WO2022215448A1 - ホットスタンプ成形体 - Google Patents

ホットスタンプ成形体 Download PDF

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Publication number
WO2022215448A1
WO2022215448A1 PCT/JP2022/011331 JP2022011331W WO2022215448A1 WO 2022215448 A1 WO2022215448 A1 WO 2022215448A1 JP 2022011331 W JP2022011331 W JP 2022011331W WO 2022215448 A1 WO2022215448 A1 WO 2022215448A1
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Prior art keywords
phase
mass
hot
layer
group
Prior art date
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Ceased
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PCT/JP2022/011331
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English (en)
French (fr)
Japanese (ja)
Inventor
教史 土井
憲司 小林
尚美 稲富
優貴 鈴木
宗士 藤田
雅裕 布田
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Nippon Steel Corp
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Nippon Steel Corp
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Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Priority to CN202280022871.6A priority Critical patent/CN117043383B/zh
Priority to JP2023512887A priority patent/JP7719393B2/ja
Priority to MX2023008350A priority patent/MX2023008350A/es
Priority to KR1020237026801A priority patent/KR102859054B1/ko
Priority to EP22784433.9A priority patent/EP4321647A4/en
Priority to US18/261,885 priority patent/US12404575B2/en
Publication of WO2022215448A1 publication Critical patent/WO2022215448A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • 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
    • 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
    • B21D22/20—Deep-drawing
    • 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
    • B32B15/012—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 aluminium or an aluminium alloy
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
    • 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
    • C23C2/34—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
    • 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
    • C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
    • C23C28/321—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer with at least one metal alloy layer
    • 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
    • C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
    • C23C28/322—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer only coatings of metal elements only
    • 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
    • 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
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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

Definitions

  • the present invention relates to a hot-stamped molded product.
  • Hot stamping (also called hot pressing, hot pressing, die quenching, press quenching, etc.) is known as a method of forming high-strength steel with high dimensional accuracy. Hot stamping involves heating a steel material such as a steel plate to an austenite region, performing hot forming, and obtaining desired properties by cooling after forming.
  • scale may form on the surface of the steel material during heating, which must be removed in the post-process.
  • a technique is known in which a steel material for hot stamping is plated with Al to suppress the formation of scale.
  • Japanese Patent Publication No. 63-3929 discloses a method for producing a hot-dip aluminum plated steel sheet that exhibits a low oxidation weight gain during high-temperature oxidation.
  • Japanese Patent No. 2943021 after coating the surface of an austenitic stainless steel plate strip with Al, diffusion heat treatment is performed in a non-oxidizing atmosphere within a temperature range of 700 to 800 ° C. Austenitic stainless steel having a NiAl intermetallic compound on the surface layer A method of manufacturing a steel strip is disclosed.
  • This hot stamping member has a steel material, an Al—Fe intermetallic compound layer, and an oxide film layer, and contains Be, Mg, Ca, Sr, Ba, Sc, Ti, V, Cr, and Mn in the oxide film layer. , Fe, Co, Ni, Cu, and Zn are contained in an amount of 0.01 atomic % or more and 80 atomic % or less, excluding oxygen.
  • Japanese Patent Publication No. 2017-536472 discloses a flat steel product for hot forming, which consists of a steel base material and a protective coating containing Al as a main component.
  • the protective coating contains at least one alkaline earth metal or transition metal in a total amount of 0.1% to 0.5% by weight, and the oxide of the alkaline earth metal or transition metal is hot It is said to be formed on the outer surface of the protective coating during molding.
  • An object of the present invention is to provide a hot-stamped article with excellent delayed fracture resistance.
  • a hot stamped compact comprises a steel substrate and an Al coating formed on the steel substrate, the Al coating being formed at an interface with the steel substrate, an interface layer having a structure in which part of ⁇ Fe is replaced with Al and Si; an intermediate layer formed on the interface layer; and an oxide film layer formed on the intermediate layer,
  • the layer thickness is 15 ⁇ m or more
  • the intermediate layer includes an Fe—Al—Si phase having a structure in which part of ⁇ Fe is replaced with Al and Si
  • the Fe—Al—Si phase contains Zr
  • the oxide film layer contains one or more elements selected from the group consisting of Be, Mg,
  • FIG. 1 is a cross-sectional view schematically showing the structure of a plated steel material before hot stamping.
  • FIG. 2 is a cross-sectional view schematically showing the configuration of an example of a hot-stamped body formed by hot-stamping a plated steel material.
