WO2015174530A1 - Élément de plaque d'acier laminée à chaud - Google Patents

Élément de plaque d'acier laminée à chaud Download PDF

Info

Publication number
WO2015174530A1
WO2015174530A1 PCT/JP2015/064101 JP2015064101W WO2015174530A1 WO 2015174530 A1 WO2015174530 A1 WO 2015174530A1 JP 2015064101 W JP2015064101 W JP 2015064101W WO 2015174530 A1 WO2015174530 A1 WO 2015174530A1
Authority
WO
WIPO (PCT)
Prior art keywords
hot
less
steel sheet
steel plate
content
Prior art date
Application number
PCT/JP2015/064101
Other languages
English (en)
Japanese (ja)
Inventor
匹田　和夫
啓達 小嶋
進一郎 田畑
Original Assignee
新日鐵住金株式会社
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 新日鐵住金株式会社 filed Critical 新日鐵住金株式会社
Priority to JP2016519321A priority Critical patent/JP6315087B2/ja
Priority to ES15793575T priority patent/ES2753390T3/es
Priority to CN201580024959.1A priority patent/CN106661685B/zh
Priority to KR1020167033364A priority patent/KR101908210B1/ko
Priority to PL15793575T priority patent/PL3144405T3/pl
Priority to EP15793575.0A priority patent/EP3144405B1/fr
Priority to US15/311,117 priority patent/US20170073792A1/en
Priority to MX2016014884A priority patent/MX2016014884A/es
Publication of WO2015174530A1 publication Critical patent/WO2015174530A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—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
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • 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
    • C25D3/22—Electroplating: Baths therefor from solutions of zinc
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor

