0.10%
  • Sb is an element that has the effect of suppressing decarburization of the surface layer during the annealing process when manufacturing the base steel plate.
  • the Sb content is set to 0.003% or more, preferably 0.005% or more in order to obtain the above effects.
  • the Sb content is higher than 0.10%, rolling load increases and productivity decreases. Therefore, when Sb is contained, the Sb content is set to 0.10% or less, preferably 0.05% or less, and more preferably 0.03% or less.
  • the base steel plate can typically be manufactured by rolling a steel slab obtained by casting.
  • As the steel slab it is preferable to use a steel slab having the above-mentioned composition.
  • hot slabs obtained by casting may be directly subjected to hot rolling (without reheating), and cold slabs whose temperature has been reduced after casting may be used. may be reheated and subjected to hot rolling. There is almost no difference in the properties of the steel sheets obtained when hot slab slabs are directly rolled and when cold slab slabs are rolled after being reheated.
  • the reheating temperature is not particularly limited, but is preferably in the range of 1000°C to 1300°C in consideration of productivity.
  • the hot rolling can be performed by either a normal hot rolling process or a continuous hot rolling process in which slabs are joined and rolled in finish rolling.
  • the rolling end temperature in hot rolling is not particularly limited, but from the viewpoint of productivity and plate thickness accuracy, it is preferably set to the Ar3 transformation point or higher.
  • the hot rolled steel sheet obtained by the above hot rolling is then cooled according to a conventional method.
  • the winding temperature at that time is preferably 550° C. or higher from the viewpoint of productivity. Furthermore, if the winding temperature is too high, the pickling properties will deteriorate, so the winding temperature is preferably 750° C. or lower. After the cooling, it is preferable to carry out pickling according to a conventional method.
  • cold rolling may be further performed according to a conventional method.
  • a coating layer is formed on the surface of the obtained steel plate.
  • the method of forming the coating layer is not particularly limited, and may be formed by any method such as plating, PVD, clad rolling, etc.
  • the plating include electroplating.
  • the PVD include vacuum evaporation, sputtering, and ion plating.
  • layers having a desired composition may be laminated on both sides of the base steel plate and then rolled.
  • the method for forming the coating layer is preferably selected depending on the composition of the coating layer to be formed.
  • the coating layer is a Ni layer, a Ni--Cr alloy layer, or a Ni--Zn alloy layer
  • the coating layer has a composition that is difficult to deposit from an aqueous solution, such as a Ni--Ti alloy, it is preferable to form the coating layer by PVD.
  • the conditions may be adjusted so that the coating layer on one side (front side) of the steel plate and the other side (back side) of the steel plate has the desired thickness.
  • the thickness of the coating layer on each surface can be adjusted by changing either or both of the current density and the current application time on each surface.
  • a hot press member in an embodiment of the present invention is a hot press member having a base steel plate and a coating layer with a thickness of 0.5 to 6.0 ⁇ m provided on both sides of the base steel plate.
  • the coating layer is made of Ni or a Ni-based alloy, and the Zn content in the coating layer is 0 to 30%.
  • the description of the base steel plate and coating layer in the hot press steel plate described above applies. That is, as the base steel plate of the hot press member, a steel plate similar to the base steel plate of the hot press steel plate described above can be used. Further, as the coating layer of the hot press member, a coating layer similar to the coating layer of the hot press steel plate described above can be used.
  • the Zn content in the coating layer of the hot press member is also preferably 0.5% or more, more preferably 1% or more, and even more preferably 2% or more.
  • the coating layer can also contain a total of 50% by mass or less of at least one selected from the group consisting of Al, Ti, V, Cr, Mn, Fe, Co, Mo, and W.
  • a hot press member in another embodiment of the present invention further has an oxide layer containing one or both of Mn and Fe and having a thickness of 0.1 to 5 ⁇ m on the coating layer. That is, the hot press member of the present embodiment includes a base steel plate, a coating layer with a thickness of 0.5 to 6.0 ⁇ m provided on both sides of the base steel plate, and a coating layer provided on the coating layer. and an oxide layer with a thickness of 0.1 to 5 ⁇ m.
  • the above oxide layer is formed when components contained in the coating layer or the base steel plate react with oxygen or water vapor in the atmosphere during the hot pressing process.
  • the composition and thickness of the oxide layer vary depending on heating conditions such as heating temperature, heating time, and atmosphere.
  • the thickness of the oxide layer exceeds 5 ⁇ m, the adhesion of the coating film decreases, and as a result, it becomes impossible to obtain sufficient corrosion resistance after coating. Therefore, when an oxide layer is present, the thickness of the oxide layer is 5 ⁇ m or less, preferably 3 ⁇ m or less, and more preferably 1 ⁇ m or less.
  • the thinner the oxide layer the better; however, in order to make the oxide layer less than 0.1 ⁇ m thick, the oxygen partial pressure must be extremely reduced. It is necessary to perform hot pressing in an atmosphere or to provide a process for removing oxides after hot pressing, which increases manufacturing costs. Therefore, the thickness of the oxide layer is preferably 0.1 ⁇ m or more.
  • the oxide layer contains one or both of Mn and Fe.
  • these components are eluted into the chemical conversion treatment solution in the chemical conversion treatment step.
  • the formation of the chemical conversion film is promoted, and even better paint adhesion can be obtained.
  • the total proportion of Mn and Fe to all metals contained in the oxide layer is set to 1 to 50 atomic %.
  • the thickness of the oxide layer can be measured by observing the cross section of the hot pressed member with a scanning electron microscope (SEM). More specifically, it can be measured by the method described in Examples.
  • SEM scanning electron microscope
  • the ratio of Mn and Fe to all metals contained in the oxide layer can be measured by measuring the cross section of the hot pressed member using an EPMA (electron beam probe microanalyzer). More specifically, it can be measured by the method described in Examples.