  • FIG. 3 is a cross-sectional view schematically showing the configuration of a hot-stamped body according to one embodiment of the present invention.
  • FIG. 4 is a cross-sectional photograph of the Al coating with the symbol a1.
  • FIG. 5 is a cross-sectional photograph of the Al coating of A13.
  • the present inventors conducted various studies on hydrogen absorption when hot stamping Al-plated steel materials, especially Al-Si-plated steel materials.
  • FIG. 1 is a cross-sectional view schematically showing the configuration of a plated steel material 1A before hot stamping.
  • the plated steel material 1A includes a steel base material 10 and an Al—Si plating layer 30.
  • the plated steel material 1A further includes an Al-Si-Fe alloy layer 35 formed between the steel base 10 and the Al-Si plating layer 30 by diffusing Fe of the steel base 10 into the plating layer.
  • FIG. 2 is a cross-sectional view schematically showing the configuration of a hot stamped body 9, which is an example of a hot stamped body formed by hot stamping the plated steel material 1A.
  • the hot-stamped body 9 comprises a steel base 10 and an Al coating 20 formed on the steel base 10 .
  • the Al coating 20 consists of multiple layers. Specifically, the Al coating 20 includes an interface layer 21 formed at the interface with the steel substrate 10, an intermediate layer 22 formed on the interface layer 21, and an oxide film formed on the intermediate layer 22. and layer 23 .
  • the intermediate layer 22 contains an Fe--Al--Si phase 22a and an Al--Fe phase 22b having different structures, and the Fe--Al--Si phase 22a and the Al--Fe phase 22b are distributed in layers.
  • the above classification is based on how it looks when observed with an optical microscope or scanning electron microscope (SEM), and when observed with a transmission electron microscope (TEM), each layer consists of several crystals. It may be observed as an aggregate of phases.
  • the interface layer 21 is a portion derived from the Al—Si—Fe alloy layer 35 of the plated steel material 1A (FIG. 1), and has a structure in which a part of the ⁇ Fe bcc structure is mainly replaced with Al and Si. there is
  • the interfacial layer 21 may contain an intermediate phase such as the ⁇ phase.
  • the intermediate layer 22 contains an Fe--Al--Si phase 22a and an Al--Fe phase 22b.
  • the Fe--Al--Si phase 22a like the interfacial layer 21, has a structure in which a part of the bcc structure of ⁇ Fe is replaced with Al and Si.
  • the Al--Fe phase 22b has a structure of Fe4Al13 and Fe2Al5 . As shown in FIG. 2, the Fe--Al--Si phase 22a is formed in a layered (strip-like) manner sandwiched between upper and lower Al--Fe phases 22b at an intermediate position in the thickness direction of the intermediate layer 22.
  • the oxide film layer 23 is a layer mainly composed of Al oxide.
  • group A elements specific elements in the Fe—Al—Si phase 22a, specifically Zr, Ce, Y, Ta, Ni, Cu, Nb, Cr, Co, V, and Ti.
  • FIG. 3 is a cross-sectional view schematically showing the structure of a hot-stamped body 1, which is an example of a hot-stamped body containing a predetermined amount of A group elements in the Fe--Al--Si phase 22a.
  • the size of the Fe--Al--Si phase 22a is smaller than in the case of the hot-stamped body 9 (FIG. 2).
  • the Fe--Al--Si phase 22a in the hot-stamped body 9 (FIG. 2) is layered (band-shaped), whereas in the hot-stamped body 1 the Fe--Al--Si phase 22a is discontinuous.
  • the A group elements are selectively distributed in the Fe--Al--Si phase 22a.
  • the group A elements are selectively distributed in the Fe--Al--Si phase 22a during heating and have the effect of hindering the stabilization of the Fe--Al--Si phase 22a.
  • the growth of the Al-Fe phase 22b is promoted by hindering the stabilization of the Fe-Al-Si phase 22a.
  • By increasing the thickness of the Al—Fe phase 22b the diffusion of Al to the surface of the Al coating 20 is suppressed, and the oxidation of Al is suppressed. Hydrogen absorption of the steel substrate 10 is thereby suppressed.
  • hydrogen absorption of the steel substrate 10 is suppressed by fixing hydrogen atoms by the Al—Fe phase 22b.
