WO2021153036A1 - 熱延鋼板 - Google Patents

熱延鋼板 Download PDF

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Publication number
WO2021153036A1
WO2021153036A1 PCT/JP2020/046322 JP2020046322W WO2021153036A1 WO 2021153036 A1 WO2021153036 A1 WO 2021153036A1 JP 2020046322 W JP2020046322 W JP 2020046322W WO 2021153036 A1 WO2021153036 A1 WO 2021153036A1
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hot
steel sheet
rolled steel
content
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PCT/JP2020/046322
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English (en)
French (fr)
Japanese (ja)
Inventor
和政 筒井
洋志 首藤
林　宏太郎
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Nippon Steel Corp
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Nippon Steel Corp
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Priority to KR1020227023219A priority Critical patent/KR102776903B1/ko
Priority to JP2021574510A priority patent/JP7260824B2/ja
Priority to CN202080093028.8A priority patent/CN114929915B/zh
Priority to US17/790,645 priority patent/US12392020B2/en
Priority to EP20916444.1A priority patent/EP4098762B1/en
Priority to MX2022008544A priority patent/MX2022008544A/es
Publication of WO2021153036A1 publication Critical patent/WO2021153036A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
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    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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

Definitions

  • the present invention relates to a hot-rolled steel sheet. Specifically, the present invention relates to a hot-rolled steel sheet that is formed into various shapes by press working or the like and is used, and in particular, a hot-rolled steel sheet that has high strength and is excellent in hole-expanding property and shearing workability.
  • the present application claims priority based on Japanese Patent Application No. 2020-010945 filed in Japan on January 27, 2020, the contents of which are incorporated herein by reference.
  • Patent Document 1 describes high strength for automobiles having excellent collision resistance and moldability, in which retained austenite having an average crystal particle size of 5 ⁇ m or less is dispersed in ferrite having an average crystal particle size of 10 ⁇ m or less.
  • Steel plates are disclosed.
  • austenite undergoes martensitic transformation during processing and exhibits a large elongation due to transformation-induced plasticity, but the formation of hard martensite impairs the hole-expandability.
  • Patent Document 1 discloses that not only ductility but also hole expansion property is improved by miniaturizing ferrite and retained austenite.
  • Patent Document 2 discloses a high-strength steel sheet having a tensile strength of 980 MPa or more, which has excellent elongation and hole-expanding properties, in which a second phase composed of retained austenite and / or martensite is finely dispersed in crystal grains. There is.
  • Patent Documents 3 and 4 disclose a high-strength hot-rolled steel sheet having excellent ductility and hole-spreading property, and a method for producing the same.
  • Patent Document 3 after cooling to a temperature range of 720 ° C. or lower within 1 second after the completion of hot rolling, and staying in a temperature range of more than 500 ° C. and 720 ° C. or lower for a residence time of 1 to 20 seconds, 350 to A method for producing a high-strength hot-rolled steel sheet having good ductility and stretch flangeability, which is wound in a temperature range of 500 ° C., is disclosed.
  • Patent Document 4 describes the average of grains surrounded by grain boundaries having a crystal orientation difference of 15 ° or more in a steel structure excluding retained austenite, which is mainly composed of bainite and has an appropriate amount of polygonal ferrite and retained austenite.
  • a high-strength hot-rolled steel sheet having a particle size of 15 ⁇ m or less and having good ductility and stretch flangeability is disclosed.
  • Patent Documents 1 to 4 are all techniques for improving strength and press moldability at the time of drilling, but there is no mention of a technique for improving shear workability, and parts are press molded. It is presumed that post-treatment will be required at this stage and the manufacturing cost will increase.
  • the present invention has been made in view of the above problems of the prior art, and an object of the present invention is to provide a hot-rolled steel sheet having high strength and excellent drilling and shearing properties.
  • the matrix structure of the metal structure is hard. That is, it is preferable that the soft structure fraction such as ferrite and retained austenite is as small as possible.
  • a hard structure is generally formed in a phase transformation of 600 ° C. or lower, but in this temperature range, grain boundaries and crystal orientation differences in which the crystal orientation difference is 60 ° with respect to the ⁇ 110> direction are present. A large amount of grain boundaries at 7 ° are formed.
  • (F) Increase the density of the length of the grain boundary having a crystal orientation difference of 60 ° about the ⁇ 110> direction, and the length of the grain boundary having a crystal orientation difference of 7 ° with the ⁇ 110> direction as the axis. It is effective to set the winding temperature to less than a predetermined temperature in order to reduce the density of the crystals.
  • the winding temperature is equal to or higher than the predetermined temperature, the density of the length of the grain boundary having a crystal orientation difference of 60 ° with respect to the ⁇ 110> direction decreases, and the crystal orientation difference is 7 ° with respect to the ⁇ 110> direction.
  • the density of grain boundaries is increased.
  • the gist of the present invention made based on the above findings is as follows.
  • (1) The hot-rolled steel sheet according to one aspect of the present invention has a chemical composition of mass%. C: 0.040 to 0.250%, Si: 0.05 to 3.00%, Mn: 0.50 to 4.00%, sol.
  • the rest consists of Fe and impurities
  • the metal structure is% of the area, Martensite and tempered martensite total more than 92.0% and less than 100.0%, Retained austenite is less than 3.0% Ferrite is less than 5.0% ⁇ 110> direction as an axis, and the density S 60 lengths of the grain boundary crystal orientation difference is 60 °, the ratio of the density S 7 grain boundary length crystal orientation difference is 7 ° S 60 / S 7 is more than 0.34, less than 0.60, The standard deviation of the Mn concentration is 0.60% by mass or less, The tensile strength is 980 MPa or more.