  • EPMA electron beam probe microanalyzer
  • a hot-pressed steel plate is hot-pressed to produce a hot-pressed member.
  • the method of hot pressing is not particularly limited, and can be carried out according to a conventional method.
  • a steel plate for hot pressing is heated to a predetermined heating temperature (heating step), and then the steel plate for hot pressing heated in the heating step is hot pressed (hot pressing step).
  • heating step heating step
  • hot pressing step hot pressing step
  • the heating temperature in the heating step is lower than the Ac3 transformation point of the base steel plate, the strength of the final hot pressed member will be low. Therefore, the heating temperature is preferably at least the Ac3 transformation point of the base steel plate, more preferably at least 860°C. On the other hand, if the heating temperature exceeds 1000° C., the oxide layer produced by oxidation of the base material or coating layer becomes excessively thick, which may deteriorate the paint adhesion of the resulting hot-pressed member. Therefore, the heating temperature is preferably 1000°C or lower, more preferably 960°C or lower, and even more preferably 920°C or lower. Note that the Ac3 transformation point of the base steel plate varies depending on the steel composition, but is determined by the Formaster test.
  • the temperature at which the heating is started is not particularly limited, but is generally room temperature.
  • the time required to raise the temperature from the start of heating until reaching the heating temperature is not particularly limited and can be set to any time.
  • the heating time exceeds 300 seconds, the time of exposure to high temperatures increases, and the oxide layer produced by oxidation of the base material and the plating layer becomes excessively thick. Therefore, from the viewpoint of suppressing the decrease in paint adhesion caused by oxides, the heating time is preferably 100 seconds or less, more preferably 80 seconds or less, and even more preferably 60 seconds or less. preferable.
  • the heating time is preferably 3 seconds or more, more preferably 4 seconds or more, and even more preferably 5 seconds or more.
  • the holding time is not particularly limited, and holding can be carried out for any desired length. However, if the holding time exceeds 100 seconds, the oxide layer produced by oxidation of the base material and coating layer becomes excessively thick, which may deteriorate the paint adhesion of the resulting hot-pressed member. Therefore, the holding time is preferably 100 seconds or less, more preferably 60 seconds or less, and even more preferably 20 seconds or less. On the other hand, the lower limit of the holding time is also not limited, but from the viewpoint of homogeneously austenitizing the base steel plate, it is preferably 1 second or more.
  • the atmosphere in the heating step is not particularly limited, and for example, heating can be performed under an atmospheric atmosphere or in an atmosphere into which the atmospheric air flows. From the viewpoint of reducing the amount of diffusible hydrogen remaining in the member after hot pressing, it is preferable that the dew point of the atmosphere is 10° C. or less. The lower limit of the dew point is also not particularly limited, but may be, for example, ⁇ 40° C. or higher.
  • the method of heating the hot press steel plate is not particularly limited, and any method can be used.
  • the heating can be performed, for example, by furnace heating, current heating, induction heating, high frequency heating, flame heating, or the like. Among these, it is preferable to use electrical heating, induction heating, or high-frequency heating, which can raise the temperature in a short time and has excellent energy efficiency.
  • the heating furnace any heating furnace such as an electric furnace or a gas furnace can be used.
  • the heated steel plate for hot pressing is hot pressed to form a hot pressed member.
  • the steel plate is cooled using a mold or a coolant such as water at the same time as or immediately after the working.
  • hot pressing conditions are not particularly limited.
  • pressing can be started at 600 to 800° C., which is a common hot pressing temperature range.
  • the hot pressing start temperature is preferably 600 to 1000°C.
  • a coating layer was formed on both sides of the base steel plate by the method shown in Tables 1 and 2. Each of the methods used is described below. For comparison, Comparative Example No. In No. 1, no coating layer was formed.
  • the coating layer was formed by electroplating under the following conditions. In each case, electrolysis was performed using the base steel plate as a cathode and the iridium oxide-coated titanium plate as an anode, and the thickness of the coating layer was adjusted by changing the current application time.
  • Ni plating/plating solution composition Nickel sulfate hexahydrate 240g/L Boric acid 30g/L ⁇ pH: 3.0 ⁇ Temperature: 50°C ⁇ Current density: 40A/dm 2
  • Ni-Fe alloy plating/plating solution composition Nickel sulfate hexahydrate 192g/L Iron sulfate heptahydrate 48g/L, Boric acid 30g/L ⁇ pH: 3.0 ⁇ Temperature: 50°C ⁇ Current density: 40A/dm 2
  • Ni-Co alloy plating/plating solution composition Nickel sulfate hexahydrate 180g/L Cobalt sulfate heptahydrate 60g/L Boric acid 30g/L ⁇ pH: 3.0, ⁇ Temperature: 50°C ⁇ Current density: 40A/dm 2
  • Ni-Mo alloy plating/plating solution composition Nickel sulfate hexahydrate 13g/L Sodium molybdate dihydrate 19g/L Citric acid 88g/L ⁇ pH: 3.5 ⁇ Temperature: 25°C ⁇ Current density: 10A/dm 2
  • Ni-W alloy plating/plating solution composition Nickel sulfate hexahydrate 13g/L Sodium tungstate dihydrate 30g/L Citric acid 88g/L ⁇ pH: 3.5 ⁇ Temperature: 25°C ⁇ Current density: 10A/ dm2
  • Ni-Zn alloy plating/plating solution composition Nickel sulfate hexahydrate 240g/L Zinc sulfate heptahydrate/pH: 2.0 ⁇ Temperature: 50°C ⁇ Current density: 40A/dm 2
  • concentration of zinc sulfate heptahydrate in the plating solution was adjusted so that the Zn content of the coating layer was the value shown in Tables 1 and 2.
  • Ni-Fe-Zn alloy plating A plating solution was used in which zinc sulfate heptahydrate was further added to the plating solution for the above (2) Ni-Fe alloy plating. The concentration of zinc sulfate heptahydrate in the plating solution was adjusted so that the Zn content of the coating layer was the value shown in Tables 1 and 2. Other conditions were the same as those for (2) Ni--Fe alloy plating.
  • Ni--Co--Zn alloy plating A plating solution in which zinc sulfate heptahydrate was further added to the plating solution for the above (3) Ni--Co alloy plating was used. The concentration of zinc sulfate heptahydrate in the plating solution was adjusted so that the Zn content of the coating layer was the value shown in Tables 1 and 2. Other conditions were the same as those for (3) Ni--Co alloy plating.