Definitions

  • This specification relates to a hot-formed steel plate member formed by hot forming a steel plate.
  • a hot stamping technique has been adopted as a technique for press forming a difficult-to-form material such as a high-strength steel sheet.
  • the hot stamping technique is a hot forming technique in which a material used for forming is heated to form.
  • the steel sheet is soft and has good formability during forming, and after forming, the formed member can obtain higher strength than the cold forming steel sheet.
  • Japanese Patent Application Publication No. 2006-213959 discloses a steel member having a tensile strength of 980 MPa.
  • Japanese Patent Application Publication No. 2007-314817 discloses that a hot pressed steel sheet member having excellent tensile strength and toughness can be obtained by reducing the cleanliness and the segregation degree of P and S. Yes.
  • Japanese Patent Application Publication No. 2002-102980 has a problem that the hardenability at the time of hot pressing is insufficient, resulting in poor hardness stability.
  • Japanese Patent Application Publication No. 2006-213959 and Japanese Patent Application Publication No. 2007-314817 disclose steel sheets having excellent tensile strength and toughness, there is still room for improvement in terms of local deformation characteristics. Has been.
  • An object of the embodiment of the present specification is to provide a hot-formed steel sheet member having excellent hardness stability and local deformability.
  • the hot-formed steel plate member is not a flat plate but a formed body.
  • the hot-formed steel plate member is also referred to as a “hot-formed steel plate member”.
  • Chemical composition is mass%, C: 0.08 to 0.16%, Si: 0.19% or less, Mn: 0.40 to 1.50%, P: 0.02% or less, S: 0.01% or less, sol.
  • the total volume ratio of martensite, tempered martensite and bainite is 50% or more, and the volume ratio of ferrite is 3% or less,
  • the average particle size of the former ⁇ grains is 10 ⁇ m or less,
  • There is provided a hot-formed steel sheet member in which the number density of residual carbides present is 4 ⁇ 10 3 pieces / mm 2 or less.
  • the embodiment of the present specification is based on the above knowledge, and according to one aspect of the embodiment, (1)
  • the chemical composition is mass%, C: 0.08 to 0.16%, Si: 0.19% or less, Mn: 0.40 to 1.50%, P: 0.02% or less, S: 0.01% or less, sol.
  • a hot-formed steel plate member according to (1) preferably The chemical composition is mass%, Nb: 0.003 to 0.50%, Ni: 0.01 to 2.0%, Cu: 0.01 to 1.0%, Mo: 0.01 to 1.0%, V: 0.01 to 1.0% And Ca: 0.001 to 0.005% 1 or more types selected from the group consisting of:
  • the hot-formed steel plate member according to any one of (1) to (4) preferably having a plating layer on the surface of the steel plate member.
  • the hot-formed steel plate member according to any one of (1) to (5) preferably, the steel plate member has a tensile strength of 1.0 GPa or more.
  • C 0.08 to 0.16%
  • C is an important element for enhancing the hardenability of steel and ensuring the strength after quenching. Further, since C is an austenite-forming element, it has an effect of suppressing strain-induced ferrite transformation during high strain forming. Therefore, it is easy to obtain a stable hardness distribution in the steel sheet member after hot forming. When the C content is less than 0.08%, it becomes difficult to secure a tensile strength of 1.0 GPa or more after quenching and to obtain the above-described effects. Therefore, the C content is 0.08% or more. On the other hand, if the C content exceeds 0.16%, the strength after quenching excessively increases and local deformability deteriorates. Therefore, the C content is 0.16% or less.
  • the C content is preferably 0.085% or more, and more preferably 0.9% or more. Moreover, it is preferable that C content is 0.15% or less, and it is more preferable that it is 0.14% or less.
  • Si 0.19% or less Si is an element having an action of suppressing scale formation during high-temperature heating during hot forming.
  • the Si content exceeds 0.19%, the heating temperature necessary for austenite transformation during hot forming becomes extremely high. For this reason, the cost required for heat treatment increases, and quenching becomes insufficient due to insufficient heating.
  • Si is a ferrite-forming element, if the Si content is too high, strain-induced ferrite transformation is likely to occur during high strain molding. For this reason, the hardness of the steel sheet member after hot forming is locally reduced, making it difficult to obtain a stable hardness distribution.
  • the Si content is 0.19% or less.
  • the Si content is preferably 0.15% or less.
  • the Si content is preferably 0.01% or more.
  • Mn 0.40 to 1.50%
  • Mn is an element useful for enhancing the hardenability of the steel sheet and for ensuring the strength after hot forming stably. If the Mn content is less than 0.40%, it is difficult to obtain the above effects. Therefore, the Mn content is 0.40% or more. On the other hand, when the Mn content exceeds 1.50%, coarse MnS is generated, which causes deterioration of local deformability. Therefore, the Mn content is 1.50% or less.
  • the Mn content is preferably 0.80% or more, and preferably 1.40% or less.
  • P 0.02% or less
  • P is an element contained as an impurity, but has the effect of improving the hardenability of steel and further ensuring the strength of steel after quenching stably. , You may make it contain positively.
  • the P content exceeds 0.02%, the local deformability is significantly deteriorated. Therefore, the P content is 0.02% or less.
  • the P content is preferably 0.01% or less.
  • the lower limit of the P content is not particularly limited, but excessive reduction of the P content causes a significant cost increase. For this reason, it is preferable that P content shall be 0.0002% or more.
  • S 0.01% or less S is an element that is contained as an impurity and deteriorates local deformability. When the S content exceeds 0.01%, the local deformability is significantly deteriorated. Therefore, the S content is 0.01% or less.
  • the lower limit of the S content is not particularly limited, but excessive reduction of the S content causes a significant cost increase, so the S content is preferably 0.0002% or more.
  • sol. Al 0.01 to 1.0% sol.
  • Al is an element having an action of deoxidizing molten steel to make the steel sound. sol. If the Al content is less than 0.01%, deoxidation is not sufficient. Furthermore, sol. Al is an element that has the effect of enhancing the hardenability of the steel sheet and ensuring the strength after quenching stably, so it may be positively incorporated. Therefore, sol. Al content shall be 0.01% or more. However, even if it contains exceeding 1.0%, the effect acquired by the effect
  • N 0.01% or less
  • N is an element that is contained as an impurity and deteriorates toughness. If the N content exceeds 0.01%, coarse nitrides are formed in the steel, and the local deformability and toughness are significantly deteriorated. Therefore, the N content is 0.01% or less.
  • the N content is preferably 0.008% or less.
  • the lower limit of the N content is not particularly limited, but excessive reduction of the N content causes a significant cost increase. For this reason, the N content is preferably 0.0002% or more, and more preferably 0.0008% or more.
  • Cr 0.25 to 3.00% Cr is an element having an effect of enhancing the hardenability of steel. Therefore, it is an especially important element in the embodiment in which the Mn content is limited to 1.50% or less.
  • Cr is an austenite-forming element and has an action of suppressing strain-induced ferrite transformation during high strain forming. Therefore, by containing Cr, it becomes easy to obtain a stable hardness distribution in the steel sheet member after hot forming. If the Cr content is less than 0.25%, the above effects cannot be obtained sufficiently. Therefore, the Cr content is 0.25% or more. On the other hand, if the Cr content exceeds 3.00%, Cr concentrates in carbides in the steel, delays the solid solution of carbides in the heating process when subjected to hot forming, and decreases hardenability. Therefore, the Cr content is 3.00% or less.
