WO2016152148A1 - 高強度鋼板およびその製造方法 - Google Patents

高強度鋼板およびその製造方法 Download PDF

Info

Publication number
WO2016152148A1
WO2016152148A1 PCT/JP2016/001651 JP2016001651W WO2016152148A1 WO 2016152148 A1 WO2016152148 A1 WO 2016152148A1 JP 2016001651 W JP2016001651 W JP 2016001651W WO 2016152148 A1 WO2016152148 A1 WO 2016152148A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
steel sheet
width direction
ferrite
center
Prior art date
Application number
PCT/JP2016/001651
Other languages
English (en)
French (fr)
Inventor
佑馬 本田
船川　義正
耕造 原田
Original Assignee
Ｊｆｅスチール株式会社
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=56979249&utm_source=***_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2016152148(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to EP16768054.5A priority Critical patent/EP3255168B1/en
Priority to MX2017012198A priority patent/MX2017012198A/es
Priority to US15/559,576 priority patent/US10494693B2/en
Priority to JP2016545379A priority patent/JP6052476B1/ja
Priority to KR1020177027030A priority patent/KR101989371B1/ko
Priority to CN201680018071.1A priority patent/CN107406947B/zh
Publication of WO2016152148A1 publication Critical patent/WO2016152148A1/ja

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • 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
    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
    • 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
    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
    • B32B15/043—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material of metal
    • 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
    • B32B15/18—Layered products comprising a layer of metal comprising iron or steel
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/26—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—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
    • C23C28/02—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 only coatings only including layers of metallic material
    • C23C28/023—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 only coatings only including layers of metallic material only coatings of metal elements only
    • C23C28/025—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 only coatings only including layers of metallic material only coatings of metal elements only with at least one zinc-based 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
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • 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
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • 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
    • C21D2211/009—Pearlite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12958—Next to Fe-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]