  • Ni-Mo-Zn alloy plating A plating solution in which zinc sulfate heptahydrate was further added to the plating solution for the Ni-Mo alloy plating in (4) above was used. The concentration of zinc sulfate heptahydrate in the plating solution was adjusted so that the Zn content of the coating layer was the value shown in Tables 1 and 2. Other conditions were the same as those for (4) Ni--Mo alloy plating.
  • Ni--W--Zn alloy plating A plating solution in which zinc sulfate heptahydrate was further added to the plating solution for the Ni--W alloy plating in (5) above was used. The concentration of zinc sulfate heptahydrate in the plating solution was adjusted so that the Zn content of the coating layer was the value shown in Tables 1 and 2. Other conditions were the same as those for (5) Ni--W alloy plating.
  • Zn plating/plating solution composition Zinc sulfate heptahydrate 240g/L ⁇ pH: 2.0 ⁇ Temperature: 50°C ⁇ Current density: 40A/dm 2
  • PVD The coating layer was formed by PVD by ion plating using a batch radio frequency (RF) excitation ion plating device manufactured by Showa Shinku Co., Ltd.
  • the temperature of the base steel plate was 400°C, the pressure was 3 Pa, and the bias voltage was -20V.
  • the composition of the coating layer was controlled by adjusting the composition of the metal used as the vapor deposition source. Further, the thickness of the coating layer was controlled by adjusting the deposition time.
  • invention example No. 1 is the same as the above-mentioned invention example No. except that a Ni-16%Cr-8%Fe-0.5%Zn alloy was used as the laminated alloy.
  • Invention example No. 14 was prepared using the same method as in Example No. Thirty hot pressing steel plates were produced. Similarly, using Ni-16%Cr-8%Fe-2%Zn alloy as the laminated alloy, Invention Example No. 46 steel plates for hot pressing were produced.
  • the coating layer was formed by hot-dip plating by immersing the base steel plate in a hot-dip plating bath for 1 second, and then wiping with N 2 gas.
  • the composition of the coating layer was controlled by adjusting the composition of the hot-dip plating bath used.
  • composition and thickness of the coating layer of the obtained hot press steel plate were measured using the following methods. The measurement results are shown in Tables 1 and 2.
  • Component composition of coating layer A cross-sectional sample of the hot press steel plate to be evaluated was prepared by shearing a 10 mm x 15 mm sample and embedding it in a conductive resin. The average composition of the coating layer from the outermost layer to the interface with the base material was measured by EPMA. The component composition of the coating layer was determined by averaging the measured values for three arbitrary samples.
  • the thickness of the coating layer of the hot press steel plate was measured by SEM observation using the cross-sectional sample.
  • the thickness of the coating layer was measured at 10 arbitrary locations within a field of view with a width of 100 ⁇ m or more.
  • the thickness of the coating layer was determined by averaging all the measured values for three arbitrary samples.
  • the above-mentioned steel plate for hot press was subjected to hot press. Specifically, a 200 mm x 1000 mm test piece was taken from the hot press steel plate, and the test piece was directly heated with a current-carrying resistance heating device. The heating was carried out under the following conditions: heating temperature: 950° C., heating time: 20 seconds, holding time: 5 seconds.
  • a hat-shaped hot press was performed at 2 spm (Strokes Per Minute) using a press device installed adjacent to the heating furnace.
  • the molding start temperature was 800°C.
  • the shape of the obtained hot-pressed member was such that the width of the flat portion of the upper surface was 70 mm, the length of the flat portion of the side surface was 30 mm, and the length of the flat portion of the lower surface was 25 mm.
  • the bending R of the mold was 7R for both shoulders on the upper surface and both shoulders on the lower surface.
  • composition and thickness of coating layer The composition and thickness of the coating layer of the obtained hot press member were measured in the same manner as the composition and thickness of the coating layer of the hot press steel plate described above.
  • the cross-sectional sample used for the measurement was prepared by the following procedure. First, the flat part of the top of the hot press member was cut out and sheared to obtain a 10 mm x 15 mm sample. Next, the sample was embedded in a conductive resin to obtain a cross-sectional sample. The measurement results are shown in Tables 3 and 4.
  • composition and thickness of the oxide layer in the hot press member were measured using the following methods. The measurement results are shown in Tables 3 and 4.
  • composition of oxide layer The composition of the oxide layer in the hot pressed member was measured by EPMA. In the measurement, point analysis was performed at ten arbitrary points within a field of view with a width of 100 ⁇ m or more using the cross-sectional sample. From the measurement results, the content (atomic %) of each metal element relative to all metal elements contained in the oxide layer was determined.
  • the thickness of the oxide layer in the hot pressed member was measured by SEM observation using the cross-sectional sample.
  • the thickness of the coating layer was measured at ten arbitrary locations within a field of view with a width of 100 ⁇ m or more, and the thickness of the oxide layer was determined by averaging all the measured values.
  • I max The maximum value of I among the three samples was defined as I max , and was used as an index of the variation in the thickness of the coating layer in the hot pressed member of that example. Judgment was made based on the following criteria using the obtained I max , and cases A and B were determined to be passed. The evaluation results are shown in Tables 3 and 4. A: Imax ⁇ 0.2 B: 0.2 ⁇ Imax ⁇ 0.5 C:I max >0.5
  • the steel sheets for hot pressing that meet the conditions of the present invention have suppressed variations in the thickness of the coating layer even when heated at high speeds, and therefore are heated at high speeds. It has high compatibility with Moreover, the steel plate for hot pressing that satisfies the conditions of the present invention was prevented from liquid metal embrittlement cracking during hot press forming. Furthermore, the hot-pressed member obtained by hot-pressing the hot-pressed steel plate of the present invention also had excellent paint adhesion.