  • the Cr content is preferably 0.30% or more, and more preferably 0.40% or more. Moreover, it is preferable that Cr content is 2.50% or less, and it is preferable that it is 2.00%
  • Ti 0.01 to 0.05%
  • Ti is an element having an action of suppressing recrystallization of austenite grains when the hot forming steel sheet is heated to Ac 3 point or more and used for hot forming. Furthermore, it has the effect
  • Ti content shall be 0.05% or less.
  • the Ti content is preferably 0.015% or more.
  • Ti content is 0.04% or less, and it is preferable that it is 0.03% or less.
  • B 0.001 to 0.01%
  • B is an element having an effect of enhancing the hardenability of steel and ensuring the strength after quenching stably. Therefore, it is an especially important element in the embodiment in which the Mn content is limited to 1.50% or less. If the B content is less than 0.001%, the above effects cannot be obtained sufficiently. Therefore, the B content is 0.001% or more. On the other hand, when the B content exceeds 0.01%, the above effect is saturated, and further, local deformability deterioration of the quenched portion is caused. Therefore, the B content is 0.01% or less.
  • the B content is preferably 0.005% or less.
  • the hot-formed steel plate member of the embodiment has a chemical composition composed of the above elements C to B, the remaining Fe and impurities.
  • impurities are components mixed in due to various factors in the manufacturing process, such as ores and scraps, when manufacturing steel sheets industrially, and are allowed within a range that does not adversely affect the embodiment. Means what will be done.
  • the hot-formed steel sheet member of the embodiment further contains one or more elements selected from the group consisting of Nb, Ni, Cu, Mo, V, and Ca in the amounts shown below. You may let them.
  • Nb 0 to 0.50% Nb suppresses recrystallization and forms fine carbides to suppress grain growth when heating a hot forming steel sheet to Ac 3 point or higher to be used for hot forming. Fine austenite grains It is an element which has the effect
  • Ni 0 to 2.0%
  • Ni is an element effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching, and therefore Ni may be contained as necessary. However, even if Ni is contained in excess of 2.0%, the effect is small, and the cost is unnecessarily increased. For this reason, when it contains Ni, the content shall be 2.0% or less.
  • the Ni content is preferably 1.5% or less. In order to obtain the above effect, the Ni content is preferably 0.01% or more, and more preferably 0.05% or more.
  • Cu 0 to 1.0%
  • Cu is an element effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching, and may be contained as necessary. However, even if Cu is contained exceeding 1.0%, the effect is small, and the cost is unnecessarily increased. For this reason, when it contains Cu, the content shall be 1.0% or less.
  • the Cu content is preferably 0.5% or less. In order to obtain the above effect, the Cu content is preferably 0.01% or more, and more preferably 0.03% or more.
  • Mo 0 to 1.0%
  • Mo is an element having an action of forming fine carbides to suppress grain growth and making austenite grains fine when heating a hot-forming steel sheet to Ac 3 or more to be used for hot forming. is there. It also has the effect of greatly improving the local deformability of the hot-formed steel sheet member. For this reason, you may contain Mo as needed. However, when the Mo content exceeds 1.0%, the effect is saturated and the cost is increased unnecessarily. Therefore, when it contains Mo, the content shall be 1.0% or less.
  • the Mo content is preferably 0.7% or less. To obtain the above effect, the Mo content is preferably 0.01% or more, and more preferably 0.04% or more.
  • V 0 to 1.0%
  • V is an element effective for enhancing the hardenability of the steel sheet and stably securing the strength after quenching, and may be contained as necessary. However, even if V is contained exceeding 1.0%, the effect is small, and the cost is unnecessarily increased. For this reason, when it contains V, the content shall be 1.0% or less.
  • the V content is preferably 0.08% or less. In order to obtain the above effect, the V content is preferably 0.01% or more, and more preferably 0.02% or more.
  • Ca 0 to 0.005%
  • Ca is an element that has the effect of reducing the inclusions in the steel and improving the local deformability after quenching, and thus may be included as necessary.
  • the content shall be 0.005% or less.
  • the Ca content is preferably 0.004% or less.
  • the Ca content is preferably 0.001% or more, and more preferably 0.002% or more.
  • (B) Metal structure in the embodiment, in order to improve local deformability, it is preferable to suppress variation in hardness in the metal structure after hot forming. When the difference in hardness in the structure becomes large, it becomes a starting point of voids. Therefore, it is preferable to suppress the mixture of low-temperature transformation structure such as hard martensite and bainite and soft ferrite structure as much as possible. Therefore, the hot-formed steel sheet member of the embodiment preferably has a metal structure mainly composed of a low-temperature transformation structure and a volume ratio of ferrite of 3% or less.
  • the metal structure mainly composed of a low temperature transformation structure means a metal structure in which the total volume ratio of martensite, tempered martensite and bainite is 50% or more.
  • the tempered martensite here means martensite in which martensite transformed during quenching is tempered by automatic tempering, and martensite that has undergone low temperature tempering such as a paint baking process after quenching.
  • the low temperature transformation structure in the metal structure is preferably 80% or more and more preferably 90% or more in volume ratio.
  • the retained austenite contained in the metal structure is preferably 10% or less by volume ratio.
  • MnS concentrates in the center as inclusions, and it becomes easy to form hard martensite, resulting in a difference in hardness from the surroundings and a deterioration in local deformability.
  • the value of ⁇ of the hot-formed steel sheet member is preferably set to 1.6 or less.
  • the value of ⁇ is more preferably 1.2 or less.
  • the segregation of Mn in the steel sheet is controlled mainly by the steel sheet composition, particularly the impurity content, and the conditions for continuous casting, and does not substantially change before and after hot rolling and hot forming. Therefore, the inclusions and segregation status of the hot-forming steel sheet are almost the same as the inclusions and segregation status of the hot-formed steel sheet member produced by hot forming. Since the value of ⁇ does not change greatly by hot forming, the value of ⁇ of the hot-formed steel sheet member is also reduced to 1.6 or less by setting the value of ⁇ of the hot-forming steel sheet to 1.6 or less. When the value of ⁇ is 1.2 or less, the value of ⁇ of the hot-formed steel sheet member can also be 1.2 or less.
  • the maximum Mn concentration at the center of the plate thickness is determined by the following method. Using an electronic probe microanalyzer (EPMA), line analysis is performed at the center of the plate thickness of the steel sheet, three measured values are selected in descending order from the analysis result, and the average value is calculated. In addition, the average Mn concentration at the 1/4 depth position of the plate thickness from the surface is determined by the following method. Similarly, using EPMA, analysis is performed at 10 positions at the 1/4 depth position of the steel sheet, and the average value is calculated.
  • EPMA electronic probe microanalyzer
  • the cleanliness value is more preferably 0.04% or less.
  • the value of the cleanliness of steel is obtained by calculating the area percentage occupied by the above-mentioned A-type, B-type and C-type inclusions.
  • the cleanness value of the hot-formed steel sheet member is also 0 by setting the cleanness value of the hot-formed steel sheet to 0.08% or less. 0.08% or less, and by setting it to 0.04% or less, the cleanliness value of the hot-formed steel sheet member can also be made 0.04% or less.