  • group B elements Be, Mg, Ca, Sr, Ba, Sc, and Zn (these seven elements are hereinafter referred to as "group B elements") to the oxide film layer 23. It has been clarified that hydrogen absorption of the steel substrate 10 can be further suppressed by containing the above elements in predetermined amounts. Group B elements have the property of being more easily oxidized than Al, and have the effect of suppressing the hydrogen absorption of the steel base 10 by suppressing the oxidation of Al.
  • the hot stamp molded body 1 is a molded body formed by hot stamping a steel material.
  • a hot stamped body 1 includes a steel base 10 and an Al coating 20 formed on the steel base 10 .
  • the Al coating 20 comprises an interface layer 21 formed at the interface with the steel substrate 10, an intermediate layer 22 formed on the interface layer 21, and an oxide film layer 23 formed on the intermediate layer 22. I have.
  • An interface layer 21 is formed at the interface with the steel substrate 10 .
  • the interface layer 21 has a structure in which a part of the bcc structure of ⁇ Fe is replaced with Al and Si.
  • the chemical composition of the interface layer 21 has a distribution that changes along the thickness direction.
  • the chemical composition of the interface layer 21 is, for example, Fe: 60 to 98 mass %, Al: 1 to 40 mass %, and Si: 1 to 20 mass % on average in the thickness direction.
  • the interface layer 21 may contain small amounts of elements other than Si, Fe, and Al.
  • the upper limit of the total content of elements other than Si, Fe, and Al contained in the interface layer 21 is preferably 3.0% by mass, more preferably 1.5% by mass.
  • the boundary between the interface layer 21 and the steel substrate 10 is not clear, but in this case, the interface layer 21 is defined as having a depth of 10 ⁇ m from the interface of the intermediate layer 22, and the average chemical composition of this range is obtained. shall be
  • the chemical composition of the interface layer 21 can be measured by analyzing the cross section of the Al coating 20 with an electron probe microanalyzer (EPMA) or an energy resolving spectrometer (EDS) of an SEM.
  • EPMA electron probe microanalyzer
  • EDS energy resolving spectrometer
  • the thickness of the interface layer 21 is not particularly limited, it is, for example, 5 to 15 ⁇ m.
  • An intermediate layer 22 is formed on the interfacial layer 21 .
  • the intermediate layer 22 contains an Fe--Al--Si phase 22a and an Al--Fe phase 22b.
  • the Fe--Al--Si phase 22a like the interfacial layer 21, has a structure in which a part of the bcc structure of ⁇ Fe is replaced with Al and Si.
  • the Al--Fe phase 22b has a structure of Fe4Al13 and Fe2Al5 . Note that the Al—Fe phase 22b may also contain Si in a solid solution.
  • the Fe--Al--Si phase 22a and the Al--Fe phase 22b can be distinguished by analyzing the chemical composition of the cross section of the Al coating 20 with EPMA or SEM EDS.
  • the Fe--Al--Si phase 22a and the Al--Fe phase 22b can also be distinguished by analyzing the crystal structure by X-ray diffraction or electron beam diffraction.
  • the interfacial layer 21 and the Fe--Al--Si phase 22a have structures similar to each other, they can be distinguished by their positions. That is, the interfacial layer 21 is formed at the interface with the steel base 10, while the Fe--Al--Si phase 22a is formed at an intermediate position of the intermediate layer 22 in the thickness direction.
  • the Si content in the Fe--Al--Si phase 22a is 1-20% by mass. If the Si content is lower than 1% by mass, the oxide film layer 23 grows and as a result the amount of hydrogen absorbed into the steel substrate 10 increases. If the Si content is higher than 20% by mass, the intermediate layer 22 will not grow sufficiently, and the amount of hydrogen absorbed by the steel substrate 10 will also increase.
  • the lower limit of the Si content in the Fe--Al--Si phase 22a is preferably 5% by mass, more preferably 8% by mass.
  • the upper limit of the Si content in the Fe--Al--Si phase 22a is preferably 18% by mass, more preferably 16% by mass.
  • the Fe content in the Fe--Al--Si phase 22a is not particularly limited, but is, for example, 30-80% by mass.
  • the Al content in the Fe--Al--Si phase 22a is not particularly limited, but is, for example, 5-50% by mass.
  • the Fe—Al—Si phase 22a is one selected from the group consisting of Zr, Ce, Y, Ta, Ni, Cu, Nb, Cr, Co, V, and Ti in addition to Fe, Al, and Si. or contains two or more elements.
  • the eleven elements of Zr, Ce, Y, Ta, Ni, Cu, Nb, Cr, Co, V, and Ti are hereinafter referred to as group A elements.
