EP3272892A1 - Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung davon - Google Patents

Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung davon Download PDF

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Publication number
EP3272892A1
EP3272892A1 EP16764383.2A EP16764383A EP3272892A1 EP 3272892 A1 EP3272892 A1 EP 3272892A1 EP 16764383 A EP16764383 A EP 16764383A EP 3272892 A1 EP3272892 A1 EP 3272892A1
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steel sheet
rolled steel
content
strength cold
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French (fr)
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EP3272892A4 (de
EP3272892B1 (de
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Shimpei Yoshioka
Katsutoshi Takashima
Kohei Hasegawa
Yoshimasa Funakawa
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D6/001—Heat treatment of ferrous alloys containing 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • 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
    • C22C38/38—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C23G1/081—Iron or steel solutions containing H2SO4
    • 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
    • C21D2211/001—Austenite
    • 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
    • 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
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the present invention relates to a high-strength cold-rolled steel sheet having a tensile strength (TS) of 1,300 MPa or higher, a good chemical conversion property, and good formability and being useful in applications pertaining to automotive components, and to a method for producing the high-strength cold-rolled steel sheet.
  • TS tensile strength
  • Steel sheets for automobiles are used after the steel sheets have been painted. Before painting, such steel sheets are treated with chemical conversion such as phosphate conversion. Since chemical conversion of steel sheets is an important treatment to ensure corrosion resistance after painting, steel sheets for automobiles need to have a good chemical conversion property.
  • Patent Literature 1 the balance between strength and ductility has been improved by adding a large amount of C.
  • addition of a large amount of C leads to a deterioration in stretch flangeability due to a difference in hardness between two phases.
  • Patent Literature 3 addition of a large amount of Mn causes Si-Mn compound oxides to be finely dispersed on the surface of a steel sheet and allows the Si-Mn compound oxides to serve as nucleation sites for zinc phosphate crystals, which reduces the amount of SiO 2 on the surface of the steel sheet to as low an amount as possible to ensure the chemical conversion property. It is, however, difficult to obtain a tensile strength of 1,300 MPa and an elongation of 10% or higher when the C content and the Si content are as described in Patent Literature 3.
  • an object of the present invention is to provide a high-strength cold-rolled steel sheet having a tensile strength (TS) of 1,300 MPa or higher, a good chemical conversion property, and good formability and to a method for producing the high-strength cold-rolled steel sheet.
  • TS tensile strength
  • a high-strength cold-rolled steel sheet having a tensile strength (TS) of 1,300 MPa or higher, a good chemical conversion property, and good formability can be produced by pickling a steel sheet that does not contain more Mn than necessary but contains Si and Mn in the range satisfying formula (1) below and that has been continuously annealed after cold rolling, and further re-pickling the steel sheet to remove Si-based oxide on the surface of the steel sheet: Si / Mn ⁇ 0.5 in the formula, [Si] represents the Si content (% by mass), and [Mn] represents the Mn content (% by mass).
  • a high-strength cold-rolled steel sheet has a composition including, in terms of % by mass, C: 0.15% or more and 0.22% or less, Si: 1.0% or more and 2.0% or less, Mn: 1.7% or more and 2.5% or less, P: 0.05% or less, S: 0.02% or less, Al: 0.01% or more and 0.05% or less, N: 0.005% or less, and the balance being iron and unavoidable impurities.
  • the composition satisfies formula (1) below.
  • the steel sheet has a structure including, in terms of area fraction, 60% or more and less than 100% of tempered martensite, 5% or less (inclusive of 0%) of untransformed austenite, and the balance being ferrite.
  • the ferrite has an average crystal grain size of less than 3.5 ⁇ m. Less than 10 particles/100 ⁇ m 2 of Si-Mn compound oxide particles having a circle equivalent diameter of 5 ⁇ m or less are present on the surface of the steel sheet. The surface of the steel sheet is covered with Si-based oxide at a coverage of 1% or less.
  • the steel sheet has a tensile strength of 1,300 MPa or higher: Si / Mn ⁇ 0.5 in the formula, [Si] represents the Si content (% by mass), and [Mn] represents the Mn content (% by mass).
  • the high-strength cold-rolled steel sheet according to the first embodiment has the composition further including, in terms of % by mass, Ti: 0.010% or more and 0.020% or less.