  • the cleanliness value of the hot-formed steel plate or hot-formed steel plate member is obtained by the following method.
  • test materials are cut out from five locations.
  • the plate thickness of the hot-formed steel plate or hot-formed steel plate member is t, 1 / 8t, 1 / 4t, 1 / 2t, 3 / 4t, 7 / 8t in the plate thickness direction of each test material
  • the cleanliness is investigated by point calculation. The numerical value having the largest cleanliness value (lowest cleanliness) at each plate thickness is taken as the cleanliness value of the specimen.
  • Average particle size of old ⁇ grains 10 ⁇ m or less
  • Local deformability is improved by reducing the old ⁇ particle size in the hot-formed steel sheet member.
  • voids are generated at the boundaries of the old ⁇ grain boundaries and the substructure within the grains.
  • the refinement of the old ⁇ grains suppresses the generation of voids and delays the connection. Deformability can be improved. If the average particle size of the former ⁇ exceeds 10 ⁇ m, this effect cannot be exhibited. Therefore, the average particle diameter of the old ⁇ grains in the hot-formed steel sheet member is 10 ⁇ m or less.
  • it is effective to lower the heating temperature, delay the dissolution of carbide during heating, and suppress the grain growth.
  • the average particle diameter of old ⁇ grains can be measured using a method defined by ISO643. That is, the number of crystal grains in the measurement visual field is measured, the average area of the crystal grains is obtained by dividing the area of the measurement visual field by the number of crystal grains, and the crystal grain diameter in the equivalent circle diameter is calculated. At that time, it is preferable to measure the number of grains at the boundary of the visual field as 1/2 and adjust the magnification so that the number of crystal grains is 200 or more. In order to improve accuracy, it is preferable to measure a plurality of visual fields.
  • Residual carbide 4 ⁇ 10 3 pieces / mm 2 or less
  • Residual carbide has an effect of suppressing ⁇ grain growth during heating and holding during hot forming by pinning. Therefore, it is desirable for residual carbides to be present during heating and holding. The smaller the residual carbide after hot forming, the better the hardenability and the higher the strength. Therefore, it is preferable that the number density of residual carbides can be reduced upon completion of heating and holding.
  • the number density of residual carbides present in the hot-formed steel plate member is preferably 4 ⁇ 10 3 pieces / mm 2 or less.
  • the high-strength hot-formed steel plate member according to the embodiment may have a plating layer on the surface for the purpose of improving corrosion resistance.
  • the plating layer may be an electroplating layer or a hot dipping layer.
  • Examples of the electroplating layer include electrogalvanizing, electro-Zn—Ni alloy plating, electro-Zn—Fe alloy plating and the like.
  • the hot dip galvanizing layer includes hot dip galvanizing, alloyed hot dip galvanizing, hot dip aluminum plating, hot dip Zn-Al alloy plating, hot dip Zn-Al-Mg alloy plating, hot dip Zn-Al-Mg-Si alloy plating, etc. Illustrated.
  • the amount of plating adhesion is not particularly limited, and may be adjusted within a general range.
  • a slab is produced by casting.
  • the heating temperature of the molten steel is set to 5 ° C. higher than the liquidus temperature of the steel, and the molten steel per unit time. It is desirable to limit the casting amount to 6 t / min or less.
  • the molten steel flow in the mold is fast, so that inclusions are easily trapped in the solidified shell and inclusions in the slab increase.
  • the molten steel heating temperature is less than 5 ° C higher than the liquidus temperature, the viscosity of the molten steel increases, and inclusions hardly float in the continuous casting machine, resulting in an increase in inclusions in the slab. Cleanliness is likely to deteriorate.
  • the molten steel heating temperature from the liquidus temperature of the molten steel is 5 ° C. or more and the molten steel casting amount per unit time is 6 t / min or less, inclusions are hardly brought into the slab. As a result, the amount of inclusions at the stage of producing the slab can be effectively reduced, and the steel plate cleanliness of 0.08% or less can be easily achieved.
  • the molten steel heating temperature is more preferably 8 ° C. or higher than the liquidus temperature, and the molten steel casting amount per unit time is more preferably 5 t / min or less.
  • the molten steel heating temperature 8 ° C. or more higher than the liquidus temperature and setting the molten steel casting amount per unit time to 5 t / min or less it becomes easy to make the cleanliness 0.04% or less. Therefore it is desirable.
  • the center segregation reduction treatment include a method of discharging molten steel enriched in Mn in an unsolidified layer before the slab is completely solidified.
  • molten steel enriched with Mn before complete solidification can be discharged.
  • the electromagnetic stirring treatment can be performed, for example, by applying a flow to the unsolidified molten steel at 250 to 1000 gauss, and the unsolidified layer reduction treatment, for example, reduces the final solidified portion with a gradient of about 1 mm / m. Can be done.
  • ⁇ ⁇ Soaking (soaking) treatment may be performed on the slab obtained by the above method as necessary.
  • a preferable soaking temperature is 1200 to 1300 ° C.
  • a soaking time is 20 to 50 hours.
  • hot rolling is performed on the slab.
  • the hot rolling start temperature is 1000 to 1300 ° C. and the hot rolling completion temperature is 850 ° C. or higher from the viewpoint of more uniformly generating carbides.
  • the coiling temperature is preferably higher from the viewpoint of workability, but if it is too high, the yield decreases due to scale formation, so it is preferably 500 to 650 ° C.
  • the hot-rolled steel sheet obtained by hot rolling is descaled by pickling or the like.
  • the hot-rolled steel sheet subjected to descaling treatment is annealed to obtain a hot-rolled annealed steel sheet and It is preferable to do.
  • the form of carbides existing in the steel sheet before hot forming and the concentration of elements in the carbides Degree is important. Although it is desirable that the carbide is finely dispersed, in that case, since the dissolution of the carbide is accelerated, the effect of suppressing grain growth cannot be expected. If elements such as Mn and Cr are concentrated in the carbide, the carbide is difficult to dissolve. For this reason, it is desirable that the form of carbide in the steel sheet before hot forming is finely dispersed and the concentration of elements in the carbide is high.
  • the form of carbide can be controlled by adjusting the annealing conditions after hot rolling. Specifically, it is preferable to perform annealing for 5 hours or less by setting the annealing temperature to Ac1 point or lower and Ac1 point to ⁇ 100 ° C. or higher.
  • the carbide When the coiling temperature after hot rolling is set to 550 ° C. or less, the carbide is easily finely dispersed. However, since the concentration level of the element in the carbide also decreases, the concentration of the element is advanced by annealing.
  • the coiling temperature is 550 ° C. or higher, pearlite is generated, and element concentration in the carbide in pearlite is progressing.
  • annealing is performed in order to divide the pearlite and disperse the carbide.
  • the hot-rolled annealed steel sheet, the cold-rolled steel sheet that has been cold-rolled to the hot-rolled annealed steel sheet, or the cold-rolled annealed steel that has been annealed A steel plate can be used. What is necessary is just to select a process process suitably according to the plate
  • Cold rolling may be performed using a normal method. From the viewpoint of ensuring good flatness, the rolling reduction in cold rolling is preferably 30% or more. On the other hand, in order to avoid an excessive load, the rolling reduction in cold rolling is preferably 80% or less.
  • annealing is preferably performed at an Ac1 point or less and for a time or less, preferably for 3 hours or less.