  • group A elements Zr, Ce, Ni, Cr, Co, V, and Ti are preferred, and Ni and Cr are particularly preferred.
  • the total content of group A elements in the Fe--Al--Si phase 22a is 0.10-5.0% by mass.
  • the A group elements prevent stabilization of the Fe—Al—Si phase 22a, promote growth of the Al—Fe phase 22b, and suppress hydrogen absorption of the steel base 10. If the total content of group A elements is less than 0.1% by mass, this effect cannot be sufficiently obtained. On the other hand, if the total content of group A elements is higher than 5.0% by mass, the Fe--Al--Si phase 22a may rather become enlarged.
  • the lower limit of the total content of group A elements in the Fe--Al--Si phase 22a is preferably 0.20% by mass, more preferably 0.30% by mass.
  • the upper limit of the content of the group A element in the Fe--Al--Si phase 22a is preferably 4.0% by mass, more preferably 3.0% by mass.
  • the Fe--Al--Si phase 22a may contain small amounts of elements other than Si, Fe, Al, and A group elements.
  • the upper limit of the total content of elements other than Si, Fe, Al, and A group elements contained in the Fe—Al—Si phase 22a is preferably 1.0% by mass, more preferably 0.5% by mass. is.
  • the chemical composition of the Fe-Al-Si phase 22a can be measured by analyzing the cross section of the Al coating 20 with EPMA or SEM EDS, as in the case of the interfacial layer 21. Specifically, the content of the element is measured at a plurality of locations, and the average value is taken as the content of the element.
  • the chemical composition of the Al—Fe phase 22b described below can also be measured in a similar manner.
  • the chemical composition of the Al—Fe phase 22b is not particularly limited, but is, for example, Fe: 15-70% by mass, Al: 30-85% by mass, and Si: 0-20% by mass.
  • the Al--Fe phase 22b basically has the structure of Fe 4 Al 13 and Fe 2 Al 5 , but may contain Si in a solid solution.
  • the Al—Fe phase 22b may contain small amounts of elements other than Si, Fe, and Al.
  • the upper limit of the total content of elements other than Si, Fe, and Al contained in the Al—Fe phase 22b is preferably 1.0% by mass, more preferably 0.5% by mass.
  • the area ratio of the Fe--Al--Si phase 22a in the intermediate layer 22 is preferably 5-35%.
  • the upper limit of the area ratio of the Fe--Al--Si phase 22a in the intermediate layer 22 is more preferably 30%, more preferably 25%.
  • the intermediate layer 22 may contain a small amount of other phases in addition to the Fe--Al--Si phase 22a and the Al--Fe phase 22b.
  • Phases other than the Fe--Al--Si phase 22a and the Al--Fe phase 22b are, for example, the ⁇ phase.
  • the area ratio of the phases other than the Fe--Al--Si phase 22a and the Al--Fe phase 22b in the intermediate layer 22 is preferably 10.0% or less, more preferably 5.0% or less.
  • the thickness of the intermediate layer 22 is 15 ⁇ m or more.
  • the lower limit of the thickness of the intermediate layer 22 is preferably 20 ⁇ m, more preferably 25 ⁇ m.
  • the upper limit of the thickness of the intermediate layer 22 is not particularly limited, it is, for example, 50 ⁇ m.
  • An oxide layer 23 is formed over the intermediate layer 22 .
  • the oxide film layer 23 is a layer mainly composed of Al oxide.
  • the oxide film layer 23 may contain elements other than Al and O.
  • the oxide film layer 23 may contain, for example, Si, Fe, and the group A elements described above.
  • the oxide film layer 23 further contains one or more elements selected from the group consisting of Be, Mg, Ca, Sr, Ba, Sc, and Zn.
  • the seven elements of Be, Mg, Ca, Sr, Ba, Sc, and Zn are hereinafter referred to as group B elements.
  • group B elements Mg, Ca, Sr and Ba are preferred, and Mg is particularly preferred.
  • the group B element preferably exists in the form of an oxide.
  • the total proportion of the group B elements in the components excluding oxygen in the oxide film layer 23 (hereinafter simply referred to as "the proportion of group B elements") is 0.01 to 80.0% by mass.
  • Group B elements have the property of being more easily oxidized than Al, and have the effect of suppressing the hydrogen absorption of the steel base 10 by suppressing the oxidation of Al. If the proportion of the group B element is less than 0.01% by mass, this effect cannot be sufficiently obtained. If the proportion of the B group element is higher than 80.0% by mass, the oxide film layer 23 may rather become thicker.