  • the high-strength cold-rolled steel sheet according to any one of the first to third embodiments has the composition further including, in terms of % by mass, B: 0.0002% or more and 0.0020% or less.
  • the high-strength cold-rolled steel sheet according to any one of the first to fourth embodiments has the composition further including, in terms of % by mass, at least one selected from V: 0.01% or more and 0.30% or less, Mo: 0.01% or more and 0.30% or less, and Cr: 0.01% or more and 0.30% or less.
  • the high-strength cold-rolled steel sheet according to any one of the first to sixth embodiments has the composition further including, in terms of % by mass, at least one selected from Sn: 0.001% or more and 0.100% or less, Sb: 0.001% or more and 0.100% or less, Ca: 0.0002% or more and 0.0100% or less, W: 0.01% or more and 0.10% or less, Co: 0.01% or more and 0.10% or less, and REM: 0.0002% or more and 0.0050% or less.
  • a method for producing a high-strength cold-rolled steel sheet includes: heating a steel having the composition according to any one of the first to seventh embodiments to a temperature of 1,200 °C or higher, then performing hot rolling at a finish rolling delivery temperature equal to or higher than 800 °C, performing coiling at a temperature of 450 °C or higher and 700 °C or lower, and performing cold rolling; then performing an annealing treatment that involves performing heating to an annealing temperature of Ac 1 point or higher and Ac 3 point or lower where a holding time in a temperature range from Ac 1 point to Ac 3 point is 30 seconds or longer and 1,200 seconds or shorter, performing primary cooling from the annealing temperature to a primary cooling finishing temperature equal to or higher than 600 °C at an average cooling rate below 100 °C/s, and performing secondary cooling to a secondary cooling finishing temperature equal to or lower than 100 °C at an average cooling rate of 100 °C/s or higher and 1,000 °C/s or lower; then performing a tempering
  • the re-pickling uses, as a pickling solution, a non-oxidizing acid, which is different from a pickling solution used in the pickling.
  • high-strength cold-rolled steel sheet refers to a cold-rolled steel sheet having a tensile strength (TS) of 1,300 MPa or higher.
  • the present invention provides a high-strength cold-rolled steel sheet having a tensile strength of 1,300 MPa or higher, a good chemical conversion property, and good formability. Since the high-strength cold-rolled steel sheet of the present invention has a tensile strength of 1,300 MPa or higher and has a good chemical conversion property and good formability, the steel sheet of the present invention can be preferably used in applications pertaining to automotive parts and the like and offers significant advantageous effects of, for example, reducing the weight of automotive parts and improving the reliability thereof.
  • Carbon (C) is an element effective in improving the balance between the strength and ductility of the steel sheet. At a C content below 0.15%, it is difficult to ensure a tensile strength of 1,300 MPa or higher. At a C content exceeding 0.22%, coarse cementite is precipitated, which degrades formability such as stretch flangeability.
  • the C content is therefore in the range of 0.15% or more and 0.22% or less.
  • the C content is preferably 0.16% or more.
  • the C content is preferably 0.20% or less.
  • Silicon (Si) is an element effective in ensuring strength without significantly reducing the ductility of the steel sheet. At a Si content below 1.0%, a steel sheet having high strength and high formability cannot be produced. At a Si content exceeding 2.0%, pickling and subsequent re-pickling still fail to completely remove Si oxide on the surface of the steel sheet, which results in a poor chemical conversion property.
  • the Si content is therefore in the range of 1.0% or more and 2.0% or less.
  • the Si content is preferably 1.0% or more.
  • the Si content is preferably 1.5% or less.
  • Mn 1.7% or more and 2.5% or less
  • [Si] represents the Si content (% by mass)
  • [Mn] represents the Mn content (% by mass).
  • Si-based oxide and Si-Mn compound oxides produced depend on the balance between Si and Mn. If one oxide is produced in a much larger amount than the other oxide, pickling and subsequent re-pickling still fail to completely remove the oxides on the surface of the steel sheet, which results in a poor chemical conversion property. It is thus necessary to specify the quantitative ratio of Si to Mn. If the Mn content is much larger than the Si content, that is, [Si]/[Mn] ⁇ 0.5, excessive amounts of Si-Mn-based oxides (Si-Mn compound oxides) are produced and as a result, the chemical conversion property intended in the present invention is not obtained. Therefore, [Si]/[Mn] ⁇ 0.5.