  • the hot-formed steel sheet member according to the embodiment may have a plating layer on the surface for the purpose of improving corrosion resistance or the like.
  • the plating layer is preferably formed on the steel plate before hot forming.
  • annealing may be performed prior to the plating process in the continuous hot dip galvanizing line, or only the plating process may be performed without performing annealing at a low heating holding temperature.
  • an alloying heat treatment may be performed after hot dip galvanization to form an alloyed hot dip galvanized steel sheet.
  • Zinc-based plating can also be applied by electroplating.
  • the zinc-based plating can be applied to at least a part of the surface of the steel material, but in the case of a steel plate, it is generally applied to the entire surface of one side or both sides.
  • a high-strength hot-formed steel plate member can be obtained by performing hot forming on the hot-formed steel plate.
  • the heating rate of the steel sheet during hot forming is preferably 20 ° C./sec or more from the viewpoint of suppressing grain growth. More preferably, it is 50 ° C./sec or more. It is desirable that the heating temperature of the steel sheet during hot forming exceeds Ac 3 point and is 1050 ° C. or lower. When the heating temperature is 3 points or less of Ac, the austenite single phase state is not obtained before hot forming, and ferrite, pearlite, or bainite remains in the steel sheet.
  • the metal structure is not mainly composed of martensite after hot forming, and the desired hardness may not be obtained. Further, not only the hardness variation of the hot-formed steel sheet member is increased, but also the local deformability is deteriorated.
  • the heating temperature of the steel sheet during hot forming is preferably 1050 ° C. or lower. Further, if the heating time is less than 1 min, the austenite single phase may be insufficient even when heated, and further, the carbide is not sufficiently dissolved. The number density of carbides increases. When it exceeds 10 minutes, austenite will coarsen and the local deformability of a hot-formed steel plate member may deteriorate. Accordingly, the heating time of the steel sheet during hot forming is desirably 1 to 10 minutes.
  • the hot forming start temperature is Ar 3 points or more. After hot forming, it is desirable to rapidly cool at a cooling rate of 10 ° C./sec or more, and it is more desirable to quench at a rate of 20 ° C./sec or more. There is no particular upper limit on the cooling rate.
  • the steel sheet member In order to obtain a hot-formed steel sheet member having a martensite-based metal structure with little hardness variation, it is desirable to rapidly cool the steel sheet until the surface temperature of the steel sheet is 350 ° C. or lower after hot forming.
  • the cooling end temperature is preferably 100 ° C. or lower, more preferably room temperature.
  • the obtained slab was hot rolled by a hot rolling tester to obtain a hot rolled steel sheet having a thickness of 3.0 mm. After winding, the hot rolled steel sheet was pickled and further annealed. Some of the steel sheets were further cold-rolled with a cold rolling tester to obtain cold-rolled steel sheets having a thickness of 1.5 mm. Further, some of the cold-rolled steel sheets were annealed at 600 ° C. for 2 hours to obtain cold-rolled annealed steel sheets.
  • hot pressing hatch forming
  • the hot-formed steel plate member 2 was obtained.
  • the steel sheet is heated in a heating furnace with changing the surface temperature between 820 ° C. and 1100 ° C., held at that temperature for 90 seconds, then removed from the heating furnace and immediately heated in a mold with a cooling device.
  • An intermediate press was performed, and a quenching treatment was performed simultaneously with molding. The following evaluation was performed about the said hot-formed steel plate member. The evaluation results are shown in Table 2.
  • hot rolled means a hot-rolled steel sheet having a thickness of 3.0 mm that has been hot-rolled
  • cold-rolled means a thickness that has been further cold-rolled to the hot-rolled steel sheet. This means a cold-rolled steel sheet having a thickness of 1.5 mm. * Means outside the scope of the embodiment.
  • Residual ⁇ volume fraction is obtained by chemically polishing an inner layer of 1/8 of the plate thickness from the surface of the steel sheet, and then by X-ray diffraction using a Mo tube.
  • the diffraction strength I ⁇ (200) of ferrite (200) and ferrite (211) It was obtained from the intensity ratio of the diffraction intensity I ⁇ (211) and the diffraction intensity I ⁇ (220) of (220) of austenite and the diffraction intensity I ⁇ (311) of (311).
  • V ⁇ (volume%) 0.25 ⁇ ⁇ I ⁇ (220) / (1.35 ⁇ I ⁇ (200) + I ⁇ (220)) + I ⁇ (220) / (0.69 ⁇ I ⁇ (211) + I ⁇ (220)) + I ⁇ (311) / (1.5 ⁇ I ⁇ (200) + I ⁇ (311)) + I ⁇ (311) / (0.69 ⁇ I ⁇ (211) + I ⁇ (311)) ⁇
  • ⁇ Measurement of Mn segregation degree ⁇ > In the central part of the thickness of the hot-formed steel sheet member, line analysis using EPMA is performed, and after selecting three measured values in order from the analysis result, the average value is calculated, and the maximum Mn at the central part of the thickness is calculated. The concentration was determined. In addition, at the 1/4 depth position of the sheet thickness from the surface of the hot-formed steel plate member, analysis is performed at 10 locations using EPMA, the average value is calculated, and the 1/4 depth position of the sheet thickness from the surface is calculated. The average Mn concentration was determined. And Mn segregation degree (alpha) was calculated
  • the average grain size of old ⁇ grains in hot-formed steel sheet members is the equivalent of a circle by measuring the number of crystal grains in the measurement field of view and dividing the area of the measurement field by the number of crystal grains to determine the average area of the crystal grains It calculated
  • the local deformability was measured by a notch tensile test.
  • the tensile test piece had a parallel part width of 16.5 mm and a parallel part length of 60 mm, and the rolling direction was taken as the longitudinal direction. Further, a V-notch having a depth of 2 mm was processed at the center of the length of the tensile test piece to obtain a notched tensile test piece. The thickness of the notch test piece was 1.4 mm.
  • the shape of the notch tensile test piece is shown in FIG.
  • a tensile test was performed using the above-described notched tensile test piece, and the notch elongation at the time of breaking at the V notch portion was measured to evaluate the local deformability.
  • the gauge distance was 5 mm, and the tensile speed (crosshead speed) during the tensile test was 0.5 mm / min.
  • test number 2 indicates that the composition of the steel satisfies the range of the embodiment, but the casting amount of molten steel per unit time is large. The deformability was inferior.
  • Test No. 3 since the center segregation reduction treatment and the soaking treatment were not carried out, the Mn segregation degree exceeded 1.6 and the local deformability was inferior.
  • Test No. 5 resulted in poor local deformability due to the cleanliness value exceeding 0.08% because the molten steel heating temperature was low. In Test No.
  • test No. 16 since the S content exceeded the upper limit of the range of the embodiment, the cleanliness value exceeded 0.08%, resulting in poor local deformability.
  • Test No. 17 since the Mn content exceeded the upper limit of the range of the embodiment, the Mn segregation degree exceeded 1.6 and the local deformability was inferior.
  • Test No. 18 where the Si content exceeds the upper limit of the range of the embodiments, A 3-point increases, the volume ratio of ferrite is more than 3% after hot forming, hardness less stable results It became.
  • Test No. 19 resulted in inferior local deformability because the C content exceeded the upper limit of the range of the embodiment.
  • Test No. 20 resulted in inferior hardness stability because the Cr content was lower than the range of the embodiment.
  • Test Nos. 1, 4, 7, 8, 10, 12, 13 and 15 satisfying the range of the embodiment resulted in excellent hardness stability and local deformability.