Definitions

  • the present invention relates to a high-strength steel plate applied to automobile parts and the like and a method for manufacturing the same.
  • High-strength steel sheets are widely used from the viewpoint of reducing the weight of the steel sheets used as materials for automobile members.
  • skeleton members and collision-resistant members are required to be difficult to deform at the time of collision in order to ensure the safety of passengers, and the yield ratio of steel plates that are used as these materials is required to be high.
  • the difference in tensile strength between the center and the end in the sheet width direction of the steel sheet is small.
  • Various steel sheets and manufacturing techniques thereof have been disclosed so far for the yield ratio requirement.
  • Patent Document 1 discloses a high-strength steel sheet excellent in paint bake hardenability containing Nb and Ti in total of 0.01% or more and having a recrystallization rate of 80% or more as a main phase and a method for producing the same.
  • Patent Document 2 discloses a high-strength steel sheet having 20-50% non-recrystallized ferrite as a steel structure and excellent in impact resistance and a method for producing the same.
  • the present invention has been made in order to solve the above-mentioned problems in view of such circumstances, and its purpose is to provide a high-strength steel sheet having a high yield ratio and a small strength difference between the center and the end in the width direction of the steel sheet. Is to get.
  • the present inventors conducted intensive research to solve the above problems.
  • the average crystal grain size of ferrite is refined below a certain level so that the difference in average crystal grain size between the center and the end of the steel sheet is reduced.
  • controlling the coiling temperature after hot rolling to an appropriate range was effective.
  • the present invention has been made based on the above findings, and the gist thereof is as follows.
  • Component composition is mass%, C: 0.02% or more and less than 0.10%, Si: less than 0.10%, Mn: less than 1.0%, P: 0.10% or less, S: 0.020% or less, Al: 0.01% or more and 0.10% or less, N: 0.010% or less, Nb: 0.005% or more and less than 0.070%, the balance being Fe and inevitable impurities
  • the steel structure is composed of ferrite: 90% or more in area ratio, pearlite: 0-10%, martensite, retained austenite and cementite: 0-3%, and the average crystal of the ferrite at the center in the width direction of the steel sheet
  • the particle diameter d C is 15.0 ⁇ m or less, and the difference between the average crystal grain diameter d E of the ferrite and the average crystal grain diameter d C at a position of 100 mm from the end in the steel sheet width direction to the center in the steel sheet width direction is 5.0 ⁇ m.
  • a high-strength steel sheet that is:
  • the component composition further includes, by mass%, Cr: 0.3% or less, Mo: 0.3% or less, B: 0.005% or less, Cu: 0.3% or less, Ni: 0.00.
  • the temperature at the center of the hot rolled steel sheet in the width direction of the steel sheet is 500 to 650 ° C.
  • the difference between the temperature and the temperature at the 100 mm position from the end in the width direction of the steel sheet to the center in the width direction of the steel sheet is wound at 50 ° C. or less, the hot-rolled steel sheet after winding is cold-rolled, and the cold-rolled steel sheet is subjected to a continuous annealing furnace A method for manufacturing high-strength steel sheets to be annealed.
  • the present invention by appropriately controlling the manufacturing conditions such as the component composition and the coiling conditions after hot rolling, the center and the end in the width direction of the steel sheet, while maintaining a high yield ratio required for automotive member applications.
  • the difference in tensile strength can be reduced.
  • the present invention it is possible to stably produce a high-strength steel plate. As a result, it is possible to further reduce the weight of automobiles and reduce yield loss due to press cracks, and the utility value of the present invention in the automobile and steel industries is extremely high.
  • the purpose of the present invention is to make the yield ratio as high as 0.70 or higher in a high strength steel plate having a tensile strength of 330 MPa or more and less than 500 MPa, and to reduce the difference in tensile strength between the center and the end in the width direction of the steel plate to 20 MPa or less. That is.
  • a component composition containing Nb of 0.005% or more, a ferrite single phase, or a steel structure mainly containing ferrite and containing at least one of pearlite, martensite, retained austenite and cementite in addition to ferrite It is effective to set the average crystal grain size of the ferrite at the center in the width direction of the steel sheet to 15.0 ⁇ m or less and the difference in the average crystal grain size of the ferrite between the center and the end in the width direction of the steel sheet to 5.0 ⁇ m or less.
  • the yield strength and the tensile strength are such that the tensile direction is perpendicular to the rolling direction from the position where the center of the parallel portion of the test piece coincides with the 100 mm position from the center in the width direction of the steel sheet to the center side in the width direction of the steel sheet.
  • a JIS No. 5 tensile test piece is collected and obtained by a tensile test based on JIS Z 2241.
  • Component composition of the high-strength steel sheet of the present invention is mass%, C: 0.02% or more and less than 0.10%, Si: less than 0.10%, Mn: less than 1.0%, P : 0.10% or less, S: 0.020% or less, Al: 0.01% or more and 0.10% or less, N: 0.010% or less, Nb: 0.005% or more and less than 0.070%
  • the balance consists of Fe and inevitable impurities.
  • the above component composition is further in mass%, Cr: 0.3% or less, Mo: 0.3% or less, B: 0.005% or less, Cu: 0.3% or less, Ni: 0.3 Any 1 type or 2 types or less of% or less may be contained.
  • C 0.02% or more and less than 0.10% C precipitates as Nb carbide (in this specification, Nb carbide includes Nb carbonitride) and suppresses precipitation strengthening and coarsening of ferrite grains. This contributes to an increase in yield strength and tensile strength. If the C content is less than 0.02%, the precipitation amount of Nb carbide decreases, so that the intended tensile strength of the present invention cannot be obtained. When the C content is 0.10% or more, the ferrite grain size becomes coarse due to the coarsening of Nb carbides, and pearlite and martensite are excessively generated, so the yield ratio decreases to less than 0.70. To do. For this reason, C content shall be 0.02% or more and less than 0.10%. Preferably it is 0.02% or more. Preferably it is 0.06% or less.
  • Si Less than 0.10% Si is generally effective in increasing the yield strength and tensile strength by solid solution strengthening of ferrite. However, if Si is contained, the work hardening ability is remarkably improved, so that the increase in tensile strength is larger than the yield strength, so that the yield ratio is lowered and the surface properties are also deteriorated. For this reason, the smaller the Si content, the better. In the present invention, the Si content is less than 0.10%. In principle, the Si content may be 0%, but is industrially often contained by 0.001% or more.
  • Mn Less than 1.0% By containing Mn, yield strength and tensile strength increase due to solid solution strengthening of ferrite.
  • Mn content is 1.0% or more, casting segregation causes a difference in the ferrite transformation start temperature after hot rolling between the Mn enriched part and the diluted part, resulting in a difference in the precipitation temperature of the Nb carbide.
  • the average crystal grain size of the ferrite after annealing becomes non-uniform, and the difference in tensile strength between the center in the width direction of the steel sheet and the end exceeds 20 MPa. Therefore, the Mn content is less than 1.0%. Preferably it is 0.2% or more. Preferably it is 0.8% or less.
  • P 0.10% or less
  • yield strength and tensile strength increase due to solid solution strengthening of ferrite.
  • the P content exceeds 0.10%, the tensile strength locally increases due to segregation of casting and segregation of ferrite grain boundaries, so the difference in tensile strength between the center in the width direction of the steel sheet and the end is increased.
  • the P content is 0.10% or less.
  • the P content may be 0%, but is preferably 0.01% or more and 0.04% or less.
  • S 0.020% or less
  • S is an element unavoidably included in the component composition as an impurity.
  • the yield strength and the tensile strength are reduced by decreasing the solid solution Mn due to the formation of MnS and the like, and the crack at the time of press forming is promoted by the decrease in ductility.
  • the upper limit of S content is 0.020%.
  • the content is 0.015% or less.
  • the S content may be 0%, but industrially, the content is often 0.0001% or more.
  • Al 0.01% or more and 0.10% or less Al is added to deoxidize and fix solute N as AlN in the refining process.
  • the Al content needs to be 0.01% or more.
  • the Al content is 0.01% or more and 0.10% or less.
  • it is 0.01% or more.
  • it is 0.07% or less. More preferably, it is 0.06% or less.
  • N 0.010% or less N is an element inevitably contained until the hot metal refining process. If the N content exceeds 0.010%, coarse Nb carbide precipitates during casting, and then the Nb carbide does not dissolve even by slab heating, leading to coarsening of ferrite average crystal grains. Therefore, the N content is 0.010% or less. In principle, the N content may be 0%, but is industrially often contained in an amount of 0.0001% or more.
  • Nb 0.005% or more and less than 0.070%
  • Nb is an important element contributing to refinement of ferrite average crystal grains and an increase in yield ratio due to precipitation of Nb carbides. This effect is small when the Nb content is less than 0.005%.
  • the Nb content is 0.070% or more, Nb carbide is excessively precipitated and unrecrystallized ferrite remains even after annealing, which causes an increase in the difference in tensile strength between the center in the width direction of the steel sheet and the end. Therefore, the Nb content is 0.005% or more and less than 0.070%. Preferably it is 0.010% or more. Preferably it is 0.040% or less.
  • the high strength steel sheet of the present invention can contain the following components as optional components.
  • Cr 0.3% or less Cr may be contained as a trace element that does not impair the effects of the present invention. If the Cr content exceeds 0.3%, the martensite may be excessively generated due to the improvement of the hardenability, and the yield ratio may be lowered. Therefore, when adding Cr, Cr content shall be 0.3% or less.
  • Mo 0.3% or less Mo may be contained as a trace element that does not impair the effects of the present invention. However, if the Mo content exceeds 0.3%, martensite may be generated excessively due to the improvement of hardenability, which may lead to a decrease in yield ratio. Therefore, when Mo is added, the Mo content is 0.3% or less.
  • B 0.005% or less B may be contained as a trace element that does not impair the effects of the present invention. However, if the B content exceeds 0.005%, martensite may be generated excessively due to the improvement of hardenability, leading to a decrease in yield ratio. Therefore, when adding B, B content shall be 0.005% or less.
  • Cu 0.3% or less Cu may be contained as a trace element that does not impair the effects of the present invention. However, if the Cu content exceeds 0.3%, martensite may be generated excessively due to the improvement of hardenability, which may lead to a decrease in yield ratio. Therefore, when adding Cu, Cu content shall be 0.3% or less.
  • Ni 0.3% or less Ni may be contained as a trace element that does not impair the effects of the present invention. However, if the Ni content exceeds 0.3%, martensite may be generated excessively due to the improvement of hardenability, leading to a decrease in yield ratio. Therefore, when Ni is added, the Ni content is 0.3% or less.
  • the remainder other than the above is Fe and inevitable impurities.
  • elements such as Ti, V, Sn, Sb, Co, W, Ca, Na, and Mg are contained as inevitable impurities within a minute range that does not impair the effects of the present invention. May be.
  • the steel structure of the high-strength steel sheet of the present invention consists of ferrite: 90% or more, pearlite: 0-10%, martensite, retained austenite, and cementite: 0-3%. Further, the average crystal grain size d C of ferrite at the center in the width direction of the steel sheet is 15.0 ⁇ m or less, the average crystal grain diameter d E of ferrite at the position of 100 mm from the end in the width direction of the steel sheet to the center side in the width direction of the steel sheet and the above average crystal The difference in particle size d C is 5.0 ⁇ m or less.