  • the hot-rolled steel sheet according to (1) above may have an average crystal grain size of less than 3.0 ⁇ m on the surface layer.
  • the hot-rolled steel sheet according to (1) or (2) above has a chemical composition of% by mass.
  • a hot-rolled steel sheet having excellent strength, drilling property and shearing workability can be obtained. Further, according to the above-mentioned preferred embodiment according to the present invention, it is possible to obtain a hot-rolled steel sheet having the above-mentioned characteristics and further suppressing the occurrence of bending internal cracks, that is, having excellent bending internal crack resistance. can.
  • the hot-rolled steel sheet according to the above aspect of the present invention is suitable as an industrial material used for automobile members, mechanical structural members, and building members.
  • the hot-rolled steel sheet according to this embodiment has a mass% of C: 0.040 to 0.250%, Si: 0.05 to 3.00%, Mn: 0.50 to 4.00%, sol. .. Al: 0.001 to 2.000%, P: 0.100% or less, S: 0.0300% or less, N: 0.1000% or less, O: 0.0100% or less, and the balance: Fe and impurities including.
  • C 0.040 to 0.250%
  • Si 0.05 to 3.00%
  • Mn 0.50 to 4.00%
  • sol. .. Al 0.001 to 2.000%
  • P 0.100% or less
  • S 0.0300% or less
  • N 0.1000% or less
  • O 0.0100% or less
  • Fe and impurities including Each element will be described in detail below.
  • C 0.040 to 0.250%
  • C increases the surface integral of the hard phase. Further, C increases the strength of martensite by binding with precipitation strengthening elements such as Ti, Nb, and V. If the C content is less than 0.040%, it becomes difficult to obtain the desired strength. Therefore, the C content is 0.040% or more.
  • the C content is preferably 0.060% or more, more preferably 0.070% or more.
  • the C content is set to 0.250% or less.
  • the C content is preferably 0.150% or less.
  • Si 0.05 to 3.00% Si has the effect of delaying the precipitation of cementite. By this action, the surface integral ratio of martensite and tempered martensite can be increased, and the strength of the hot-rolled steel sheet can be increased by solid solution strengthening. Further, Si has an action of making the steel sound by deoxidation (suppressing the occurrence of defects such as blow holes in the steel). If the Si content is less than 0.05%, the effect of the above action cannot be obtained. Therefore, the Si content is set to 0.05% or more. The Si content is preferably 0.50% or more and 1.00% or more.
  • the Si content is 3.00% greater than the surface texture and chemical conversion of the hot-rolled steel sheet, and further with deteriorated significantly hole expandability and weldability, A 3 transformation point increases significantly. This makes it difficult to perform hot rolling in a stable manner. Therefore, the Si content is set to 3.00% or less.
  • the Si content is preferably 2.70% or less, more preferably 2.50% or less.
  • Mn 0.50 to 4.00% Mn has the effect of suppressing the ferrite transformation and increasing the strength of the hot-rolled steel sheet. If the Mn content is less than 0.50%, a tensile strength of 980 MPa or more cannot be obtained. Therefore, the Mn content is set to 0.50% or more.
  • the Mn content is preferably 1.00% or more, 1.50% or more, and 1.80% or more.
  • the Mn content exceeds 4.00%, the crystal orientation difference of the crystal grains in the hard phase becomes non-uniform due to the segregation of Mn, and the unevenness of the fracture surface on the end face after shearing becomes large. Therefore, the Mn content is set to 4.00% or less.
  • the Mn content is preferably 3.70% or less and 3.50% or less.
  • Al has the effect of deoxidizing the steel to be healthy, and also has the effect of increasing the area fraction of martensite and tempered martensite by suppressing the precipitation of cementite from austenite. .. sol. If the Al content is less than 0.001%, the effect of the above action cannot be obtained. Therefore, sol. The Al content is 0.001% or more. sol. The Al content is preferably 0.010% or more. On the other hand, sol. If the Al content exceeds 2.000%, the above effects are saturated and economically unfavorable. The Al content is 2.000% or less. sol. The Al content is preferably 1.500% or less and 1.300% or less. In this embodiment, sol. Al means acid-soluble Al, and indicates solid solution Al existing in steel in a solid solution state.
  • P 0.100% or less
  • P is an element generally contained as an impurity, but it is also an element having an action of increasing the strength by strengthening the solid solution. Therefore, P may be positively contained, but P is an element that is easily segregated, and when the P content exceeds 0.100%, the decrease in hole widening property due to grain boundary segregation becomes remarkable. .. Therefore, the P content is set to 0.100% or less.
  • the P content is preferably 0.030% or less.
  • the lower limit of the P content does not need to be specified, but it is preferably 0.001% from the viewpoint of refining cost.
  • S 0.0300% or less
  • S is an element contained as an impurity and forms sulfide-based inclusions in the steel to reduce the hole-expanding property of the hot-rolled steel sheet.
  • the S content exceeds 0.0300%, the hole-expandability of the hot-rolled steel sheet is significantly reduced. Therefore, the S content is 0.0300% or less.
  • the S content is preferably 0.0050% or less.
  • the lower limit of the S content does not need to be specified, but is preferably 0.0001% from the viewpoint of refining cost.
  • N 0.1000% or less
  • N is an element contained in steel as an impurity and has an effect of reducing the hole expanding property of the hot-rolled steel sheet.
  • the N content is set to 0.1000% or less.
  • the N content is preferably 0.0800% or less, and more preferably 0.0700% or less.