Landscapes

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

Abstract

　L'invention concerne un élément de plaque d'acier laminée à chaud présentant une composition chimique, en % en masse, de 0,08 à 0,16 % de C, de 0,19 % ou moins de Si, de 0,40 à 1,50 % de Mn, de 0,02 % ou moins de P, de 0,01 % ou moins de S, de 0,01 à 1,0 % d'Al sol., de 0,01 % ou moins de N, de 0,25 à 3,00 % de Cr, de 0,01 à 0,05 % de Ti, de 0,001 à 0,01 % de B, de 0 à 0,50 % de Nb, de 0 à 2,0 % de Ni, de 0 à 1,0 % de Cu, de 0 à 1,0 % de Mo, de 0 à 1,0 % de V et de 0 à 0,005 % de Ca, le reste étant du Fe et des impuretés inévitables, dans laquelle la fraction volumique totale de martensite, de martensite revenue et de bainite est de 50 % ou plus, la fraction volumique de ferrite est de 3 % ou moins, la grosseur moyenne de particule des grains γ antérieurs est de 10 µm ou moins et la densité numérique de carbures résiduels qui sont présents est de 4 × 103 par mm2 ou moins.
PCT/JP2015/064101 2014-05-15 2015-05-15 Élément de plaque d'acier laminée à chaud WO2015174530A1 (fr)

Priority Applications (8)

Application Number Priority Date Filing Date Title
JP2016519321A JP6315087B2 (ja) 2014-05-15 2015-05-15 熱間成形鋼板部材
ES15793575T ES2753390T3 (es) 2014-05-15 2015-05-15 Elemento de plancha de acero formado en caliente
CN201580024959.1A CN106661685B (zh) 2014-05-15 2015-05-15 热成形钢板构件
KR1020167033364A KR101908210B1 (ko) 2014-05-15 2015-05-15 열간 성형 강판 부재
PL15793575T PL3144405T3 (pl) 2014-05-15 2015-05-15 Element z blachy stalowej cienkiej formowanej na gorąco
EP15793575.0A EP3144405B1 (fr) 2014-05-15 2015-05-15 Élément de tôle d'acier formé à chaud
US15/311,117 US20170073792A1 (en) 2014-05-15 2015-05-15 Hot-formed steel sheet member
MX2016014884A MX2016014884A (es) 2014-05-15 2015-05-15 Elemento placa de acero laminada en caliente.