  • Ferrite 90% or more Ferrite has good ductility and is the main phase of the steel structure of the present invention, and its content is 90% or more in terms of area ratio. If the ferrite content is less than 90% by area ratio, a yield ratio of 0.70 or more cannot be obtained. Therefore, the ferrite content is 90% or more in terms of area ratio. Preferably, it is 95% or more.
  • the steel structure of the present invention may be a ferrite single phase (the ferrite content is 100% in area ratio).
  • Pearlite is effective for obtaining desired yield strength and tensile strength. However, when the pearlite content exceeds 10% by area ratio, a yield ratio of 0.70 or more cannot be obtained.
  • the pearlite content is 0 to 10% in terms of area ratio. Preferably, the content is 0 to 5%.
  • the steel structure of the high-strength steel sheet of the present invention can contain 0 to 3% of martensite, retained austenite and cementite in addition to ferrite and pearlite.
  • a yield ratio of 0.70 or more cannot be obtained. Therefore, the total of martensite, retained austenite and cementite is 0 to 3% in terms of area ratio.
  • Average crystal grain size d C of ferrite at the center in the width direction of the steel sheet 15.0 ⁇ m or less
  • the average crystal grain size of ferrite is important for obtaining a high yield ratio of 0.70 or more, which is the object of the present invention.
  • the average crystal grain size of ferrite at the center in the width direction of the steel sheet is 15.0 ⁇ m or less. Preferably it is 10.0 ⁇ m or less.
  • the lower limit of the average ferrite grain size is not particularly limited, but if it is less than 1.0 ⁇ m, the tensile strength and yield strength increase excessively, which may lead to stretch flangeability and elongation deterioration. It is preferably 1.0 ⁇ m or more.
  • the difference in diameter is that the difference in tensile strength between the center in the width direction of the steel sheet and the end (100 mm position from the edge in the width direction of the steel sheet to the center in the width direction of the steel sheet) is 20 MPa or less. The smaller the difference, the better.
  • the ferrite average crystal grain size difference between the center in the width direction of the steel plate and the end exceeds 5.0 ⁇ m, the difference in tensile strength exceeds 20 MPa, and the high strength steel plate intended by the present invention cannot be obtained. Therefore, the ferrite average crystal grain size difference is set to 5.0 ⁇ m or less. Further, it is preferably 3.0 ⁇ m or less.
  • the lower limit of the difference is not particularly limited, but to make it less than 1.0 ⁇ m, a large capital investment is required to make the temperature distribution in the width direction during hot rolling and annealing uniform. For this reason, it is preferably 1.0 ⁇ m or more.
  • the area ratio of each structure was observed by SEM in the range of the plate thickness 1/8 to 3/8 from the surface of the plate thickness direction cross section in the cross section perpendicular to the rolling width direction, centering on the position of the plate thickness 1/4. Obtained by the point counting method described in ASTM E 562-05.
  • the average crystal grain size of ferrite is the center and end of the steel sheet in the width direction in the range of the thickness 1/8 to 3/8 centered on the position of the thickness 1/4 from the surface of the cross section in the thickness direction.
  • To 100 mm position in the center in the width direction of the steel sheet) is observed by SEM, and the equivalent circle diameter is calculated from the observation area and the number of crystal grains.
  • the width of the coil of the target steel sheet is 800 to 1700 mm.
  • the high-strength steel sheet of the present invention melts steel having the above component composition, manufactures a slab (steel piece) by casting, performs hot rolling and cold rolling, and then anneals in a continuous annealing furnace. It is manufactured by. Pickling may be performed after hot rolling.
  • the temperature means the surface temperature.
  • the casting method is not particularly limited, and casting may be performed by either the ingot casting method or the continuous casting method as long as the segregation of the significant component composition and the unevenness of the structure do not occur.
  • a high-temperature cast slab may be rolled as it is, or a slab cooled to room temperature may be reheated and then rolled. If there is a surface defect such as a crack at the time of the slab, the slab can be treated with a grinder. When the slab is reheated, it is preferably heated to 1100 ° C. or higher in order to dissolve the Nb carbide.
  • the slab is subjected to rough rolling and finish rolling. Thereafter, the hot rolled steel sheet is wound into a hot rolled coil.
  • the rough rolling conditions in the hot rolling are not particularly limited, and may be performed according to a conventional method.
  • the finish rolling conditions are not particularly limited, and may be carried out in accordance with a conventional method.
  • finishing rolling temperature shall be Ar3 point or more.
  • the coiling temperature is important in the production conditions for the high-strength steel sheet of the present invention.
  • Winding temperature 500-650 ° C
  • the coiling temperature is an important production condition for controlling the ferrite grain size after annealing to 15.0 ⁇ m or less by the precipitation amount of Nb carbide and the precipitate diameter. If the coiling temperature is less than 500 ° C. at the center in the width direction of the steel sheet, Nb carbides do not sufficiently precipitate during cooling after winding, and precipitate in a relatively short time during annealing heating and soaking. For this reason, the precipitate diameter becomes non-uniform, and the difference in tensile strength between the center in the width direction and the end in the width direction increases due to particle size variation.
  • the coiling temperature exceeds 650 ° C.
  • the Nb carbide precipitate diameter becomes excessively large and the ferrite average crystal grain diameter becomes coarse, so that a yield ratio of 0.70 or more cannot be obtained. Therefore, the coiling temperature is 500 to 650 ° C.
  • the temperature is preferably 550 to 630 ° C.
  • the temperature difference (coiling temperature difference) with respect to the center in the width direction is to control the ferrite average crystal grain size difference after annealing to 5.0 ⁇ m or less by the precipitation amount of Nb carbide and the precipitate diameter.
  • the manufacturing conditions are important, and the smaller the difference, the better.
  • the temperature difference exceeds 50 ° C. the difference between the precipitation amount of Nb carbide and the precipitate diameter becomes significant, and the average grain size difference after annealing exceeds 5.0 ⁇ m.
  • the winding temperature difference is set to 50 ° C. or less.
  • the temperature is preferably 30 ° C. or lower.
  • a method of heating the vicinity of the end in the width direction of the steel sheet using an edge heater or the like or adjusting the cooling amount by edge masking may be employed.
  • the heating method is not particularly limited, and can be performed by direct heating or induction heating.
  • the lower limit of the difference is not particularly limited. However, in order to make it lower than 5 ° C., a large amount of capital investment such as adding an edge heater is required immediately before winding, so that it is preferably 5 ° C. or higher.
  • Cold rolling may be performed according to a conventional method, and the rolling rate is preferably 30 to 80%.
  • annealing is performed using a continuous annealing furnace.
  • the heating rate during annealing is not particularly limited, but is preferably 0.1 to 30.0 ° C./s from the viewpoint of production efficiency and equipment investment.
  • the heating method is not particularly limited, and can be performed by a radiant tube method or a direct fire heating method.
  • the conditions of soaking temperature and time are preferably set so that the soaking temperature is 700 to 900 ° C. and the soaking time is maintained for 1 second or longer.
  • the upper limit of the holding time (soaking time) is not particularly limited, but if the holding time is too long, the Nb carbides are coarsened, so the holding time is preferably 300 seconds or less.
  • the cooling conditions after the soaking are not particularly limited.
  • the cooling stop temperature is 400 to 500 ° C.
  • the average cooling rate is 30 ° C./s or less
  • the holding time is 10 to 100 seconds in the temperature range of 400 to 500 ° C. Can be mentioned.
  • the surface of the high strength steel plate obtained by the above method can be plated.
  • the plating hot dip galvanizing immersed in a hot dip galvanizing bath is suitable.
  • An alloyed hot-dip galvanized layer can be formed by subjecting the hot-dip galvanized layer to an alloying treatment.
  • the alloying treatment is performed, if the holding temperature is less than 450 ° C., alloying does not proceed sufficiently and the plating adhesion and corrosion resistance deteriorate. Further, when the holding temperature exceeds 560 ° C., alloying proceeds excessively and problems such as powdering occur during pressing. Therefore, the holding temperature is preferably 450 to 560 ° C. Further, if the holding time is less than 5 seconds, alloying does not proceed sufficiently and the plating adhesion and corrosion resistance deteriorate, so the holding time is preferably 5 seconds or more.
  • temper rolling with an elongation of 0.1 to 5.0% may be performed as necessary.
  • the high-strength steel sheet targeted by the present invention can be obtained.
  • the characteristics intended by the present invention can be achieved even if surface treatment such as electrogalvanization, chemical conversion treatment, or organic coating treatment is applied. Will not be damaged.
  • hot dip galvanization or alloyed hot dip galvanization was performed using CGL (continuous galvanizing / galvannealing line).
  • CGL continuous galvanizing / galvannealing line.
  • an alloying treatment was performed by holding at 510 ° C. for 10 seconds.
  • the obtained high-strength steel sheet was subjected to steel structure observation and a tensile test.
  • the area ratio of the steel structure is 1000 times the range of the plate thickness 1/8 to 3/8 centered at the 1/4 thickness position from the surface of the cross section in the plate thickness direction in the cross section perpendicular to the rolling width direction. Enlarged and obtained by the point counting method described in ASTM E 562-05.
  • the average crystal grain size of ferrite is the center in the width direction of the steel sheet in the range of the plate thickness 1/8 to 3/8 from the surface of the cross section in the plate thickness direction in the cross section perpendicular to the rolling width direction.
  • the end 100 mm position from the end in the width direction of the steel plate to the center in the width direction of the steel plate) was enlarged 1000 times by SEM, and the equivalent circle diameter was calculated from the area and the number of crystal grains.
  • ⁇ is ferrite
  • P pearlite
  • M martensite
  • ⁇ grain size is the ferrite average crystal grain size in the center of the steel sheet width direction
  • ⁇ grain size difference is between the center and the end of the steel sheet width direction. It means the difference in ferrite average crystal grain size.
  • Yield strength and tensile strength are such that the tensile direction is perpendicular to the rolling direction from the position where the center of the parallel part of the test piece coincides with the position of the steel sheet width direction center or the width direction end to the steel sheet width direction center side.
  • a JIS No. 5 tensile test piece was collected and obtained by a tensile test in accordance with JIS Z 2241.
  • the tensile strength (TS) is 330 MPa or more and less than 500 MPa
  • the yield ratio (YR) is 0.70 or more
  • TS difference difference in tensile strength
  • TS difference difference in tensile strength
  • Table 2 shows the observation results and tensile test results of the steel structure.
  • No. 1 to 3, 6, 8 to 9, 12 to 15 and 18 satisfy all the requirements of the present invention, so that the high yield strength of the present invention is high and the difference in tensile strength in the width direction of the steel sheet is small. A steel plate is obtained.
  • no. Nos. 4 to 5, 7, 10 to 11, 16 to 17, and 19 to 21 have steel components or production conditions outside the scope of the present invention, and a desired steel structure is not obtained. A steel plate is not obtained.
  • the high-strength steel sheet of the present invention is suitable for a field where a high yield ratio is required centering on automobile inner plate parts and the like.