  • Phosphorus (P) is an impurity element and needs to be reduced in amount because it degrades ductility. At a P content exceeding 0.05%, grain boundary embrittlement associated with segregation of P to austenite grain boundaries during casting degrades local ductility. As a result, the balance between strength and ductility is impaired.
  • the P content is therefore 0.05% or less.
  • the P content is preferably 0.02% or less.
  • Al 0.01% or more and 0.05% or less
  • Aluminum (Al) has an effect of improving ductility by forming Al oxide to reduce the amount of oxides such as Si oxide. However, a significant effect is not obtained at an Al content below 0.01%. If Al is added in an excess amount exceeding 0.05%, Al combines with N to form a nitride. This nitride is precipitated at austenite grain boundaries during casting to cause grain boundary embrittlement, which degrades stretch flangeability.
  • the Al content is therefore in the range of 0.01% or more and 0.05% or less.
  • N Nitrogen
  • Al and Ti These nitrides degrade stretch flangeability as described above.
  • Ti nitride and Al nitride significantly degrade stretch flangeability, and an increased amount of a solid solution of N leads to a considerable reduction in elongation.
  • the N content is therefore 0.005% or less.
  • the N content is preferably 0.002% or less.
  • Nb 0.02% or more and 0.10% or less
  • B Boron
  • C,B boron carbide Fe 23
  • the steel sheet preferably further includes at least one selected from V: 0.01% or more and 0.30% or less, Mo: 0.01% or more and 0.30% or less, and Cr: 0.01% or more and 0.30% or less.
  • V 0.01% or more and 0.30% or less
  • the steel sheet preferably further includes at least one selected from Cu: 0.01% or more and 0.30% or less and Ni: 0.01% or more and 0.30% or less.
  • Both Sn and Sb have an effect of suppressing surface oxidation, decarburization, and nitridization, and thus Sn and Sb may be added as desired. However, this effect is small at a Sn content below 0.001% and a Sb content below 0.001%. This effect is saturated at a Sn content exceeding 0.100% and a Sb content exceeding 0.100%. Therefore, the Sn content, if added, is 0.001% or more and 0.100% or less, and the Sb content, if added, is 0.001% or more and 0.100% or less.
  • the Sn content is preferably 0.005% or more, and the Sb content is preferably 0.005% or more.
  • the Sn content is preferably 0.010% or less, and the Sb content is preferably 0.010% or less.
  • the steel sheet contains, in terms of area fraction, 60% or more and less than 100% of tempered martensite, 5% or less (inclusive of 0%) of untransformed austenite, and the balance being ferrite.
  • the ferrite has an average crystal grain size of less than 3.5 ⁇ m.
  • the ferrite has an average crystal grain size of 3.5 ⁇ m or more, crystal grain refining strengthening is not enough to obtain a predetermined strength. During deformation, variations in deformation between crystal grains tend to be generated, which degrades formability. Threrefore, the average crystal grain size of ferrite is less than 3.5 ⁇ m.
  • the number of Si-Mn compound oxide particles having a circle equivalent diameter of 5 ⁇ m or less can be determined by the method of Examples described below.
  • the surface refers to a region extending in the thickness direction from the surface layer to a depth corresponding to 3% of the thickness.
  • the finish rolling delivery temperature is 800 °C or higher, a hot-rolled uniform matrix phase structure can be obtained. If the finish rolling delivery temperature is below 800 °C, the steel sheet has an uneven structure, and there is an increased risk of low ductility and various defects formed during forming. Therefore, the finish rolling delivery temperature is 800 °C or higher.
  • the upper limit of the finish rolling delivery temperature is not limited, but is preferably 1,000 °C or lower because rolling the steel at an excessively high temperature produces scale defects and the like.
  • the annealing temperature is preferably 780 °C or higher. If the holding time at the annealing temperature is too short, the microstructure is not annealed well, which provides an uneven structure including the deformation structure formed by cold rolling and thus results in low ductility. However, if the holding time is too long, this holding time is not desirable because of long production time and high production costs. Therefore, the holding time is 30 to 1,200 seconds. A preferred lower limit of the holding time is 150 seconds. A preferred upper limit is 600 seconds.