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2014-101443 2014-05-15
JP2014-101444 2014-05-15
JP2014101443 2014-05-15
JP2014101444 2014-05-15

Publications (1)

Publication Number Publication Date
WO2015174530A1 true WO2015174530A1 (fr) 2015-11-19

Family

ID=54480065

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2015/064101 WO2015174530A1 (fr) 2014-05-15 2015-05-15 Élément de plaque d'acier laminée à chaud

Country Status (10)

Country Link
US (1) US20170073792A1 (fr)
EP (1) EP3144405B1 (fr)
JP (1) JP6315087B2 (fr)
KR (1) KR101908210B1 (fr)
CN (1) CN106661685B (fr)
ES (1) ES2753390T3 (fr)
MX (1) MX2016014884A (fr)
PL (1) PL3144405T3 (fr)
TW (1) TWI563101B (fr)
WO (1) WO2015174530A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018062381A1 (fr) * 2016-09-28 2018-04-05 Ｊｆｅスチール株式会社 Tôle d'acier et son procédé de production
JP2020528963A (ja) * 2017-07-25 2020-10-01 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ 熱間成形された部品を製造するための鋼ストリップ、シート又はブランク、部品、及びブランクを部品に熱間成形する方法
JP2021523373A (ja) * 2018-05-10 2021-09-02 フンダシオ エウレカト 薄板試験片を作成するための装置

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3124637B9 (fr) * 2014-03-26 2019-12-04 Nippon Steel Corporation Élément de tôle d'acier formé à chaud à haute résistance
WO2017017484A1 (fr) * 2015-07-30 2017-02-02 Arcelormittal Procédé pour la fabrication d'une pièce durcie qui ne présente pas de problèmes lme (liquide metal embrittlement - fragilité par les métaux liquides)
EP3701057B1 (fr) * 2017-10-24 2021-12-01 ArcelorMittal Procédé de fabrication d'une tôle d'acier revêtue
CN111279007B (zh) 2017-10-24 2023-01-24 安赛乐米塔尔公司 用于制造镀锌扩散退火钢板的方法
MA50898A (fr) 2017-11-17 2021-04-07 Arcelormittal Procédé pour la fabrication d'une tôle d'acier revêtue de zinc résistant à la fragilisation par métal liquide
WO2020162513A1 (fr) * 2019-02-05 2020-08-13 日本製鉄株式会社 Élément en acier revêtu, tôle d'acier revêtue et procédés de production d'un tel élément et d'une telle tôle d'acier
WO2020204037A1 (fr) * 2019-04-01 2020-10-08 日本製鉄株式会社 Article moulé estampé à chaud, plaque d'acier pour estampage à chaud, et procédés de fabrication de ceux-ci
KR102604058B1 (ko) * 2019-05-31 2023-11-22 닛폰세이테츠 가부시키가이샤 핫 스탬프 성형체
KR102279900B1 (ko) * 2019-09-03 2021-07-22 주식회사 포스코 열간 성형용 강판, 열간 성형 부재 및 그 제조방법
EP4079913A4 (fr) * 2019-12-20 2023-02-22 Posco Acier pour formage à chaud, élément formé à chaud et procédés de fabrication associés

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006183139A (ja) * 2004-11-30 2006-07-13 Jfe Steel Kk 自動車用部材およびその製造方法
JP2007211276A (ja) * 2006-02-08 2007-08-23 Sumitomo Metal Ind Ltd 熱間プレス用めっき鋼板およびその製造方法ならびに熱間プレス成形部材の製造方法
JP2007314817A (ja) * 2006-05-23 2007-12-06 Sumitomo Metal Ind Ltd 熱間プレス用鋼板および熱間プレス鋼板部材ならびにそれらの製造方法
WO2009082091A1 (fr) * 2007-12-26 2009-07-02 Posco Tôle d'acier laminée à chaud ayant une propriété de formage à la presse à chaud supérieure et une résistance à la rupture par traction élevée, article formé utilisant la tôle d'acier et procédé pour fabriquer la tôle d'acier et l'article formé
WO2012157581A1 (fr) * 2011-05-13 2012-11-22 新日本製鐵株式会社 Article moulé estampé à chaud et son procédé de production, élément d'absorption d'énergie et son procédé de production
WO2013105631A1 (fr) * 2012-01-13 2013-07-18 新日鐵住金株式会社 Article moulé par estampage à chaud et son procédé de production

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101484601B (zh) * 2006-05-10 2012-07-25 住友金属工业株式会社 热挤压成形钢板构件及其制造方法
JP5910168B2 (ja) * 2011-09-15 2016-04-27 臼井国際産業株式会社 Ｔｒｉｐ型２相マルテンサイト鋼及びその製造方法とそのｔｒｉｐ型２相マルテンサイト鋼を用いた超高強度鋼製加工品
WO2013065346A1 (fr) * 2011-11-01 2013-05-10 Ｊｆｅスチール株式会社 Feuille d'acier laminée à chaud, de haute résistance, ayant d'excellentes caractéristiques de flexion et une excellente ténacité aux basses températures et son procédé de fabrication