  • the lower limit of the N content does not need to be specified in particular, but as will be described later, when one or more of Ti, Nb and V are contained to refine the metal structure, precipitation of carbonitride is required.
  • the N content is preferably 0.0010% or more, and more preferably 0.0020% or more in order to promote the above.
  • O 0.0100% or less
  • O forms a coarse oxide that becomes a starting point of fracture when it is contained in a large amount in steel, and causes brittle fracture and hydrogen-induced cracking. Therefore, the O content is set to 0.0100% or less.
  • the O content is preferably 0.0080% or less and 0.0050% or less.
  • the O content may be 0.0005% or more and 0.0010% or more in order to disperse a large number of fine oxides when the molten steel is deoxidized.
  • the balance of the chemical composition of the hot-rolled steel sheet according to the present embodiment may be Fe and impurities.
  • the impurities mean those mixed from ore as a raw material, scrap, manufacturing environment, etc., and are allowed as long as they do not adversely affect the hot-rolled steel sheet according to the present embodiment. do.
  • the hot-rolled steel sheet according to the present embodiment may optionally contain Ti, Nb, V, Cu, Cr, Mo, Ni, B, Ca, Mg, REM, Bi, Zr, Co, Zn, W and Sn. It may be contained as an element. When the above optional element is not contained, the lower limit of the content is 0%.
  • the above optional elements will be described in detail.
  • Ti 0.005 to 0.300%
  • Nb 0.005 to 0.100%
  • V 0.005 to 0.500% Since Ti, Nb and V all precipitate as carbides or nitrides in steel and have an action of refining the metal structure by a pinning effect, one or more of these elements are contained. May be good. In order to obtain the effect of the above action more reliably, the Ti content should be 0.005% or more, the Nb content should be 0.005% or more, or the V content should be 0.005% or more. It is preferable to do so. That is, it is preferable that the content of even one of Ti, Nb and V is 0.005% or more.
  • the Ti content is 0.300% or less, the Nb content is 0.100% or less, and the V content is 0.500% or less.
  • the Ti content is preferably 0.200% or less, 0.150% or less, 0.120% or less, 0.110% or less, or 0.100% or less.
  • the Cu has an action of enhancing the hardenability of the hot-rolled steel sheet and an action of precipitating as carbide in the steel at a low temperature to increase the strength of the hot-rolled steel sheet.
  • the Cu content is preferably 0.01% or more, and more preferably 0.05% or more.
  • the Cu content is set to 2.00% or less.
  • the Cu content is preferably 1.50% or less and 1.00% or less.
  • the Cr content is preferably 0.01% or more and 0.05% or more.
  • the Cr content is set to 2.00% or less.
  • Mo has an action of enhancing the hardenability of the hot-rolled steel sheet and an action of precipitating carbides in the steel to increase the strength.
  • the Mo content is preferably 0.01% or more and 0.02% or more.
  • the Mo content is set to 1.00% or less.
  • the Mo content is preferably 0.50% or less and 0.20% or less.
  • Ni has the effect of enhancing the hardenability of hot-rolled steel sheets. Further, when Ni contains Cu, it has an effect of effectively suppressing the grain boundary cracking of the slab caused by Cu. In order to obtain the effect of the above action more reliably, the Ni content is preferably 0.02% or more. Since Ni is an expensive element, it is economically unfavorable to contain it in a large amount. Therefore, the Ni content is set to 2.00% or less.
  • B has an effect of enhancing the hardenability of the hot-rolled steel sheet.
  • the B content is preferably 0.0001% or more and 0.0002% or more.
  • the B content is set to 0.0100% or less.
  • the B content is preferably 0.0050% or less.
  • Ca 0.0005 to 0.0200%
  • Mg 0.0005 to 0.0200%
  • REM 0.0005 to 0.1000%
  • Bi 0.0005 to 0.020%
  • Ca, Mg and REM all have an effect of improving the formability of the hot-rolled steel sheet by adjusting the shape of the inclusions to a preferable shape.
  • Bi has an effect of improving the formability of the hot-rolled steel sheet by refining the solidified structure. Therefore, one or more of these elements may be contained.
  • any one or more of Ca, Mg, REM and Bi is 0.0005% or more.
  • the Ca content or Mg content exceeds 0.0200%, or when the REM content exceeds 0.1000%, inclusions are excessively formed in the steel, and on the contrary, the hole expandability of the hot-rolled steel sheet. May decrease.
  • the Bi content exceeds 0.020%, the effect of the above action is saturated, which is economically unfavorable. Therefore, the Ca content and Mg content are 0.0200% or less, the REM content is 0.1000% or less, and the Bi content is 0.020% or less.
  • the Bi content is preferably 0.010% or less.
  • REM refers to a total of 17 elements composed of Sc, Y and lanthanoid, and the content of REM refers to the total content of these elements.
  • lanthanoids they are industrially added in the form of misch metal.
  • the present inventors have confirmed that the effect of the hot-rolled steel sheet according to the present embodiment is not impaired even if a small amount of Sn is contained. However, if a large amount of Sn is contained, defects may occur during hot rolling, so the Sn content is set to 0.050% or less.
  • the chemical composition of the hot-rolled steel sheet described above may be measured by a general analysis method.
  • ICP-AES Inductively Coupled Plasma-Atomic Emission Spectrometry
  • sol. Al may be measured by ICP-AES using a filtrate obtained by heat-decomposing the sample with an acid.
  • C and S may be measured by using the combustion-infrared absorption method, and N may be measured by using the inert gas melting-thermal conductivity method.
  • the metal structures of martensite and tempered martensite are more than 92.0% and 100.0% or less in total, the retained austenite is less than 3.0%, and ferrite.