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Chemical Kinetics & Catalysis (AREA)
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  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)
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  • Electroplating Methods And Accessories (AREA)
  • Laminated Bodies (AREA)
PCT/JP2023/023229 2022-09-05 2023-06-22 熱間プレス用鋼板、熱間プレス部材、および熱間プレス部材の製造方法 Ceased WO2024053207A1 (ja)

Priority Applications (6)

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EP23862752.5A EP4541938A4 (en) 2022-09-05 2023-06-22 HOT-PRESSING STEEL SHEET, HOT-PRESSED MEMBER AND METHOD FOR PRODUCING HOT-PRESSED MEMBER
CN202380059570.5A CN119731371A (zh) 2022-09-05 2023-06-22 热压用钢板、热压部件和热压部件的制造方法
JP2023551265A JP7683717B2 (ja) 2022-09-05 2023-06-22 熱間プレス用鋼板、熱間プレス部材、および熱間プレス部材の製造方法
KR1020247042929A KR20250011698A (ko) 2022-09-05 2023-06-22 열간 프레스용 강판, 열간 프레스 부재 및, 열간 프레스 부재의 제조 방법
US18/994,758 US20260049380A1 (en) 2022-09-05 2023-06-22 Steel sheet for hot pressing, hot-pressed member, and hot-pressed member production method
MX2025002610A MX2025002610A (es) 2022-09-05 2025-03-04 Lamina de acero para prensado en caliente, miembro prensado en caliente y metodo de produccion de miembro prensado en caliente