  • the lower limit of the ratio of the group B elements is preferably 1.0% by mass, more preferably 3.0% by mass, still more preferably 10% by mass, still more preferably 15% by mass.
  • the upper limit of the ratio of the group B elements is preferably 60.0% by mass, more preferably 40.0% by mass, and still more preferably 35% by mass.
  • the chemical composition of the oxide film layer 23 can be measured by analyzing the cross section of the Al coating 20 with EPMA or SEM EDS, as with the interface layer 21 and the intermediate layer 22 . EDS of TEM is also possible.
  • the chemical composition of oxide layer 23 can also be measured by depth profiling composition analysis by glow discharge spectroscopy (GDS) or Auger electron spectroscopy (AES).
  • the thickness of the oxide film layer 23 is preferably 0.01 to 1.00 ⁇ m. Hydrogen absorption of the steel base 10 tends to be suppressed more as the oxide film layer 23 is thinner.
  • the upper limit of the thickness of the oxide film layer 23 is preferably 0.50 ⁇ m, more preferably 0.30 ⁇ m.
  • the interface between the oxide film layer 23 and the intermediate layer 22 can be determined by observing the oxygen concentration distribution.
  • the interface between the oxide film layer 23 and the intermediate layer 22 is determined to be the position where the detected intensity of oxygen has decreased to 1/6 of the maximum value using the GDS.
  • the Fe--Al--Si phase 22a contains one or two elements selected from the group consisting of Ni and Cr, and the total content of Ni and Cr in the Fe--Al--Si phase 22a is 0.5. 10 to 5.0% by mass, the oxide film layer 23 contains Mg, and the ratio of Mg in the components other than oxygen in the oxide film layer 23 is particularly 0.01 to 80.0% by mass. preferable.
  • the steel base material 10 is not particularly limited as long as it is a steel material suitable for hot stamping.
  • a steel base material applicable to the hot stamped body 1 has, for example, a chemical composition in mass % of C: 0.1 to 0.6%, Si: 0.01 to 0.60%, Mn: 0.50. ⁇ 3.00%, P: 0.05% or less, S: 0.020% or less, Al: 0.10% or less, Ti: 0.01-0.10%, B: 0.0001-0.0100 %, N: 0.010% or less, Cr: 0 to 1.0%, Mo: 0 to 1.0%, Cu: 0 to 1.0%, Ni: 0 to 1.0%, the balance: Fe and A steel material that is an impurity can be exemplified.
  • Examples of the form of the steel base material before hot stamping include steel sheets such as hot-rolled steel sheets and cold-rolled steel sheets.
  • the chemical composition of the steel base material 10 will be described below. In the following description, "%" of element content means % by mass.
  • C 0.1-0.6% Carbon (C) is contained to ensure the desired mechanical strength. If the C content is too low, a sufficient improvement in mechanical strength may not be obtained. On the other hand, if the C content is too high, the elongation and reduction in area of drawing will tend to decrease.
  • the upper limit of the C content is more preferably 0.4%.
  • Si 0.01-0.60% Silicon (Si) is an element that improves mechanical strength, and like C, is contained to ensure the desired mechanical strength. If the Si content is too low, a sufficient improvement in mechanical strength may not be obtained. On the other hand, if the Si content is too high, the influence of Si oxides formed on the surface layer of the steel substrate may reduce the wettability during plating, resulting in non-plating.
  • Mn 0.50-3.00%
  • Mn Manganese
  • S which is one of the impurities. If the Mn content is too low, these effects may not be obtained sufficiently. On the other hand, if the Mn content is too high, the amount of retained austenite will be too large, possibly resulting in a decrease in strength.
  • P 0.05% or less Phosphorus (P) is an impurity contained in the steel base material.
  • P contained in the steel base may segregate at the grain boundaries of the steel base and reduce the toughness of the steel base. It is preferable to reduce the P content as much as possible.
  • S 0.020% or less Sulfur (S) is an impurity contained in the steel base material.
  • S contained in the steel substrate may form sulfides and reduce the toughness of the steel substrate. It is preferable to reduce the S content as much as possible.
  • Al 0.10% or less
  • Aluminum (Al) is generally used for the purpose of deoxidizing steel. However, when the Al content is high, the Ac 3 point of the steel substrate increases, so it is necessary to raise the heating temperature necessary to ensure the hardenability of the steel during hot stamping. Therefore, the Al content is preferably 0.10% or less.