  • the metal structure of the cross section parallel to the rolling direction at a depth of 1/4 of the plate thickness from the surface and at the center position in the plate width direction is defined.
  • the reason is that the metallographic structure at this position represents a typical metallographic structure of the steel sheet.
  • the position of 1/4 depth from the surface to the plate thickness is a region from 1/8 depth from the surface to 3/8 depth from the surface to the plate thickness.
  • Retained austenite is a tissue that exists as a face-centered cubic lattice even at room temperature. Residual austenite has the effect of increasing the ductility of hot-rolled steel sheets due to transformation-induced plasticity (TRIP). On the other hand, retained austenite transforms into high-carbon martensite during shearing, which hinders stable crack generation and causes large irregularities in the fracture surface on the end face after shearing.
  • TRIP transformation-induced plasticity
  • the surface integral of the retained austenite is 3.0% or more, the above-mentioned action becomes apparent, and not only the shearing workability of the hot-rolled steel sheet deteriorates (the unevenness of the fracture surface on the end face becomes large), but also the hole expanding property also deteriorates. .. Therefore, the surface integral of retained austenite is less than 3.0%.
  • the surface integral of retained austenite is preferably less than 1.0%. Since the smaller the retained austenite, the more preferable it is, the surface integral of the retained austenite may be 0%.
  • Ferrite is generally a soft structure. If a predetermined amount or more of ferrite is contained, not only the desired strength cannot be obtained, but also the region of the sheared surface on the end face after shearing is increased. If the area of the sheared surface on the end face after shearing is increased, the unevenness of the fracture surface becomes large, which is not preferable.
  • the surface integral of ferrite is 5.0% or more, the above action becomes apparent and the shearing workability of the hot-rolled steel sheet deteriorates. Therefore, the surface integral of ferrite is set to less than 5.0%.
  • the surface integral of ferrite is preferably less than 1.0%. Since the smaller the amount of ferrite, the more preferable it is, the surface integral of ferrite may be 0%.
  • Methods for measuring the area fraction of retained austenite include X-ray diffraction, EBSP (electron backscatter diffraction image, Electron Backscattering Diffraction Pattern) analysis, and magnetic measurement methods, and the measured values may differ depending on the measurement method. ..
  • the surface integral of retained austenite is measured by X-ray diffraction.
  • the depth of 1/4 of the plate thickness of the steel plate (from the depth of 1/8 of the plate thickness to the depth of 3/8 of the plate thickness from the surface to the plate thickness).
  • ⁇ (110), ⁇ (200), ⁇ (211), ⁇ (111), ⁇ ( The integrated intensity of a total of 6 peaks of 200) and ⁇ (220) is obtained, and the area fraction of retained austenite is obtained by calculating using the intensity averaging method.
  • the surface integral of ferrite is measured by the following method.
  • the cross section perpendicular to the rolling direction is mirror-finished and polished at room temperature with colloidal silica containing no alkaline solution for 8 minutes to remove the strain introduced into the surface layer of the sample.
  • an EBSD analyzer composed of a thermal field emission scanning electron microscope (JSM-7001F manufactured by JEOL) and an EBSD detector (DVC5 type detector manufactured by TSL) is used.
  • the degree of vacuum in the EBSD analyzer is 9.6 ⁇ 10-5 Pa or less
  • the acceleration voltage is 15 kV
  • the irradiation current level is 13
  • the electron beam irradiation level is 62.
  • the Grain Average Simulation value is 1.0 °.
  • the following regions are determined to be ferrite.
  • the surface integral of ferrite is obtained by obtaining the surface integral of the region determined to be ferrite.
  • Total area fraction of martensite and tempered martensite More than 92.0% and 100.0% or less
  • the total area fraction of martensite and tempered martensite is 92.0% or less. If there is, the desired strength cannot be obtained. Therefore, the total surface integral of martensite and tempered martensite is more than 92.0%. It is not necessary to include both martensite and tempered martensite, and when either martensite or tempered martensite is included, the surface integral ratio may be more than 92.0%. When both martensite and tempered martensite are included, the total surface integral of martensite and tempered martensite may be more than 92.0%.
  • the total surface integral of martensite and tempered martensite is preferably 95.0% or more, 97.0% or more, and 99.0% or more.
  • the method for measuring the surface integral of martensite and tempered martensite will be described below.
  • a Vickers indentation is imprinted in the vicinity of the observation position.
  • the contamination on the surface layer is removed by polishing, leaving the structure of the observation surface, and nightal etching is performed.
  • the same field of view as the EBSD observation surface is observed by SEM at a magnification of 3000 times.
  • the region having a substructure in the grain and where cementite is precipitated with a plurality of variants is determined to be tempered martensite.
  • the region where the brightness is high and the substructure is not exposed by etching is judged as "martensite and retained austenite”.
  • the area fraction of martensite can be obtained by subtracting the area fraction of retained austenite obtained by the above-mentioned X-ray diffraction from the area fraction of the obtained "martensite and retained austenite".
  • a method such as buffing using alumina particles having a particle size of 0.1 ⁇ m or less or Ar ion sputtering may be used.
  • the matrix In order to obtain a hot-rolled steel sheet having a tensile strength of S 60 / S 7 of more than 0.34 and less than 0.60 and 980 MPa or more, the matrix must have a hard structure.
  • a hard structure is generally formed in a phase transformation of 600 ° C. or lower, but in this temperature range, a grain boundary with a crystal orientation difference of 60 ° and a crystal orientation difference of 7 ° with the ⁇ 110> direction as the axis. A large number of grain boundaries are formed.