  • Tempering is preferably performed in the range of 150 °C to 250 °C. If the holding time is shorter than 120 seconds, martensite is softened insufficiently in the temperature range from 100 °C to 300 °C, so that the effect of improving formability cannot be expected. If the holding time is longer than 1,800 seconds, this holding time is not desirable because martensite is softened to an excessive degree so as to significantly reduce the strength and a long re-heating time increases the production costs.
  • the re-pickling remove Si oxide and Si-Mn oxides on the surface of the steel sheet and improve the chemical conversion property.
  • the re-pickling preferably uses, as a pickling solution, a non-oxidizing acid, which is different from a pickling solution used in the pickling.
  • an acid mixture of 0.1 to 50 g/L of hydrochloric acid, 0.1 to 150 g/L of sulfuric acid, 0.1 to 20 g/L of hydrochloric acid, and 0.1 to 60 g/L of sulfuric acid can be used preferably.
  • the high-strength cold-rolled steel sheet of the present invention having a tensile strength (TS) of 1,300 MPa or higher and having a good chemical conversion property and good formability is produced. Since the high-strength cold-rolled steel sheet of the present invention after annealing has good sheet shape (flatness), the process for correcting the shape of the steel sheet by, for example, rolling and leveler processing is not always needed, but the steel sheet after annealing may be rolled at an elongation rate of about several percent without causing any problem in order to adjust material properties and surface roughness.
  • TS tensile strength
  • Sample steels A to R each having the composition described in Table 1 were each smelted under vacuum to produce a slab, which was then hot-rolled under the conditions described in Table 2 to produce a hot-rolled steel sheet.
  • This hot-rolled steel sheet was pickled to remove surface scale and then cold-rolled (rolling reduction ratio: 60%).
  • the steel sheet was then subjected to continuous annealing and the tempering treatment under the conditions described in Table 2 and then subjected to pickling and re-pickling.
  • a sample was taken from the steel sheet obtained above and subjected to observation (measurement) of the metallographic structure, a tensile test, and a hole expansion test.
  • the number of Si-Mn oxide particles having a circle equivalent diameter of 5 ⁇ m or less and the coverage of Si-based oxide on the surface of the steel sheet were obtained.
  • the chemical conversion property was determined. The measurement methods and the calculation methods are described below.
  • the metallographic structure was observed as follows: cutting the sample such that the thickness cross section parallel to the rolling direction was targeted for observation, etching the thickness middle area with 1% Nital, and then observing a typical microstructure under a scanning electron microscope (SEM).
  • SEM scanning electron microscope
  • the volume fraction of two phases was obtained by a point counting method on the basis of the SEM image taken at a magnification of x1,000, and the grain size of each phase was obtained by linear analysis.
  • the obtained volume fraction was defined as the area fraction.
  • the coverage of Si-based oxide on the surface of the steel sheet was obtained as follows: identifying Si-based oxide in the same method as described above by observing the surface of the steel sheet under a SEM in five fields of view at x1,000 and performing EDX analysis in the five fields of view; and calculating the coverage by a point counting method (a method involving drawing 15 straight lines vertically and 15 straight lines horizontally on the SEM image and calculating the probability of presence of Si-based oxide at intersections (225 points).
  • the chemical conversion property was evaluated as follows: performing chemical conversion using a commercial chemical conversion agent (PALBOND PB-L3065 (registered trademark) available from Nihon Parkerizing Co., Ltd.) under the conditions of a bath temperature of 35 °C and a treatment time of 120 seconds; observing the surface of the steel sheet after chemical conversion under a SEM in five fields of view at a magnification of x500; and rating the chemical conversion property as "A” which means good when 95% or more (area fraction) of a chemical-conversion crystal was evenly formed in all five fields of view, and rating the chemical conversion property as "B” which means poor when more than 5% (area fraction) of defects were found at least in one field of view.
  • a commercial chemical conversion agent (PALBOND PB-L3065 (registered trademark) available from Nihon Parkerizing Co., Ltd.) under the conditions of a bath temperature of 35 °C and a treatment time of 120 seconds
  • Samples No. 13 and No. 14 are Comparative Examples in which the Si content is out of the scope of the present invention.
  • Sample No. 13 fails to have a good chemical conversion property because Si oxide is present on the surface of the steel sheet even after the two-step pickling treatment.
  • Sample No. 14 fails to have a predetermined elongation.