  • the Al content is more preferably 0.05% or less, still more preferably 0.01% or less.
  • Titanium is one of strength enhancing elements. If the Ti content is too low, the effect of improving strength and the effect of improving oxidation resistance may not be sufficiently obtained. On the other hand, if the Ti content is too high, carbides and nitrides are formed, which may soften the steel.
  • B 0.0001 to 0.0100% Boron (B) acts during quenching and has the effect of improving strength. If the B content is too low, a sufficient strength improvement effect may not be obtained. On the other hand, if the B content is too high, inclusions may be formed to embrittle the steel base material and reduce the fatigue strength.
  • N 0.010% or less Nitrogen (N) is an impurity contained in the steel base material.
  • N contained in the steel substrate may form nitrides and reduce the toughness of the steel substrate.
  • N contained in the steel base material may combine with B to reduce the amount of solid solution B, thereby reducing the hardenability improvement effect of B. It is preferable to reduce the N content as much as possible.
  • the steel base material 10 may contain Cr, Mo, Cu and Ni.
  • Cr 0-1.0% Mo: 0-1.0%
  • Cu 0-1.0%
  • Ni 0-1.0%
  • Cr chromium
  • Mo molybdenum
  • Cu copper
  • Ni nickel
  • a preferred lower limit for the content of these elements is 0.01%.
  • the rest of the chemical composition of the steel base 10 is Fe and impurities.
  • impurities refers to elements mixed in from ores and scraps used as raw materials for steel, or elements mixed in from the environment during the manufacturing process. Impurities include, for example, Zn, Co, Sn, Nb, V, As, Zr, Ca, Mg, etc., in addition to the elements listed above.
  • a plating layer is formed on the surface of the steel material by hot dip plating.
  • the temperature of the plating bath is preferably 600-700°C. If the temperature of the plating bath is lower than 600° C., the viscosity of the plating bath will be low, making uniform plating difficult. If the temperature of the plating bath is higher than 700° C., the components change in a short time due to volatilization, making process control difficult.
  • the content of the group A element in the plating bath is preferably 0.05-5.0% by mass.
  • the higher the content of the group A element in the plating bath the higher the content of the group A element in the Fe—Al—Si phase 22a.
  • the lower limit of the content of the group A element in the plating bath is more preferably 0.2% by mass, still more preferably 0.5% by mass.
  • the upper limit of the content of the group A element in the plating bath is more preferably 3.0% by mass, still more preferably 2.0% by mass.
  • Addition of B group elements is also performed by addition to the plating bath.
  • the content of the group B element in the plating bath is preferably 0.01 to 1.0% by mass.
  • the lower limit of the content of the group B element in the plating bath is more preferably 0.05% by mass, still more preferably 0.08% by mass.
  • the upper limit of the content of the B group element in the plating bath is more preferably 0.8% by mass, still more preferably 0.6% by mass.
  • the Si content in the plating bath is, for example, 1.0 to 20.0% by mass.
  • the balance of the plating bath is primarily Al.
  • the plating bath may contain small amounts of elements other than Al, Si, A group elements, and B group elements.
  • the total content of elements other than Al, Si, A group elements, and B group elements contained in the plating bath is preferably 5.0% by mass or less, more preferably 3.0% by mass or less, It is more preferably 2.0% by mass or less, and still more preferably 1.0% by mass or less.
  • Plating is preferably performed so that the plating layer has a thickness of 20 to 30 ⁇ m.
  • the thickness of the plating layer is adjusted so that the intermediate layer 22 has a thickness of 15 ⁇ m or more after the hot stamping process.
  • the thickness of the plating layer can be adjusted by the temperature, viscosity, immersion time, gas spraying, etc. of the plating bath.
  • the heating method may be either a high-temperature furnace or electric heating.
  • the heating rate is, for example, 1 to 50° C./s. It is preferable that the holding temperature is 850 to 950° C. and the holding time is 2 minutes or more.
  • the temperature drop (cooling) rate is, for example, 30 to 1000° C./s.
  • the upper limit of the retention time is preferably 30 minutes, more preferably 10 minutes.
  • the hot stamped body 1 can be manufactured through the above steps. Although the method of hot stamping the plated steel material has been described above, instead of this, an Al coating layer is formed by depositing Al or the like on the surface of the steel base 10 by vapor deposition or thermal spraying, and this Al coating layer is provided.