  • the density of the grain boundaries having a crystal orientation difference of 60 ° with respect to the ⁇ 110> direction is high, and the grain boundaries are uniformly dispersed (that is, the grain boundaries having a crystal orientation difference of 60 ° with respect to the ⁇ 110> direction).
  • the strength of the material is increased, plastic deformation in shearing is suppressed, and unevenness of the fracture surface on the end face after shearing is suppressed.
  • the density of the length of the grain boundary having a crystal orientation difference of 60 ° is defined as S 60
  • the density of the length of the grain boundary having a crystal orientation difference of 7 ° is defined as S 7 with the ⁇ 110> direction as the axis.
  • S 60 / S 7 is set to more than 0.34. Preferably, it is 0.40 or more and 0.45 or more. In order to suppress the unevenness of the fracture surface on the end face after shearing, it is desirable that S 60 / S 7 is larger, but the practical upper limit is 0.60. Therefore, S 60 / S 7 is set to less than 0.60.
  • the grain boundary having a crystal orientation difference of X ° with respect to the ⁇ 110> direction means that when two adjacent crystal grains A and crystal grains B are specified at a certain grain boundary, one crystal grain B is defined as ⁇ . 110> refers to a grain boundary having a crystal boundary in which the crystal orientations of the crystal grains A and the crystal grains B are the same when rotated by X ° about the axis. However, considering the measurement accuracy of the crystal orientation, an orientation difference of ⁇ 4 ° is allowed from the matching orientation relation.
  • the density S 7 of the length of the grain boundary density S 60 and the crystal orientation difference of grain boundary length crystal orientation difference of 60 ° is 7 °
  • EBSP -Measurement is performed using the OIM (Electron Backscatter Diffraction Pattern-Orientation Image Microscope) method.
  • OIM Electro Backscatter Diffraction Pattern-Orientation Image Microscope
  • a highly inclined sample is irradiated with an electron beam in a scanning electron microscope (SEM), the Kikuchi pattern formed by backscattering is photographed with a high-sensitivity camera, and the photographed photograph is image-processed by a computer. By doing so, the crystal orientation of the irradiation point can be measured in a short waiting time.
  • the EBSP-OIM method is performed using an EBSD analyzer composed of a thermal field emission scanning electron microscope (JSM-7001F manufactured by JEOL) and an EBSD detector, and an OIM Analysis (registered trademark) manufactured by AMETEK.
  • JSM-7001F thermal field emission scanning electron microscope
  • EBSD detector an OIM Analysis (registered trademark) manufactured by AMETEK.
  • OIM Analysis registered trademark manufactured by AMETEK.
  • the analyzable area of the EBSP-OIM method is an area that can be observed by SEM. Although it depends on the resolution of the SEM, according to the EBSP-OIM method, analysis can be performed with a minimum resolution of 20 nm.
  • S 7 is obtained by dividing the average value of the lengths of the grain boundaries having a crystal orientation difference of 7 ° about the ⁇ 110> direction by the area of the measurement region. As described above, a directional difference of ⁇ 4 ° is allowed.
  • retained austenite is not a structure generated by phase transformation at 600 ° C. or lower and has no effect of dislocation accumulation, retained austenite is not included in the analysis in this measurement method. That is, in this embodiment, ⁇ 110> direction as an axis, the density of grain boundary length density S 60 and the crystal orientation difference of grain boundary length crystal orientation difference of 60 ° is 7 ° S 7 Are of martensite, tempered martensite and ferrite. In the EBSP-OIM method, retained austenite having a crystal structure of fcc can be excluded from the analysis target.
  • Standard deviation of Mn concentration 0.60% by mass or less 1/4 depth from the surface of the hot-rolled steel sheet according to the present embodiment (1/8 depth from the surface to the surface)
  • the standard deviation of the Mn concentration at the center position in the plate width direction is 0.60 mass% or less.
  • the standard deviation of the Mn concentration is preferably 0.55% by mass or less, 0.50% by mass or less, and 0.40% by mass or less.
  • the lower limit of the standard deviation of the Mn concentration is desirable as the value is smaller because it suppresses the unevenness of the fracture surface on the end face after shearing, but the practical lower limit is 0.10% by mass due to the restrictions of the manufacturing process. ..
  • the standard deviation of the Mn concentration is measured by the following method. After mirror-polishing the L cross section of the hot-rolled steel sheet, the depth from the surface to 1/4 of the plate thickness (the region from the surface to the depth of 1/8 of the plate thickness to the region from the surface to the depth of 3/8 of the plate thickness) and the plate width. The center position in the direction is measured with an electron probe microanalyzer (EPMA) to measure the standard deviation of the Mn concentration.
  • the measurement conditions are that the acceleration voltage is 15 kV, the magnification is 5000 times, and the distribution image in the range of 20 ⁇ m in the sample rolling direction and 20 ⁇ m in the sample plate thickness direction is measured. More specifically, the measurement interval is set to 0.1 ⁇ m, and the Mn concentration at 40,000 or more points is measured.
  • the standard deviation of the Mn concentration is obtained by calculating the standard deviation based on the Mn concentration obtained from all the measurement points.
  • the mechanism of internal bending cracking is presumed as follows. During bending, compressive stress is generated inside the bend. At first, the entire inside of the bend is deformed uniformly while processing proceeds, but when the amount of processing increases, the deformation cannot be carried out only by uniform deformation, and the deformation progresses due to the local concentration of strain (generation of shear deformation zone). .. As this shear band grows further, cracks along the shear band are generated from the inner surface of the bend and grow.
  • in-bending cracks are more likely to occur as the strength increases is that uniform deformation is less likely to proceed due to the decrease in work hardening ability due to the increase in strength, and biased deformation is likely to occur at an early stage of processing ( It is presumed that a shear band is generated (or under loose processing conditions).