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006183139A (ja) * 2004-11-30 2006-07-13 Jfe Steel Kk 自動車用部材およびその製造方法
JP2007211276A (ja) * 2006-02-08 2007-08-23 Sumitomo Metal Ind Ltd 熱間プレス用めっき鋼板およびその製造方法ならびに熱間プレス成形部材の製造方法
JP2007314817A (ja) * 2006-05-23 2007-12-06 Sumitomo Metal Ind Ltd 熱間プレス用鋼板および熱間プレス鋼板部材ならびにそれらの製造方法
WO2009082091A1 (fr) * 2007-12-26 2009-07-02 Posco Tôle d'acier laminée à chaud ayant une propriété de formage à la presse à chaud supérieure et une résistance à la rupture par traction élevée, article formé utilisant la tôle d'acier et procédé pour fabriquer la tôle d'acier et l'article formé
WO2012157581A1 (fr) * 2011-05-13 2012-11-22 新日本製鐵株式会社 Article moulé estampé à chaud et son procédé de production, élément d'absorption d'énergie et son procédé de production
WO2013105631A1 (fr) * 2012-01-13 2013-07-18 新日鐵住金株式会社 Article moulé par estampage à chaud et son procédé de production

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018062381A1 (fr) * 2016-09-28 2018-04-05 Ｊｆｅスチール株式会社 Tôle d'acier et son procédé de production
JP6388085B2 (ja) * 2016-09-28 2018-09-12 Ｊｆｅスチール株式会社 鋼板およびその製造方法
JPWO2018062381A1 (ja) * 2016-09-28 2018-09-27 Ｊｆｅスチール株式会社 鋼板およびその製造方法
US11268164B2 (en) 2016-09-28 2022-03-08 Jfe Steel Corporation Steel sheet and method for producing the same
JP2020528963A (ja) * 2017-07-25 2020-10-01 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ 熱間成形された部品を製造するための鋼ストリップ、シート又はブランク、部品、及びブランクを部品に熱間成形する方法
JP7326247B2 (ja) 2017-07-25 2023-08-15 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 熱間成形された部品を製造するための鋼ストリップ、シート又はブランク、部品、及びブランクを部品に熱間成形する方法
JP2021523373A (ja) * 2018-05-10 2021-09-02 フンダシオ エウレカト 薄板試験片を作成するための装置
JP7089065B2 (ja) 2018-05-10 2022-06-21 フンダシオ エウレカト 薄板試験片を作成するための装置

Also Published As

Publication number Publication date
MX2016014884A (es) 2017-03-07
ES2753390T3 (es) 2020-04-08
KR101908210B1 (ko) 2018-10-15
EP3144405A4 (fr) 2018-01-03
JPWO2015174530A1 (ja) 2017-04-27
TW201602360A (zh) 2016-01-16
US20170073792A1 (en) 2017-03-16
TWI563101B (en) 2016-12-21
KR20160147025A (ko) 2016-12-21
EP3144405A1 (fr) 2017-03-22
JP6315087B2 (ja) 2018-04-25
CN106661685A (zh) 2017-05-10
CN106661685B (zh) 2018-04-20
EP3144405B1 (fr) 2019-08-21
PL3144405T3 (pl) 2020-02-28

Similar Documents

Publication Publication Date Title
JP6237884B2 (ja) 高強度熱間成形鋼板部材
JP6315087B2 (ja) 熱間成形鋼板部材
US10501832B2 (en) Plated steel sheet
JP6380660B2 (ja) 熱処理鋼板部材およびその製造方法
JP4725415B2 (ja) 熱間プレス用鋼板および熱間プレス鋼板部材ならびにそれらの製造方法
KR102186320B1 (ko) 강판 및 도금 강판
JP6380659B2 (ja) 熱処理鋼板部材およびその製造方法
WO2019208556A1 (fr) Élément en acier et son procédé de production
TWI515310B (zh) 熱壓印成形體、冷軋鋼板、及熱壓印成形體之製造方法
JP5541428B1 (ja) 鋼板
KR101479391B1 (ko) 형상 동결성이 우수한 냉연 박강판 및 그 제조 방법
JP7160184B2 (ja) 鋼板及びその製造方法
WO2016163467A1 (fr) Tôle d'acier pour traitement thermique
JP6032173B2 (ja) 引張最大強度９８０ＭＰａを有する耐遅れ破壊特性に優れた高強度鋼板、高強度溶融亜鉛めっき鋼板、並びに、高強度合金化溶融亜鉛めっき鋼板
WO2020204027A1 (fr) Article moulé estampé à chaud, et procédé de fabrication de celui-ci

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 15793575

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2016519321

Country of ref document: JP

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 15311117

Country of ref document: US

Ref document number: MX/A/2016/014884

Country of ref document: MX

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: IDP00201608105

Country of ref document: ID

ENP Entry into the national phase

Ref document number: 20167033364

Country of ref document: KR

Kind code of ref document: A

REEP Request for entry into the european phase

Ref document number: 2015793575

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2015793575

Country of ref document: EP

REG Reference to national code

Ref country code: BR

Ref legal event code: B01A

Ref document number: 112016026692

Country of ref document: BR

ENP Entry into the national phase

Ref document number: 112016026692

Country of ref document: BR

Kind code of ref document: A2

Effective date: 20161114