Landscapes

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

Abstract

　降伏比が高く、鋼板幅方向中央と端部との強度差が小さい高強度鋼板を得る。成分組成は、質量％で、Ｃ：０．０２％以上０．１０％未満、Ｓｉ：０．１０％未満、Ｍｎ：１．０％未満、Ｐ：０．１０％以下、Ｓ：０．０２０％以下、Ａｌ：０．０１％以上０．１０％以下、Ｎ：０．０１０％以下、Ｎｂ：０．００５％以上０．０７０％未満を含有し、残部がＦｅおよび不可避的不純物からなり、鋼組織は、面積率でフェライト：９０％以上、パーライト：０～１０％、マルテンサイト、残留オーステナイトおよびセメンタイトの合計：０～３％からなり、鋼板幅方向中央における上記フェライトの平均結晶粒径ｄＣが１５．０μｍ以下であり、鋼板幅方向端から鋼板幅方向中央側に１００ｍｍの位置における上記フェライトの平均結晶粒径ｄＥと上記平均結晶粒径ｄＣの差の絶対値が５．０μｍ以下である高強度鋼板とする。

Description

高強度鋼板およびその製造方法
　本発明は、自動車部品等に適用される高強度鋼板およびその製造方法に関する。
　自動車部材の素材となる鋼板として、部材軽量化などの観点から、高強度鋼板が広く用いられる。例えば、骨格部材や耐衝突用部材などは、乗員の安全確保のため衝突時に変形しにくいことが求められ、これらの素材となる鋼板の降伏比は高いことが要求される。一方、割れが発生することなく安定的にプレス成形するには、鋼板の板幅方向における中央と端部との引張強さの差が小さいことも望まれる。降伏比の要求に対しては、これまでに種々の鋼板およびその製造技術が開示されている。
　特許文献１には、Ｎｂ、Ｔｉを合計で０．０１％以上含有し、再結晶率８０％以上のフェライトを主相とする塗装焼付硬化性に優れた高強度鋼板とその製造方法が開示されている。また、特許文献２には、鋼組織として２０～５０％の未再結晶フェライトを含む、耐衝突特性に優れた高強度鋼板とその製造方法が開示されている。
特許第４７４００９９号公報 特許第４９９５１０９号公報
　特許文献１または２に記載の技術では、熱間圧延後の鋼板幅方向の巻取温度を適正に制御しておらず、その結果、鋼板板幅方向のフェライト粒径の均一性が不十分と考えられる。したがって、特許文献１または２に記載の技術では、板幅方向の中央と端の引張強さの差が小さい高強度鋼板は得られないと考えられる。また、特許文献２のように、熱間圧延後の鋼組織の一部に未再結晶フェライトを生成させる場合に、鋼板の幅方向中央と端部との引張強さの差が小さい高強度鋼板を得るには、焼鈍において板幅方向の温度を極めて厳密に管理する必要がある。このため、特許文献２に記載の発明による板幅方向の強度差が小さい鋼板の工業化は実質的に不可能である。
　本発明は、このような事情を鑑みて上記問題を解決するためになされたものであり、その目的は、降伏比が高く、鋼板幅方向中央と端部との強度差が小さい高強度鋼板を得ることである。
　本発明者らは、上記の課題を解決すべく鋭意研究を実施した。その結果、フェライトを主体とする鋼組織において、フェライトの平均結晶粒径を一定以下に微細化し、鋼板の幅中央と端部とで平均結晶粒径の差が小さくなるようにすることが、上記課題解決のために重要であることを見出した。そして、所望の鋼組織とするためには、所定の成分組成に調整するとともに、熱間圧延後の巻取温度を適正な範囲に制御することが有効であることを見出した。
　本発明は、以上の知見に基づきなされたもので、その要旨は以下のとおりである。
　［１］成分組成は、質量％で、Ｃ：０．０２％以上０．１０％未満、Ｓｉ：０．１０％未満、Ｍｎ：１．０％未満、Ｐ：０．１０％以下、Ｓ：０．０２０％以下、Ａｌ：０．０１％以上０．１０％以下、Ｎ：０．０１０％以下、Ｎｂ：０．００５％以上０．０７０％未満を含有し、残部がＦｅおよび不可避的不純物からなり、鋼組織は、面積率でフェライト：９０％以上、パーライト：０～１０％、マルテンサイト、残留オーステナイトおよびセメンタイトの合計：０～３％からなり、鋼板幅方向中央における前記フェライトの平均結晶粒径ｄＣが１５．０μｍ以下であり、鋼板幅方向端から鋼板幅方向中央側に１００ｍｍの位置における前記フェライトの平均結晶粒径ｄＥと前記平均結晶粒径ｄＣの差が５．０μｍ以下である高強度鋼板。
　［２］前記成分組成は、さらに、質量％で、Ｃｒ：０．３％以下、Ｍｏ：０．３％以下、Ｂ：０．００５％以下、Ｃｕ：０．３％以下、Ｎｉ：０．３％以下のいずれか１種または２種以上を含有する［１］に記載の高強度鋼板。
　［３］高強度鋼板の表面に溶融亜鉛めっき層を有する［１］または［２］に記載の高強度鋼板。
　［４］前記溶融亜鉛めっき層が合金化溶融亜鉛めっき層である［３］に記載の高強度鋼板。
　［５］［１］または［２］に記載の成分組成を有する鋼片を熱間圧延後、熱延鋼板の鋼板幅方向中央における温度が５００～６５０℃、巻取時の鋼板幅方向中央の温度と鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置の温度との差を５０℃以下として巻取り、巻取後の前記熱延鋼板を冷間圧延し、冷延鋼板を連続焼鈍炉で焼鈍する高強度鋼板の製造方法。
　［６］前記焼鈍後において、高強度鋼板の表面に溶融亜鉛めっきを施す［５］に記載の高強度鋼板の製造方法。
　［７］前記溶融亜鉛めっきに合金化処理を施す［６］に記載の高強度鋼板の製造方法。
　本発明によれば、成分組成および熱延後の巻取条件などの製造条件を適正に制御することにより、自動車部材用途として要求される高降伏比としつつ、鋼板幅方向の中央と端部との引張強さの差を小さくできる。
　さらに、本発明によれば、高強度鋼板を安定して製造することが可能である。この結果、自動車の更なる軽量化やプレス割れによる歩留まりロスの低減が可能になり、本発明の自動車、鉄鋼業界における利用価値は極めて大きい。
　以下、本発明の実施形態について説明する。なお、本発明は以下の実施形態に限定されない。以下の説明において、成分の含有量を表す「％」は「質量％」を意味する。
　先ず、本発明の概要について説明する。本発明の目的は引張強さが３３０ＭＰａ以上５００ＭＰａ未満の高強度鋼板において、降伏比を０．７０以上と高く、鋼板幅方向の中央と端部との引張強さの差を２０ＭＰａ以下と小さくすることである。そのためには、Ｎｂを０．００５％以上含有する成分組成とし、フェライト単相、またはフェライトを主体としフェライト以外にパーライト、マルテンサイト、残留オーステナイトおよびセメンタイトのいずれか１種以上を含む鋼組織とし、鋼板幅方向中央における該フェライトの平均結晶粒径を１５．０μｍ以下とし、鋼板幅方向中央と端部とのフェライトの平均結晶粒径の差を５．０μｍ以下とすることが有効である。
　また、所望のフェライト平均結晶粒径とするためには、熱延後の巻取温度を５００～６５０℃に管理し、巻取時の板幅方向の温度を均一にすることが重要である。具体的には鋼板幅方向中央と端部との温度差を５０℃以下にすることが重要である。これにより、Ｎｂ炭化物を熱延巻取後の冷却中に均一微細に析出させることができ、焼鈍後のフェライト平均結晶粒径を鋼板幅方向中央と端部とで均一化できると考えられる。
　なお、降伏強さと引張強さは、試験片の平行部中央が、鋼板幅方向中央または幅方向端から鋼板幅方向中央側に１００ｍｍ位置に一致する位置から、引張方向が圧延方向と垂直になるようＪＩＳ５号引張試験片を採取し、ＪＩＳ　Ｚ　２２４１に準拠した引張試験により求める。
　次いで、本発明の高強度鋼板について、成分組成、鋼組織の順で説明する。
　（１）成分組成
　本発明の高強度鋼板の成分組成は、質量％で、Ｃ：０．０２％以上０．１０％未満、Ｓｉ：０．１０％未満、Ｍｎ：１．０％未満、Ｐ：０．１０％以下、Ｓ：０．０２０％以下、Ａｌ：０．０１％以上０．１０％以下、Ｎ：０．０１０％以下、Ｎｂ：０．００５％以上０．０７０％未満を含有し、残部がＦｅおよび不可避的不純物からなる。また、上記成分組成は、さらに、質量％で、Ｃｒ：０．３％以下、Ｍｏ：０．３％以下、Ｂ：０．００５％以下、Ｃｕ：０．３％以下、Ｎｉ：０．３％以下のいずれか１種または２種以上を含有してもよい。
　Ｃ：０．０２％以上０．１０％未満
　Ｃは、Ｎｂ炭化物（本明細書においてＮｂ炭化物には、Ｎｂ炭窒化物も含む。）として析出し、析出強化やフェライト粒の粗大化を抑制することを通じて降伏強さと引張強さの増加に寄与する。Ｃ含有量が０．０２％未満ではＮｂ炭化物の析出量が減少するため、本発明が目的とする引張強さが得られない。Ｃ含有量が０．１０％以上になるとＮｂ炭化物の粗大化に起因してフェライト粒径が粗大化したり、パーライト、マルテンサイトが過度に生成したりするために降伏比が０．７０未満に低下する。このため、Ｃ含有量は０．０２％以上０．１０％未満とする。好ましくは０．０２％以上である。好ましくは０．０６％以下である。
　Ｓｉ：０．１０％未満