  • the internal bending crack becomes remarkable in the steel sheet having a tensile strength of 980 MPa or more. Further, the present inventors have found that the finer the crystal grain size of the surface layer of the hot-rolled steel sheet, the more the local strain concentration is suppressed and the less likely it is that internal bending cracks occur.
  • the average crystal grain size of the surface layer of the hot-rolled steel sheet is preferably less than 3.0 ⁇ m. More preferably, it is 2.5 ⁇ m or less. The lower limit is not particularly limited, but may be 1.0 ⁇ m or more, 1.5 ⁇ m or more, or 2.0 ⁇ m or more.
  • the surface layer is a region from the surface of the hot-rolled steel sheet to a depth of 50 ⁇ m from the surface.
  • the crystal grain size of the surface layer is measured using the above-mentioned EBSP-OIM method.
  • analysis was performed in a region of 1200 times magnification and 40 ⁇ m ⁇ 30 ⁇ m in at least 5 visual fields.
  • a place where the angle difference between adjacent measurement points is 5 ° or more is defined as a grain boundary, and the crystal grain size of the area average is calculated.
  • the obtained area average crystal grain size is defined as the average crystal grain size of the surface layer.
  • Retained austenite is not a structure generated by phase transformation at 600 ° C or lower and has no effect of dislocation accumulation. Therefore, retained austenite is not included in the analysis in this measurement method. That is, in the present embodiment, the average crystal grain size of the surface layer is that of martensite, tempered martensite and ferrite. In the EBSP-OIM method, retained austenite having a crystal structure of fcc can be excluded from the analysis target.
  • the hot-rolled steel sheet according to this embodiment has a tensile (maximum) strength of 980 MPa or more. If the tensile strength is less than 980 MPa, the applicable parts are limited, and the contribution of weight reduction of the vehicle body is small.
  • the upper limit is not particularly limited, but may be 1780 MPa from the viewpoint of suppressing mold wear.
  • Tensile strength is measured in accordance with JIS Z 2241: 2011 using JIS Z 2241: 2011 No. 5 test piece.
  • the sampling position of the tensile test piece may be 1/4 from the end in the plate width direction, and the direction perpendicular to the rolling direction may be the longitudinal direction.
  • the hot-rolled steel sheet according to the present embodiment preferably has a hole expansion ratio ⁇ of 62% or more.
  • the hole expansion ratio ⁇ is 62% or more, the applicable parts are not limited, and a hot-rolled steel sheet that greatly contributes to weight reduction of the vehicle body can be obtained.
  • the upper limit does not have to be limited.
  • the hole expansion ratio ⁇ is measured in accordance with JIS Z 2256: 2010 using a No. 5 test piece of JIS Z 2241: 2011.
  • the sampling position of the hole expansion test piece may be 1/4 from the end in the plate width direction.
  • the product (TS ⁇ ⁇ ) of the tensile strength, which is an index of the hole expanding property, and the hole expanding property is preferably 60,000 MPa ⁇ % or more.
  • the applicable parts are not limited, and a hot-rolled steel sheet that greatly contributes to weight reduction of the vehicle body can be obtained.
  • the plate thickness of the hot-rolled steel sheet according to the present embodiment is not particularly limited, but may be 0.5 to 8.0 mm.
  • the thickness of the hot-rolled steel sheet according to the present embodiment may be 0.5 mm or more. It is preferably 1.2 mm or more and 1.4 mm or more.
  • the plate thickness may be 8.0 mm or less. It is preferably 6.0 mm or less.
  • the hot-rolled steel sheet according to the present embodiment having the above-mentioned chemical composition and metal structure may be provided with a plating layer on the surface for the purpose of improving corrosion resistance or the like to be a surface-treated steel sheet.
  • the plating layer may be an electroplating layer or a hot-dip plating layer.
  • the electroplating layer include electrogalvanization and electroZn—Ni alloy plating.
  • the hot-dip plating layer include hot-dip zinc plating, alloyed hot-dip zinc plating, hot-dip aluminum plating, hot-dip Zn-Al alloy plating, hot-dip Zn-Al-Mg alloy plating, and hot-dip Zn-Al-Mg-Si alloy plating.
  • NS hot-dip zinc plating, alloyed hot-dip zinc plating, hot-dip aluminum plating, hot-dip Zn-Al alloy plating, hot-dip Zn-Al-Mg alloy plating, and hot-dip Zn-Al-Mg-Si alloy plat
  • the amount of plating adhesion is not particularly limited and may be the same as before. Further, it is also possible to further enhance the corrosion resistance by subjecting an appropriate chemical conversion treatment (for example, application and drying of a silicate-based chromium-free chemical conversion treatment liquid) after plating.
  • an appropriate chemical conversion treatment for example, application and drying of a silicate-based chromium-free chemical conversion treatment liquid
  • the slab is heated under predetermined conditions and then hot-rolled, accelerated and cooled to a predetermined temperature range, and the cooling history after winding is controlled. Is effective.
  • the following steps (1) to (7) are sequentially performed.
  • the temperature of the slab and the temperature of the steel plate in this embodiment refer to the surface temperature of the slab and the surface temperature of the steel plate.
  • the slab is held in a temperature range of 700 to 850 ° C. for 900 seconds or longer, then further heated and held in a temperature range of 1100 ° C. or higher for 6000 seconds or longer.
  • Hot rolling is performed in a temperature range of 850 to 1100 ° C. so that the total plate thickness is reduced by 90% or more.