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JP2000038640A (ja) 1998-07-09 2000-02-08 Sollac 熱処理後の耐久性に優れた熱間圧延および冷間圧延被覆鋼板
JP2011122207A (ja) * 2009-12-11 2011-06-23 Jfe Steel Corp 熱間プレス部材およびその製造方法
JP2012197505A (ja) * 2011-03-10 2012-10-18 Jfe Steel Corp 熱間プレス用鋼板およびそれを用いた熱間プレス部材の製造方法
JP2019518136A (ja) * 2016-04-29 2019-06-27 アルセロールミタル プレス焼入れ方法

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US20060130940A1 (en) * 2004-12-20 2006-06-22 Benteler Automotive Corporation Method for making structural automotive components and the like
JP4849186B2 (ja) * 2009-10-28 2012-01-11 Ｊｆｅスチール株式会社 熱間プレス部材およびその製造方法
JP5949680B2 (ja) * 2013-06-25 2016-07-13 Ｊｆｅスチール株式会社 熱間プレス部材の製造方法
CA3076998C (en) * 2017-10-24 2023-08-22 Arcelormittal A method for the manufacture of a coated steel sheet
KR20210092271A (ko) * 2018-12-27 2021-07-23 닛폰세이테츠 가부시키가이샤 Ni 도금 강판 및 Ni 도금 강판의 제조 방법
WO2021230311A1 (ja) * 2020-05-13 2021-11-18 日本製鉄株式会社 ホットスタンプ用鋼板
JP7610158B2 (ja) * 2021-04-06 2025-01-08 日本製鉄株式会社 ホットスタンプ用鋼板

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JP2000038640A (ja) 1998-07-09 2000-02-08 Sollac 熱処理後の耐久性に優れた熱間圧延および冷間圧延被覆鋼板
JP2011122207A (ja) * 2009-12-11 2011-06-23 Jfe Steel Corp 熱間プレス部材およびその製造方法
JP2012197505A (ja) * 2011-03-10 2012-10-18 Jfe Steel Corp 熱間プレス用鋼板およびそれを用いた熱間プレス部材の製造方法
JP2019518136A (ja) * 2016-04-29 2019-06-27 アルセロールミタル プレス焼入れ方法

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Title
See also references of EP4541938A4

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JP7683717B2 (ja) 2025-05-27
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KR20250011698A (ko) 2025-01-21
MX2025002610A (es) 2025-04-02
US20260049380A1 (en) 2026-02-19
CN119731371A (zh) 2025-03-28
EP4541938A4 (en) 2025-10-01

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