　Ｓｉは一般にフェライトの固溶強化により降伏強さと引張強さを増加させるのに有効である。しかし、Ｓｉを含有すると、加工硬化能の顕著な向上により、降伏強さに比べて引張強さの増加量が大きいため降伏比の低下を招き、表面性状も劣化させる。このため、Ｓｉ含有量は少ないほど好ましく、本発明では０．１０％未満とする。原理上Ｓｉ含有量は０％でもよいが、工業的には０．００１％以上含有されることが多い。
　Ｍｎ：１．０％未満
　Ｍｎの含有によって、フェライトの固溶強化で降伏強さと引張強さが増加する。Ｍｎ含有量が１．０％以上となると鋳造偏析によりＭｎの濃化部と希薄部で熱延後のフェライト変態開始温度に差が生じ、Ｎｂ炭化物の析出温度に差が生じる。その結果、焼鈍後のフェライトの平均結晶粒径が不均一になり、鋼板幅方向中央と端部との引張強さの差が２０ＭＰａを超える。このためＭｎ含有量は１．０％未満とする。好ましくは０．２％以上である。好ましくは０．８％以下である。
　Ｐ：０．１０％以下
　Ｐを含有することによって、フェライトの固溶強化で降伏強さと引張強さが増加する。しかし、Ｐ含有量が０．１０％を超えると、鋳造偏析やフェライト粒界偏析により局所的に引張強さが増加するため、鋼板幅方向中央と端部との引張強さの差の増大を招く。このためＰ含有量は０．１０％以下とする。原理上Ｐ含有量は０％でもよいが、好ましくは０．０１％以上０．０４％以下とする。
　Ｓ：０．０２０％以下
　Ｓは不純物として不可避的に成分組成に含まれる元素である。Ｓが含まれると、ＭｎＳの形成などにより固溶Ｍｎが減少することで降伏強さや引張強さが低下したり、延性の低下によりプレス成形時の割れを助長したりする。このため、Ｓ含有量をできるだけ低減することが好ましく、Ｓ含有量の上限は０．０２０％とする。好ましくは０．０１５％以下とする。原理上Ｓ含有量は０％でもよいが、工業的には０．０００１％以上含有されることが多い。
　Ａｌ：０．０１％以上０．１０％以下
　Ａｌは精錬工程で脱酸および固溶ＮをＡｌＮとして固定させるために添加される。十分な効果を得るには、Ａｌ含有量を０．０１％以上にする必要がある。しかしながら、Ａｌ含有量が０．１０％を超えるとＡｌＮの析出量と粒子径が鋼板幅方向で不均一になり、鋼板幅方向中央と端部とのフェライト平均結晶粒径差が大きくなる。そこで、Ａｌ含有量は０．０１％以上０．１０％以下とする。好ましくは０．０１％以上である。好ましくは０．０７％以下である。さらに好ましくは０．０６％以下である。
　Ｎ：０．０１０％以下
　Ｎは溶銑の精錬工程までに不可避的に含有される元素である。Ｎ含有量が０．０１０％を超えると、鋳造時に粗大なＮｂ炭化物が析出し、その後、スラブ加熱でもＮｂ炭化物が溶解せず、フェライト平均結晶粒の粗大化を招く。よってＮ含有量は０．０１０％以下とする。原理上Ｎ含有量は０％でもよいが、工業的には０．０００１％以上含有されることが多い。
　Ｎｂ：０．００５％以上０．０７０％未満
　Ｎｂはフェライト平均結晶粒の微細化、Ｎｂ炭化物の析出による降伏比の増加に寄与する重要な元素である。Ｎｂ含有量が０．００５％未満ではこの効果が小さい。また、Ｎｂ含有量が０．０７０％以上ではＮｂ炭化物が過剰に析出して焼鈍後も未再結晶フェライトが残存するため鋼板幅方向中央と端部との引張強さの差の増加を招く。したがってＮｂ含有量は０．００５％以上０．０７０％未満とする。好ましくは０．０１０％以上である。好ましくは０．０４０％以下である。
　本発明の高強度鋼板は、以下の成分を任意成分として含有できる。
　Ｃｒ：０．３％以下
　Ｃｒは本発明の作用効果を害さない微量元素として含有してもよい。Ｃｒ含有量が０．３％を超えると焼入性の向上によりマルテンサイトが過剰に生成して降伏比の低下を招く場合がある。したがって、Ｃｒを添加する場合、Ｃｒ含有量は０．３％以下とする。
　Ｍｏ：０．３％以下
　Ｍｏは本発明の作用効果を害さない微量元素として含有してもよい。しかしながら、Ｍｏ含有量が０．３％を超えると焼入性の向上によりマルテンサイトが過剰に生成して降伏比の低下を招く場合がある。したがって、Ｍｏを添加する場合、Ｍｏ含有量は０．３％以下とする。
　Ｂ：０．００５％以下
　Ｂは本発明の作用効果を害さない微量元素として含有してもよい。しかしながら、Ｂ含有量が０．００５％を超えると焼入性の向上によりマルテンサイトが過剰に生成して降伏比の低下を招く場合がある。したがって、Ｂを添加する場合、Ｂ含有量は０．００５％以下とする。
　Ｃｕ：０．３％以下
　Ｃｕは本発明の作用効果を害さない微量元素として含有してもよい。しかしながら、Ｃｕ含有量が０．３％を超えると焼入性の向上によりマルテンサイトが過剰に生成して降伏比の低下を招く場合がある。したがって、Ｃｕを添加する場合、Ｃｕ含有量は０．３％以下とする。
　Ｎｉ：０．３％以下
　Ｎｉは本発明の作用効果を害さない微量元素として含有してもよい。しかしながら、Ｎｉ含有量が０．３％を超えると焼入性の向上によりマルテンサイトが過剰に生成して降伏比の低下を招く場合がある。したがって、Ｎｉを添加する場合、Ｎｉ含有量は０．３％以下とする。
　上記以外の残部はＦｅおよび不可避的不純物である。また、本発明では、上記のほかにＴｉ、Ｖ、Ｓｎ、Ｓｂ、Ｃｏ、Ｗ、Ｃａ、Ｎａ、Ｍｇなどの元素も、本発明の作用効果を害さない微量な範囲で、不可避的不純物として含有してもよい。
　（２）鋼組織
　本発明の高強度鋼板の鋼組織は、面積率でフェライト：９０％以上、パーライト：０～１０％、マルテンサイト、残留オーステナイトおよびセメンタイトの合計：０～３％からなる。また、鋼板幅方向中央におけるフェライトの平均結晶粒径ｄＣが１５．０μｍ以下であり、鋼板幅方向端から鋼板幅方向中央側に１００ｍｍの位置におけるフェライトの平均結晶粒径ｄＥと上記平均結晶粒径ｄＣの差が５．０μｍ以下である。
　フェライト:９０％以上
　フェライトは良好な延性を有し、本発明の鋼組織の主相であり、その含有量は面積率で９０％以上である。フェライトの含有量が面積率で９０％未満では０．７０以上の降伏比が得られない。よってフェライトの含有量は面積率で９０％以上とする。好ましくは９５％以上とする。なお、本発明の鋼組織はフェライト単相（フェライトの含有量が面積率で１００％）でもよい。
　パーライト:０～１０％
　パーライトは所望の降伏強さと引張強さを得るために有効である。しかし、パーライト含有量が面積率で１０％を超えると０．７０以上の降伏比が得られない。パーライト含有量は面積率で０～１０％とする。好ましくは０～５％とする。
　マルテンサイト、残留オーステナイトおよびセメンタイトの合計：０～３％
　本発明の高強度鋼板の鋼組織は、フェライト、パーライト以外に、マルテンサイト、残留オーステナイトおよびセメンタイトを合計で０～３％含有することができる。マルテンサイト、残留オーステナイトおよびセメンタイトの合計が３％を超えると、０．７０以上の降伏比を得られなくなる。このためマルテンサイト、残留オーステナイトおよびセメンタイトの合計は面積率で０～３％とする。
　鋼板幅方向中央におけるフェライトの平均結晶粒径ｄＣ：１５．０μｍ以下
　フェライトの平均結晶粒径は、本発明が目的とする０．７０以上の高降伏比を得るために重要である。フェライトの平均結晶粒径が１５．０μｍを超えると、０．７０以上の降伏比が得られない。したがって、鋼板幅方向中央におけるフェライトの平均結晶粒径は１５．０μｍ以下とする。好ましくは１０．０μｍ以下とする。なお、フェライト平均結晶粒径の下限は特に限定されないが、１．０μｍ未満では引張強さや降伏強さが過度に増加し、伸びフランジ性や伸びの劣化を招く場合があるのでフェライト平均粒径は１．０μｍ以上であることが好ましい。
　鋼板幅方向端から鋼板幅方向中央側に１００ｍｍの位置におけるフェライトの平均結晶粒径ｄＥと平均結晶粒径ｄＣの差：５．０μｍ以下
　鋼板幅方向中央と端部とのフェライト平均結晶粒径の差（フェライト平均結晶粒径差）は、目的とする鋼板幅方向中央と端部（鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置）の引張強さの差を２０ＭＰａ以下とするのに重要であり、差は小さいほど好ましい。鋼板幅方向中央と端部との上記フェライト平均結晶粒径差が５．０μｍを超えると、上記引張強さの差が２０ＭＰａを超え、本発明が目的とする高強度鋼板が得られない。よって、フェライト平均結晶粒径差を５．０μｍ以下とする。また好ましくは３．０μｍ以下とする。なお、上記差の下限は特に限定されないが、１．０μｍ未満とするには熱延および焼鈍時の幅方向の温度分布を均一にするため多額の設備投資が必要になる。このため好ましくは１．０μｍ以上とする。