  • Hot rolling is completed so that the hot rolling completion temperature Tf becomes equal to or higher than the temperature T1 (° C.) represented by the following formula ⁇ 1>.
  • Acceleration cooling is started within 1.5 seconds after the completion of hot rolling, and the average cooling rate up to the temperature range of temperature T2 (° C) or lower represented by the following formula ⁇ 2> is 30 ° C / s or more. And. More preferably, it is cooled to a temperature range of the hot rolling completion temperature Tf-50 ° C. or lower within 1.0 second after the completion of hot rolling. (5) Cool from T2 (° C.) to the winding temperature at an average cooling rate of 30 ° C./s or more. (6) The winding temperature is set to a temperature range of 300 ° C. or lower.
  • T1 (° C.) 868-396 x [C] -68.1 x [Mn] + 24.6 x [Si] -36.1 x [Ni] -24.8 x [Cr] -20.7 x [Cu] ] + 250 ⁇ [sol. Al] ... ⁇ 1>
  • T2 (° C.) 770-270 x [C] -90 x [Mn] -37 x [Ni] -70 x [Cr] -83 x [Mo] ... ⁇ 2>
  • the [element symbol] in each formula indicates the content (mass%) of each element in steel. If the element is not contained, 0 is substituted.
  • the slab to be subjected to hot rolling is held in a temperature range of 700 to 850 ° C. during heating for 900 seconds or longer, and then further heated and held in a temperature range of 1100 ° C. or higher for 6000 seconds or longer.
  • the temperature of the steel sheet may be changed in this temperature range or may be constant.
  • the temperature of the steel sheet may be changed in the temperature range of 1100 ° C. or higher, or may be constant.
  • Mn is dispersed between the ferrite and the austenite, and the transformation time is lengthened so that Mn can be diffused in the ferrite region.
  • the Mn microsegregation unevenly distributed in the slab can be eliminated, and the standard deviation of the Mn concentration can be significantly reduced.
  • the grain boundaries having a crystal orientation difference of 60 ° about the ⁇ 110> direction can be uniformly dispersed in the final metal structure, and the end face after shearing can be uniformly dispersed.
  • the unevenness of the fracture surface can be reduced.
  • Hot rolling reduction rate A total plate thickness reduction of 90% or more in the temperature range of 850 to 1100 ° C.
  • the grain boundaries having a crystal orientation difference of 60 ° about the ⁇ 110> direction can be uniformly dispersed in the final metal structure, and the end face after shearing can be uniformly dispersed.
  • the unevenness of the fracture surface can be reduced. Therefore, hot rolling is performed so that the total plate thickness is reduced by 90% or more in the temperature range of 850 to 1100 ° C.
  • the plate thickness reduction in the temperature range of 850 to 1100 ° C. means the inlet plate thickness t 0 before the first pass in rolling in this temperature range, and the outlet plate thickness after the final pass in rolling in this temperature range is t 1 When, it can be expressed as (t 0 ⁇ t 1 ) / t 0 ⁇ 100 (%).
  • Hot rolling completion temperature Tf T1 (° C.) or higher
  • the hot rolling completion temperature Tf is preferably T1 (° C.) or higher.
  • Accelerated cooling after completion of hot rolling Accelerated cooling is started within 1.5 seconds, and the average cooling rate up to T2 (° C) is 30 ° C / s or more. In order to suppress the growth of the austenite crystal grains that have been granulated, it is preferable to perform accelerated cooling to T2 (° C.) or less at an average cooling rate of 30 ° C./s or more within 1.5 seconds after the completion of hot rolling.
  • the formation of ferrite and pearlite can be suppressed by accelerating cooling to T2 (° C) or lower at an average cooling rate of 30 ° C./s or higher within 1.5 seconds after the completion of hot rolling. This improves the strength of the hot-rolled steel sheet.
  • the average cooling rate referred to here is the temperature drop width of the steel sheet from the start of accelerated cooling (when the steel sheet is introduced into the cooling equipment) to T2 (° C.), and the temperature of the steel sheet is T2 (° C.) from the start of accelerated cooling. ) Divided by the time required to reach.
  • the time until the start of cooling is set to 1.5 seconds or less, and the average cooling rate up to T2 (° C) or less is set to 30 ° C / s or more, so that the ferrite transformation inside the steel sheet is performed. And / or bainite transformation and / or pearlite transformation can be suppressed, and TS ⁇ 980 MPa can be obtained. Therefore, within 1.5 seconds after the completion of hot rolling, accelerated cooling is performed so that the average cooling rate up to T2 (° C.) is 30 ° C./s or more.
  • the upper limit of the average cooling rate is not specified, but if the cooling rate is increased, the cooling equipment becomes large and the equipment cost increases. Therefore, considering the equipment cost, the average cooling rate of accelerated cooling is preferably 300 ° C./s or less. Further, the cooling shutdown temperature of accelerated cooling is preferably 350 ° C. or lower.
  • the hot rolling completion temperature Tf-50 ° C. For cooling after the completion of hot rolling, it is more preferable to cool to a temperature range of the hot rolling completion temperature Tf-50 ° C. within 1.0 second after the completion of hot rolling. This is because the growth of austenite crystal grains finely divided by hot rolling can be suppressed.
  • cooling with a large average cooling rate is performed immediately after the completion of hot rolling, for example, cooling water. May be sprayed onto the surface of the steel sheet.
  • the average cooling rate to T2 (° C) or less is set to 30 ° C / s as described above. Accelerated cooling may be performed as described above.
  • the average cooling rate from T2 (° C.) to the take-up temperature is 30 ° C./s or more.