  • Samples No. 20 to No. 22 have an insufficient martensite fraction and thus fail to have a predetermined strength.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Cleaning And De-Greasing Of Metallic Materials By Chemical Methods (AREA)
  • Chemical Treatment Of Metals (AREA)
EP16764383.2A 2015-03-18 2016-02-16 Hochfestes kaltgewalztes stahlblech und verfahren zur herstellung davon Active EP3272892B1 (de)

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EP3399064A4 (de) * 2016-02-18 2019-01-09 JFE Steel Corporation Hochfestes kaltgewalztes stahlblech
EP3626849A4 (de) * 2017-05-19 2020-05-06 JFE Steel Corporation Verfahren zur herstellung von hochfestem zinkplattiertem stahlblech
EP4001447A4 (de) * 2019-08-30 2022-06-15 JFE Steel Corporation Stahlblech, element und verfahren zur herstellung davon

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JP6699633B2 (ja) * 2017-07-25 2020-05-27 Ｊｆｅスチール株式会社 塗装後耐食性と耐遅れ破壊特性に優れた高強度冷延鋼板及びその製造方法
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KR102398869B1 (ko) * 2018-03-30 2022-05-16 제이에프이 스틸 가부시키가이샤 냉연 강판 및 그의 제조 방법
CN112996937B (zh) * 2018-11-09 2022-04-26 杰富意钢铁株式会社 锆系化成处理用冷轧钢板及其制造方法以及锆系化成处理钢板及其制造方法
EP3910087B1 (de) * 2019-01-09 2023-04-05 JFE Steel Corporation Hochfestes kaltgewalztes stahlblech und herstellungsverfahren dafür
JP6954339B2 (ja) * 2019-02-04 2021-10-27 Ｊｆｅスチール株式会社 冷延鋼板及びその製造方法
CN110129670B (zh) * 2019-04-25 2020-12-15 首钢集团有限公司 一种1300MPa级高强高塑性热冲压用钢及其制备方法
WO2020262652A1 (ja) * 2019-06-28 2020-12-30 日本製鉄株式会社 鋼板
KR20230016218A (ko) * 2020-07-20 2023-02-01 아르셀러미탈 열처리 냉연 강판 및 그 제조 방법
MX2023005701A (es) * 2021-02-02 2023-05-29 Nippon Steel Corp Lamina de acero delgada.
KR20230081744A (ko) * 2021-11-29 2023-06-08 주식회사 포스코 연신율이 우수한 초고강도 냉연강판 및 이의 제조방법
CN115044831B (zh) * 2022-06-09 2023-08-25 包头钢铁（集团）有限责任公司 一种1100MPa级冷轧马氏体钢及其制造方法
CN115505840A (zh) * 2022-08-25 2022-12-23 包头钢铁（集团）有限责任公司 一种高强度淬火配分钢及其生产方法

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JP4586449B2 (ja) * 2004-02-27 2010-11-24 Ｊｆｅスチール株式会社 曲げ性および伸びフランジ性に優れた超高強度冷延鋼板およびその製造方法
JP4461112B2 (ja) * 2006-03-28 2010-05-12 株式会社神戸製鋼所 加工性に優れた高強度鋼板
JP5359168B2 (ja) * 2008-10-08 2013-12-04 Ｊｆｅスチール株式会社 延性に優れる超高強度冷延鋼板およびその製造方法
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EP3399064A4 (de) * 2016-02-18 2019-01-09 JFE Steel Corporation Hochfestes kaltgewalztes stahlblech
US11085099B2 (en) 2016-02-18 2021-08-10 Jfe Steel Corporation High-strength cold-rolled steel sheet
EP3626849A4 (de) * 2017-05-19 2020-05-06 JFE Steel Corporation Verfahren zur herstellung von hochfestem zinkplattiertem stahlblech
US11248277B2 (en) 2017-05-19 2022-02-15 Jfe Steel Corporation Method for manufacturing high-strength galvanized steel sheet
EP4001447A4 (de) * 2019-08-30 2022-06-15 JFE Steel Corporation Stahlblech, element und verfahren zur herstellung davon

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EP3272892A4 (de) 2018-01-24
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WO2016147549A1 (ja) 2016-09-22
EP3272892B1 (de) 2019-08-28
JPWO2016147549A1 (ja) 2017-07-13
CN107429344A (zh) 2017-12-01
JP6210175B2 (ja) 2017-10-11
US20180037969A1 (en) 2018-02-08
KR101998652B1 (ko) 2019-07-10

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