  • the hot-stamped body 1 may be produced by hot-stamping the steel substrate 10 .
  • a hot-stamped article having excellent delayed fracture resistance can be obtained.
  • an Al-Si plating layer was formed on both sides of the steel sheet by hot dip plating.
  • a plating bath having a chemical composition shown in Table 2 was used.
  • the temperature of the plating bath during hot-dip plating was 700°C.
  • the coating weight was adjusted to 70 g/m 2 per side by gas wiping.
  • the plated steel sheet was heated in an electric resistance furnace at a furnace temperature of 900°C under a synthetic air stream with a dew point of 20°C so that the soaking time was 5 minutes. After that, it was molded in a mold and simultaneously cooled in the mold to obtain a hot-stamped product.
  • the content of Si in the Fe-Al-Si phase, the content of group A elements in the Fe-Al-Si phase, the area ratio of the Fe-Al-Si phase in the intermediate layer, The thickness of the intermediate layer, the ratio of the group B elements in the components other than oxygen in the oxide film layer, and the thickness of the oxide film layer were investigated.
  • hydrogen embrittlement resistance delayed fracture resistance
  • paint adhesion corrosion resistance after painting, and pitting corrosion resistance were evaluated.
  • Hydrogen analysis was performed on the obtained hot stamped molded body. Hydrogen analysis was performed by the temperature programmed desorption method, hydrogen released up to 250° C. was defined as diffusible hydrogen, and the amount was rated as follows. 2: Amount of diffusible hydrogen less than 0.1 ppm by mass 1: Amount of diffusible hydrogen 0.1 ppm by mass or more and less than 0.2 ppm by mass 0: Amount of diffusible hydrogen 0.2 ppm by mass or more
  • Paint adhesion was evaluated according to the method described in Japanese Patent No. 4373778. That is, after immersing the sample in deionized water at 60°C for 240 hours, cut 100 grids at 1 mm intervals with a cutter, and visually measure the number of peeled portions of the grid. Scored as follows. 3: Peeling area 0% or more and less than 10% 2: Peeling area 10% or more and less than 70% 1: Peeling area 70% or more and 100% or less
  • Corrosion resistance evaluation after painting was performed by the method specified in JASO M609 established by the Society of Automotive Engineers of Japan.
  • the coating film was scratched with a cutter, and the width (maximum value on one side) of the coating film blisters from the cut scratches after 180 cycles of the corrosion test was measured and rated as follows.
  • the sample was immersed in a surface conditioning agent Preparen X manufactured by Nihon Parkerizing Co., Ltd. for 1 minute at normal temperature, and then immersed in a coating base chemical agent Palbond SX35 manufactured by the same company at 35° C. for 2 minutes. After that, it was subjected to a combined cycle corrosion test by the method described in JIS H8502.
  • a coating film having a thickness of 15 ⁇ m was applied using Power Float 1200 manufactured by Nippon Paint Co., Ltd., and a cut was applied using a cutter knife as described in JIS H8502.
  • the thickness reduction amount of the steel sheet after 60 cycles of the cut portion was evaluated as follows.
  • Thickness reduction of less than 0.1 mm 4 Thickness reduction of 0.1 mm or more and less than 0.2 mm 3: Thickness reduction of 0.2 mm or more and less than 0.3 mm 2: Thickness reduction of 0.3 mm or more0.
  • Less than 4 mm 1 Thickness reduction of 0.4 mm or more
  • the hot stamped compacts with symbols A01 to A17 have a Si content in the Fe—Al—Si phase of 1 to 20% by mass, and a group A element content of It was within the range of 0.10 to 5.0% by mass. These hot-stamped products had an amount of diffusible hydrogen of less than 0.2 mass ppm in the hydrogen embrittlement resistance test. These hot-stamped products were also excellent in paint adhesion, corrosion resistance after painting, and pitting corrosion resistance. Among them, the hot stamped compacts of A01 to A05, A10, A12, A13, A15 and A17, in which the oxide film layer contained a group B element, had an amount of diffusible hydrogen of 0.5 in the hydrogen embrittlement resistance test. It was less than 1 ppm by mass, and showed particularly excellent hydrogen embrittlement resistance (delayed fracture resistance).
  • the hot-stamped bodies with symbols a1 to a7 have an amount of diffusible hydrogen of 0.2 mass ppm or more in the hydrogen embrittlement resistance test, and compared with the hot-stamped bodies with symbols A01 to A20, the hydrogen embrittlement resistance ( delayed fracture resistance) was inferior. This is because the content of the group A element in the Fe—Al—Si phase was less than 0.1% by mass or higher than 5.0% by mass in the hot stamped compacts with symbols a1 to a7. Conceivable.