　なお、各組織の面積率は圧延幅方向に垂直な断面における板厚方向断面の表面から板厚１／４位置を中心とする板厚１／８～３／８の範囲をＳＥＭで観察し、ＡＳＴＭ　Ｅ　５６２－０５に記載のポイントカウント法により求める。フェライトの平均結晶粒径は、上記板厚方向断面の表面から板厚１／４位置を中心とする板厚１／８～３／８の範囲における鋼板幅方向中央と端部（鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置）をＳＥＭで観察し、観察面積と結晶粒数から円相当径を算出することで求める。
　また、本発明では対象とする鋼板のコイルの幅は、８００～１７００ｍｍである。
　（３）製造条件
　本発明の高強度鋼板は上記成分組成を有する鋼を溶製し、鋳造によりスラブ（鋼片）を製造後、熱間圧延、冷間圧延後、連続焼鈍炉で焼鈍を行うことにより製造される。熱間圧延後に酸洗してもよい。以下、これら製造条件の限定条件について説明する。なお、以下の説明における温度は表面温度を意味する。
　鋳造方法は特に限定されるものではなく、顕著な成分組成の偏析や組織の不均一が発生しなければ、造塊法、連続鋳造法のいずれで鋳造しても構わない。
　熱間圧延は、高温の鋳造スラブをそのまま圧延しても良いし、室温まで冷却されたスラブを再加熱してから圧延してもよい。またスラブの時点で割れなどの表面欠陥がある場合はグラインダーなどによってスラブ手入れを施すことができる。スラブを再加熱する場合は、Ｎｂ炭化物を溶解させるため１１００℃以上に加熱することが好ましい。
　熱間圧延では、スラブに粗圧延、仕上圧延を施す。その後、熱延鋼板を巻取り熱延コイルとする。熱間圧延における粗圧延条件は特に限定されるものではなく常法にしたがって行えばよい。仕上圧延条件は特に限定されるものではなく常法にしたがって行えばよいが、Ａｒ３点未満で完了すると、圧延方向に伸長した粗大なフェライトが生成して延性の低下を招く場合がある。このため、仕上圧延温度はＡｒ３点以上とすることが好ましい。また、本発明の高強度鋼板の製造条件の中では巻取温度が重要である。
　巻取温度：５００～６５０℃
　巻取温度はＮｂ炭化物の析出量および析出物径により焼鈍後のフェライト粒径を１５．０μｍ以下に制御するために重要な製造条件である。鋼板の幅方向中央において、巻取温度が５００℃未満では、巻取後の冷却中にＮｂ炭化物が十分析出せず、焼鈍の加熱および均熱時に比較的短時間で析出する。このため、析出物径が不均一になり、粒径バラツキにより、幅方向中央と幅方向端部の引張強さの差が増大する。巻取温度が６５０℃を超えるとＮｂ炭化物の析出物径が過度に粗大化してフェライト平均結晶粒径が粗大化するため０．７０以上の降伏比が得られない。したがって巻取温度は５００～６５０℃とする。好ましくは５５０～６３０℃とする。
　巻取時の鋼板幅方向中央の温度と鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置の温度との差：５０℃以下
　巻取時の幅方向中央と端部（鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置）との温度差（巻取温度差）は、Ｎｂ炭化物の析出量および析出物径により、焼鈍後の上記フェライト平均結晶粒径差を５．０μｍ以下に制御するために重要な製造条件であり、差は小さいほど好ましい。温度差が５０℃を超えるとＮｂ炭化物の析出量および析出物径の差が顕著になり、焼鈍後のフェライト平均結晶粒径差が５．０μｍを超えるため本発明が目的とする、幅方向中央と端部との引張強さの差が小さい高強度鋼板が得られない。したがって、上記巻取温度差は５０℃以下とする。また、好ましくは３０℃以下とする。巻取温度差を５０℃以下とするためには、エッジヒーターなどを用いて鋼板幅方向端部近傍を加熱したり、エッジマスキングにより冷却量を調整したりする方法を採用すればよい。加熱方法は特に限定されるものではなく、直火加熱や誘導加熱などで行うことができる。なお、上記差の下限は特に限定されないが、５℃未満とするには巻取直前にエッジヒーターを増設するなどの多額の設備投資が必要になるため、好ましくは５℃以上とする。
　冷間圧延は常法にしたがって行えばよく、圧延率は３０～８０％とすることが好ましい。
　冷間圧延後、連続焼鈍炉を用いて焼鈍を行う。焼鈍時の加熱速度は特に限定されるものではないが、生産効率や設備投資の観点から０．１～３０．０℃／ｓで行うことが好ましい。加熱方式は特に限定されるものではなく、ラジアントチューブ方式や直火加熱方式で行うことができる。均熱温度および時間の条件は、均熱温度を７００～９００℃、均熱時間を１秒以上保持とすることが好ましい。なお、保持時間（均熱時間）の上限は特に限定されないが、保持時間が長くなりすぎるとＮｂ炭化物の粗大化を招くので、保持時間は３００秒以下が好ましい。
　均熱後の冷却条件は特に限定されず、例えば、冷却停止温度が４００～５００℃、平均冷却速度３０℃／ｓ以下、４００～５００℃の温度域にある保持時間１０～１００秒という条件が挙げられる。
　上記の方法で得られた高強度鋼板の表面にめっきを施すことができる。めっきは溶融亜鉛めっき浴に浸漬する溶融亜鉛めっきなどが好適である。
　溶融亜鉛めっき層に対して合金化処理を施すことにより合金化溶融亜鉛めっき層とすることができる。合金化処理を施す場合、保持温度が４５０℃未満では十分に合金化が進まずめっき密着性や耐食性が劣化する。また、保持温度が５６０℃を超えると合金化が過度に進行してプレス時にパウダリングなどの問題が発生する。このため保持温度は４５０～５６０℃とするのが好ましい。また、保持時間が５秒未満では十分に合金化が進まずめっき密着性や耐食性が劣化するため、保持時間は５秒以上とすることが好ましい。
　その後、必要に応じて伸長率０．１～５．０％の調質圧延を施してもよい。
　以上により、本発明の目的とする高強度鋼板が得られるが、冷延鋼板の場合、さらに電気亜鉛めっきや化成処理、有機系皮膜処理等の表面処理を施しても本発明の目的とする特性を損なうことはない。
　以下、本発明を実施例により詳細に説明する。
　表１に示す成分組成を有する鋼Ａ～Ｍを溶製し、スラブに鋳造して、室温まで冷却した後、１２５０℃で１時間均熱するスラブ加熱を行い、仕上圧延温度９００℃、仕上板厚３．２ｍｍの条件で熱間圧延を施し、表２に示す条件で巻取った。製造した熱延鋼板を酸洗後、仕上板厚１．４ｍｍ、幅１２５０ｍｍの冷延鋼板とし、表２に示す条件の焼鈍を施してＮｏ．１～２１の高強度鋼板を製造した。焼鈍は、めっきを施さない場合はＣＡＬ（continuous annealing line）を用いて行った。また、めっきを施す場合はＣＧＬ（continuous galvanizing/galvannealing line）を用いて、溶融亜鉛めっきまたは合金化溶融亜鉛めっきを施した。めっき層を合金化溶融亜鉛めっき層とする場合は、５１０℃で１０秒保持する合金化処理を施した。
　得られた高強度鋼板に対し、鋼組織観察と引張試験を行った。
　鋼組織の面積率は、圧延幅方向に垂直な断面における板厚方向断面の表面から板厚１／４位置を中心とする板厚１／８～３／８の範囲を、ＳＥＭで１０００倍に拡大し、ＡＳＴＭ　Ｅ　５６２－０５に記載のポイントカウント法により求めた。フェライトの平均結晶粒径は、圧延幅方向に垂直な断面における板厚方向断面の表面から板厚１／４位置を中心とする板厚１／８～３／８の範囲の鋼板幅方向中央と端部（鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置）を、ＳＥＭで１０００倍に拡大し、面積と結晶粒の個数から円相当径を算出して求めた。観察はいずれも各１０視野で行い、その平均を算出した。なお、表２のαはフェライト、Ｐはパーライト、Ｍはマルテンサイトを意味し、α粒径は鋼板幅方向中央におけるフェライト平均結晶粒径、α粒径差は鋼板幅方向中央と端部とのフェライト平均結晶粒径の差を意味する。
　降伏強さと引張強さは、試験片の平行部中央が、鋼板幅方向中央または幅方向端から鋼板幅方向中央側に１００ｍｍ位置に一致する位置から、引張方向が圧延方向と直交方向になるようＪＩＳ５号引張試験片を採取し、ＪＩＳ　Ｚ　２２４１に準拠した引張試験により求めた。なお、引張強さ（ＴＳ）が３３０ＭＰａ以上５００ＭＰａ未満、降伏比（ＹＲ）が０．７０以上、鋼板幅方向の中央と端部との引張強さの差（ＴＳ差）が２０ＭＰａ以下を良好と評価した。また、表２のＴＳおよびＹＲは鋼板幅方向の中央での引張試験結果である。
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
　表２に鋼組織の観察結果と引張試験結果を示す。Ｎｏ．１～３、６、８～９、１２～１５、１８は本発明の要件をすべて満たしているため、本発明が目的とする高降伏比で鋼板幅方向の引張強さの差が小さい高強度鋼板が得られている。一方、Ｎｏ．４～５、７、１０～１１、１６～１７、１９～２１は鋼成分もしくは製造条件が本発明の範囲外であり、所望の鋼組織が得られていないため本発明が目的とする高強度鋼板が得られていない。
　本発明の高強度鋼板は、自動車内板部品などを中心に、高降伏比が要求される分野に好適である。