  • T2 (° C.) The average cooling rate from bainite to winding temperature is preferably 30 ° C./s or more. As a result, the matrix structure can be made hard.
  • the average cooling rate here is a value obtained by dividing the temperature drop width of the steel sheet from T2 (° C.) to the winding temperature by the time required from when the steel sheet temperature reaches T2 (° C.) to winding. It means that.
  • the average cooling rate from T2 (° C.) to the winding temperature is set to 30 ° C./s or more.
  • the winding temperature is preferably 300 ° C. or lower.
  • the transformation driving force from austenite to bcc can be increased, and the deformation strength of austenite can be increased. Therefore, when transforming from austenite to bainite and martensite, the density S 60 of the grain boundary length with a crystal orientation difference of 60 ° about the ⁇ 110> direction can be suppressed, and S 60 / S 7 is 0.60. Can be less than. As a result, the unevenness of the fracture surface on the end face after shearing can be reduced. In addition, it is possible to suppress a decrease in hole-spreading property due to the influence of retained austenite. Therefore, the winding temperature is preferably 300 ° C. or lower. The winding temperature is more preferably 50 ° C. or lower.
  • the conditions in the examples are one condition example adopted for confirming the feasibility and effect of the present invention.
  • the present invention is not limited to this one-condition example.
  • the present invention can adopt various conditions as long as the gist of the present invention is not deviated and the object of the present invention is achieved.
  • the slab was held in a temperature range of 700 to 850 ° C. for the holding times shown in Tables 3A and 3B, and then further heated to the heating temperatures shown in Tables 3A and 3B. Further, accelerated cooling was started within 1.5 seconds after the completion of hot rolling.
  • the area fraction of each structure, S 60 / S 7 , standard deviation of Mn concentration, and average crystal grain size of the surface layer were determined by the above-mentioned method.
  • the obtained measurement results are shown in Table 4A and Table 4B.
  • Shear workability The shear workability of the hot-rolled steel sheet was evaluated by measuring the size of the unevenness of the fracture surface on the end face after shearing by a punching test. Five punched holes were prepared with a hole diameter of 10 mm, a clearance of 10%, and a punching speed of 3 m / s. Next, with respect to the five punched holes, ten cross sections parallel to the rolling direction were embedded in the resin, and the cross-sectional shapes were photographed with a scanning electron microscope. In the obtained observation photograph, it was possible to observe the processed cross section composed of the sagging, the sheared surface, the fracture surface and the burr as shown in FIG.
  • the sagging is an area of an R-shaped smooth surface
  • the shearing surface is an area of a punched end surface separated by shear deformation
  • the fracture surface is a punching separated by cracks generated from the vicinity of the cutting edge after the completion of shear deformation. It is a region of an end surface
  • a burr is a surface having protrusions protruding from the lower surface of a hot-rolled steel sheet.
  • the size of the unevenness of the fracture surface is measured for 10 end faces obtained from the 5 punched holes, and if the maximum value of the unevenness of the fracture surface is 3.0 ⁇ m or less, the shearing workability is excellent. It was judged as passing. On the other hand, if the maximum value of the unevenness of the fracture surface exceeds 3.0 ⁇ m, it is judged to be inferior in shearing workability and rejected.
  • the bending test piece is obtained by cutting out a strip-shaped test piece of 100 mm ⁇ 30 mm from the 1/2 position in the plate width direction of the hot-rolled steel sheet, and evaluating the bending internal crack resistance by the following bending test. did.
  • JIS Z for both bending where the bending ridge is parallel to the rolling direction (L direction) (L-axis bending) and bending where the bending ridge is parallel to the direction perpendicular to the rolling direction (C direction) (C-axis bending). 2248: 2014 (V block 90 ° bending test) was investigated to determine the bending internal crack resistance, the minimum bending radius without cracks was obtained, and the average value R of the minimum bending radii of the L and C axes was calculated as the plate thickness. The value divided by t was defined as the limit bending R / t and used as the index value of bendability. When R / t ⁇ 3.0, it was judged that the hot-rolled steel sheet had excellent bending resistance and internal cracking resistance.
  • the presence or absence of cracks is determined by mirror-polishing the cross section of the test piece after the V block 90 ° bending test cut on a surface parallel to the bending direction and perpendicular to the plate surface, and then observing the cracks with an optical microscope. When the crack length observed inside the bend exceeds 30 ⁇ m, it is judged that there is a crack. The obtained measurement results are shown in Table 4A and Table 4B.
  • the production No. whose chemical composition and metal structure are not within the range specified in the present invention. 3 to 5, 7 to 10 and 24 to 27 were inferior in any one or more of the characteristics (tensile strength TS, hole expansion ratio ⁇ , shear workability).
  • the present invention it is possible to provide a hot-rolled steel sheet having excellent strength, drilling property and shearing workability. Further, according to the above-mentioned preferred embodiment according to the present invention, it is possible to obtain a hot-rolled steel sheet having the above-mentioned characteristics and further suppressing the occurrence of bending internal cracks, that is, having excellent bending internal crack resistance. can.
  • the hot-rolled steel sheet according to the present invention is suitable as an industrial material used for automobile members, mechanical structural members, and building members.

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  • Physics & Mathematics (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)
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CN202080093028.8A CN114929915B (zh) 2020-01-27 2020-12-11 热轧钢板
US17/790,645 US12392020B2 (en) 2020-01-27 2020-12-11 Hot-rolled steel sheet
EP20916444.1A EP4098762B1 (en) 2020-01-27 2020-12-11 Hot-rolled steel sheet
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EP4417714A4 (en) * 2021-10-11 2025-05-28 Nippon Steel Corporation HOT ROLLED STEEL SHEET
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