  • FIG. 4 is a cross-sectional photograph of the Al coating with the symbol a1.
  • FIG. 5 is a cross-sectional photograph of the Al coating of A13. As shown in FIGS. 4 and 5, in A13, the area ratio of the Fe—Al—Si phase was smaller than in a1. In addition, the Fe--Al--Si phase formed in layers (stripes) in the sample a1 was discontinuous.
  • Hot stamp molded body 1A Plated steel material 10 Steel base material 20 Al coating 21 Interface layer 22 Intermediate layer 22a Fe-Al-Si phase 22b Al-Fe phase 23 Oxide film layer 30 Al-Si plating layer 35 Al-Si- Fe alloy layer

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS633929A (ja) 1986-06-24 1988-01-08 Kobe Steel Ltd 射出成形機
JP2943021B2 (ja) 1991-01-31 1999-08-30 日本冶金工業株式会社 表層にＮｉＡｌ金属間化合物を有するオーステナイト鋼板帯の製造方法
JP4373778B2 (ja) 2001-06-15 2009-11-25 日本パーカライジング株式会社 金属の表面処理用処理液及び表面処理方法
JP2017536472A (ja) 2014-09-05 2017-12-07 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトＴｈｙｓｓｅｎＫｒｕｐｐ Ｓｔｅｅｌ Ｅｕｒｏｐｅ ＡＧ Ａｌ被覆を有する平鋼製品、平鋼製品の製造方法、鋼製部材および鋼製部材の製造方法
WO2018221738A1 (ja) 2017-06-02 2018-12-06 新日鐵住金株式会社 ホットスタンプ部材
WO2020111230A1 (ja) * 2018-11-30 2020-06-04 日本製鉄株式会社 アルミめっき鋼板、ホットスタンプ部材及びホットスタンプ部材の製造方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56102523A (en) 1980-01-22 1981-08-17 Nisshin Steel Co Ltd Manufacture of aluminum-plated steel sheet having resistance to oxidation at high temperature
JP4564207B2 (ja) 2001-06-25 2010-10-20 新日本製鐵株式会社 ８００℃以上に加熱しプレス加工する高温プレス用の溶融アルミめっき鋼板
CN100370054C (zh) 2001-06-15 2008-02-20 新日本制铁株式会社 镀有铝合金体系的高强度钢板以及具有优异的耐热性和喷漆后耐腐蚀性的高强度汽车零件
JP5005254B2 (ja) 2006-05-15 2012-08-22 新日本製鐵株式会社 昇温特性、加工性、および塗装後耐食性に優れたホットプレス用Ａｌめっき鋼材
JP2013122447A (ja) * 2011-11-09 2013-06-20 Panasonic Corp 赤外線応用デバイス
KR101569509B1 (ko) 2014-12-24 2015-11-17 주식회사 포스코 프레스성형시 내파우더링성이 우수한 hpf 성형부재 및 이의 제조방법
MX2019011731A (es) * 2017-03-31 2019-11-21 Nippon Steel Corp Cuerpo estampado en caliente.
IN202017021813A (https=) * 2018-02-15 2020-08-21 Nippon Steel Corp

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS633929A (ja) 1986-06-24 1988-01-08 Kobe Steel Ltd 射出成形機
JP2943021B2 (ja) 1991-01-31 1999-08-30 日本冶金工業株式会社 表層にＮｉＡｌ金属間化合物を有するオーステナイト鋼板帯の製造方法
JP4373778B2 (ja) 2001-06-15 2009-11-25 日本パーカライジング株式会社 金属の表面処理用処理液及び表面処理方法
JP2017536472A (ja) 2014-09-05 2017-12-07 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトＴｈｙｓｓｅｎＫｒｕｐｐ Ｓｔｅｅｌ Ｅｕｒｏｐｅ ＡＧ Ａｌ被覆を有する平鋼製品、平鋼製品の製造方法、鋼製部材および鋼製部材の製造方法
WO2018221738A1 (ja) 2017-06-02 2018-12-06 新日鐵住金株式会社 ホットスタンプ部材
WO2020111230A1 (ja) * 2018-11-30 2020-06-04 日本製鉄株式会社 アルミめっき鋼板、ホットスタンプ部材及びホットスタンプ部材の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4321647A4

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