Claims (7)

  1. 　成分組成は、質量％で、Ｃ：０．０２％以上０．１０％未満、Ｓｉ：０．１０％未満、Ｍｎ：１．０％未満、Ｐ：０．１０％以下、Ｓ：０．０２０％以下、Ａｌ：０．０１％以上０．１０％以下、Ｎ：０．０１０％以下、Ｎｂ：０．００５％以上０．０７０％未満を含有し、残部がＦｅおよび不可避的不純物からなり、
    　鋼組織は、面積率でフェライト：９０％以上、パーライト：０～１０％、マルテンサイト、残留オーステナイトおよびセメンタイトの合計：０～３％からなり、
    　鋼板幅方向中央における前記フェライトの平均結晶粒径ｄＣが１５．０μｍ以下であり、
    　鋼板幅方向端から鋼板幅方向中央側に１００ｍｍの位置における前記フェライトの平均結晶粒径ｄＥと前記平均結晶粒径ｄＣの差が５．０μｍ以下である高強度鋼板。
  2. 　前記成分組成は、さらに、質量％で、Ｃｒ：０．３％以下、Ｍｏ：０．３％以下、Ｂ：０．００５％以下、Ｃｕ：０．３％以下、Ｎｉ：０．３％以下のいずれか１種または２種以上を含有する請求項１に記載の高強度鋼板。
  3. 　高強度鋼板の表面に溶融亜鉛めっき層を有する請求項１または２に記載の高強度鋼板。
  4. 　前記溶融亜鉛めっき層が合金化溶融亜鉛めっき層である請求項３に記載の高強度鋼板。
  5. 　請求項１または２に記載の成分組成を有する鋼片を熱間圧延後、熱延鋼板の鋼板幅方向中央における温度が５００～６５０℃、巻取時の鋼板幅方向中央の温度と鋼板幅方向端から鋼板幅方向中央側に１００ｍｍ位置の温度との差を５０℃以下として巻取り、巻取後の前記熱延鋼板を冷間圧延し、冷延鋼板を連続焼鈍炉で焼鈍する高強度鋼板の製造方法。
  6. 　前記焼鈍後において、高強度鋼板の表面に溶融亜鉛めっきを施す請求項５に記載の高強度鋼板の製造方法。
  7. 　前記溶融亜鉛めっきに合金化処理を施す請求項６に記載の高強度鋼板の製造方法。
PCT/JP2016/001651 2015-03-25 2016-03-22 高強度鋼板およびその製造方法 WO2016152148A1 (ja)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP16768054.5A EP3255168B1 (en) 2015-03-25 2016-03-22 High-strength steel sheet and method for manufacturing same
MX2017012198A MX2017012198A (es) 2015-03-25 2016-03-22 Lamina de acero de alta resistencia y metodo para la produccion de la misma.
US15/559,576 US10494693B2 (en) 2015-03-25 2016-03-22 High-strength steel sheet and method for producing the same
JP2016545379A JP6052476B1 (ja) 2015-03-25 2016-03-22 高強度鋼板およびその製造方法
KR1020177027030A KR101989371B1 (ko) 2015-03-25 2016-03-22 고강도 강판 및 그의 제조 방법
CN201680018071.1A CN107406947B (zh) 2015-03-25 2016-03-22 高强度钢板及其制造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015062043 2015-03-25
JP2015-062043 2015-03-25

Publications (1)

Publication Number Publication Date
WO2016152148A1 true WO2016152148A1 (ja) 2016-09-29

Family

ID=56979249

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2016/001651 WO2016152148A1 (ja) 2015-03-25 2016-03-22 高強度鋼板およびその製造方法

Country Status (7)

Country Link
US (1) US10494693B2 (ja)
EP (1) EP3255168B1 (ja)
JP (1) JP6052476B1 (ja)
KR (1) KR101989371B1 (ja)
CN (1) CN107406947B (ja)
MX (1) MX2017012198A (ja)
WO (1) WO2016152148A1 (ja)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6631762B1 (ja) * 2018-02-28 2020-01-15 Ｊｆｅスチール株式会社 冷延鋼板及びその製造方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102010081B1 (ko) * 2017-12-26 2019-08-12 주식회사 포스코 고강도 고인성 열연강판 및 그 제조방법
US20220018003A1 (en) * 2018-11-21 2022-01-20 Jfe Steel Corporation Steel sheet for cans and method for manufacturing the same
CN113718166B (zh) * 2020-05-25 2022-12-06 上海梅山钢铁股份有限公司 一种屈服强度320MPa级热镀铝锌钢板及其制造方法
CN113718167B (zh) * 2020-05-25 2022-07-15 上海梅山钢铁股份有限公司 一种屈服强度330MPa级液晶背板用热镀铝锌钢板

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04350A (ja) * 1989-11-16 1992-01-06 Kawasaki Steel Corp 伸びフランジ特性に優れた高張力冷延鋼板及び溶融亜鉛めっき鋼板並びにそれらの製造方法
JP2004351501A (ja) * 2003-05-30 2004-12-16 Jfe Steel Kk 熱延金属板の冷却方法および冷却装置ならびに高張力熱延鋼板およびその製造方法
JP2005226081A (ja) * 2004-02-10 2005-08-25 Jfe Steel Kk 機械的性質が均一な高強度熱延鋼板の製造方法
JP2006307281A (ja) * 2005-04-28 2006-11-09 Jfe Steel Kk 打抜き後の平坦度に優れる冷間圧延ままの薄鋼板およびその製造方法
JP2008138234A (ja) * 2006-11-30 2008-06-19 Jfe Steel Kk 高強度高延性缶用鋼板およびその製造方法
JP2012031458A (ja) * 2010-07-29 2012-02-16 Jfe Steel Corp 成形性に優れた高強度冷延薄鋼板およびその製造方法

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS4995109A (ja) 1973-01-17 1974-09-10
CN1025224C (zh) * 1989-11-16 1994-06-29 川崎制铁株式会社 拉伸翻边特性优良的高强度冷轧钢板及熔融镀锌钢板以及它们的制造方法
CA2380377C (en) * 2000-05-31 2007-01-09 Kawasaki Steel Corporation Cold-rolled steel sheets with superior strain-aging hardenability
EP1741800A1 (en) 2004-04-27 2007-01-10 JFE Steel Corporation Steel sheet for can and method for production thereof
JP4740099B2 (ja) 2006-03-20 2011-08-03 新日本製鐵株式会社 高強度冷延鋼板及びその製造方法
JP5135868B2 (ja) 2007-04-26 2013-02-06 Ｊｆｅスチール株式会社 缶用鋼板およびその製造方法
JP4995109B2 (ja) 2008-02-07 2012-08-08 新日本製鐵株式会社 加工性及び耐衝突特性に優れた高強度冷延鋼板及びその製造方法
KR101086330B1 (ko) * 2008-12-26 2011-11-24 주식회사 포스코 재질이 균일한 고강도강 및 그 제조방법
JP5765092B2 (ja) * 2010-07-15 2015-08-19 Ｊｆｅスチール株式会社 延性と穴広げ性に優れた高降伏比高強度溶融亜鉛めっき鋼板およびその製造方法
JP5182386B2 (ja) * 2011-01-31 2013-04-17 Ｊｆｅスチール株式会社 加工性に優れた高降伏比を有する高強度冷延鋼板およびその製造方法
JP5397437B2 (ja) 2011-08-31 2014-01-22 Ｊｆｅスチール株式会社 加工性と材質安定性に優れた冷延鋼板用熱延鋼板、溶融亜鉛めっき鋼板用熱延鋼板およびその製造方法
JP5834717B2 (ja) * 2011-09-29 2015-12-24 Ｊｆｅスチール株式会社 高降伏比を有する溶融亜鉛めっき鋼板およびその製造方法
JP5842515B2 (ja) * 2011-09-29 2016-01-13 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
US9540720B2 (en) * 2011-09-30 2017-01-10 Nippon Steel & Sumitomo Metal Corporation High-strength hot-dip galvanized steel sheet and high-strength alloyed hot-dip galvanized steel sheet having excellent formability and small material anisotropy with ultimate tensile strength of 980 MPa or more
JP5610094B2 (ja) * 2011-12-27 2014-10-22 Ｊｆｅスチール株式会社 熱延鋼板およびその製造方法
WO2013111556A1 (ja) * 2012-01-26 2013-08-01 Ｊｆｅスチール株式会社 高強度熱延鋼板及びその製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04350A (ja) * 1989-11-16 1992-01-06 Kawasaki Steel Corp 伸びフランジ特性に優れた高張力冷延鋼板及び溶融亜鉛めっき鋼板並びにそれらの製造方法
JP2004351501A (ja) * 2003-05-30 2004-12-16 Jfe Steel Kk 熱延金属板の冷却方法および冷却装置ならびに高張力熱延鋼板およびその製造方法
JP2005226081A (ja) * 2004-02-10 2005-08-25 Jfe Steel Kk 機械的性質が均一な高強度熱延鋼板の製造方法
JP2006307281A (ja) * 2005-04-28 2006-11-09 Jfe Steel Kk 打抜き後の平坦度に優れる冷間圧延ままの薄鋼板およびその製造方法
JP2008138234A (ja) * 2006-11-30 2008-06-19 Jfe Steel Kk 高強度高延性缶用鋼板およびその製造方法
JP2012031458A (ja) * 2010-07-29 2012-02-16 Jfe Steel Corp 成形性に優れた高強度冷延薄鋼板およびその製造方法

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6631762B1 (ja) * 2018-02-28 2020-01-15 Ｊｆｅスチール株式会社 冷延鋼板及びその製造方法
US11345974B2 (en) 2018-02-28 2022-05-31 Jfe Steel Corporation Cold rolled steel sheet and method for manufacturing the same

Also Published As

Publication number Publication date
KR20170118928A (ko) 2017-10-25
EP3255168A4 (en) 2017-12-20
MX2017012198A (es) 2017-12-15
CN107406947A (zh) 2017-11-28
CN107406947B (zh) 2020-02-14
KR101989371B1 (ko) 2019-06-14
JP6052476B1 (ja) 2016-12-27
US20180044753A1 (en) 2018-02-15
US10494693B2 (en) 2019-12-03
EP3255168B1 (en) 2020-08-19
JPWO2016152148A1 (ja) 2017-04-27
EP3255168A1 (en) 2017-12-13

Similar Documents

Publication Publication Date Title
KR102389648B1 (ko) 고강도 다상 강, 제조 방법 및 용도
JP6123957B1 (ja) 高強度鋼板およびその製造方法
JP5971434B2 (ja) 伸びフランジ性、伸びフランジ性の面内安定性および曲げ性に優れた高強度溶融亜鉛めっき鋼板ならびにその製造方法
JP5983896B2 (ja) 高強度鋼板およびその製造方法、ならびに高強度亜鉛めっき鋼板の製造方法
JP2019506530A (ja) 優れた成形性を有する高強度鋼板及びこれを製造する方法
CN110073026B (zh) 屈服强度、延展性和扩孔性优异的高强度冷轧钢板、热浸镀锌钢板及其制造方法
JP2020045573A (ja) 強度、延性および成形性が改善された高強度被覆鋼板を製造する方法
JP6075516B1 (ja) 高強度鋼板およびその製造方法
WO2017169941A1 (ja) 薄鋼板およびめっき鋼板、並びに、熱延鋼板の製造方法、冷延フルハード鋼板の製造方法、熱処理板の製造方法、薄鋼板の製造方法およびめっき鋼板の製造方法
CN111433380A (zh) 高强度镀锌钢板及其制造方法
JP6052476B1 (ja) 高強度鋼板およびその製造方法
WO2017169940A1 (ja) 薄鋼板およびめっき鋼板、並びに、熱延鋼板の製造方法、冷延フルハード鋼板の製造方法、熱処理板の製造方法、薄鋼板の製造方法およびめっき鋼板の製造方法
US11414721B2 (en) Method for the manufacture of TWIP steel sheet having an austenitic matrix
JP6123958B1 (ja) 高強度鋼板およびその製造方法
CN113025882B (zh) 一种热基镀锌铁素体贝氏体高强钢板及其制备方法
JP6780804B1 (ja) 高強度鋼板およびその製造方法
WO2016194342A1 (ja) 高強度鋼板及びその製造方法
KR101505252B1 (ko) 성형성이 우수한 저항복비 특성을 갖는 자동차 외판재용 냉연강판 및 그 제조 방법
JP3464611B2 (ja) 成形性と耐食性に優れた高強度溶融亜鉛メッキ熱延鋼板及びその製造方法
JP2006124799A (ja) 常温非時効性に優れた歪時効硬化型鋼板およびその製造方法

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2016545379

Country of ref document: JP

Kind code of ref document: A

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

Ref document number: 16768054

Country of ref document: EP

Kind code of ref document: A1

REEP Request for entry into the european phase

Ref document number: 2016768054

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 15559576

Country of ref document: US

ENP Entry into the national phase

Ref document number: 20177027030

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: MX/A/2017/012198

Country of ref document: MX

NENP Non-entry into the national phase

Ref country code: DE