WO2013111556A1 - Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci - Google Patents

Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci Download PDF

Info

Publication number
WO2013111556A1
WO2013111556A1 PCT/JP2013/000257 JP2013000257W WO2013111556A1 WO 2013111556 A1 WO2013111556 A1 WO 2013111556A1 JP 2013000257 W JP2013000257 W JP 2013000257W WO 2013111556 A1 WO2013111556 A1 WO 2013111556A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
steel sheet
rolled steel
hot
strength
Prior art date
Application number
PCT/JP2013/000257
Other languages
English (en)
Japanese (ja)
Inventor
典晃 ▲高▼坂
船川　義正
重見　將人
英和 大久保
篤謙 金村
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to JP2013555188A priority Critical patent/JP5565534B2/ja
Priority to KR1020147019785A priority patent/KR20140103340A/ko
Priority to US14/374,124 priority patent/US20150030880A1/en
Priority to EP13740782.1A priority patent/EP2808413B1/fr
Priority to CN201380005846.8A priority patent/CN104053806B/zh
Publication of WO2013111556A1 publication Critical patent/WO2013111556A1/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • 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
    • C22C38/001—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
    • C22C38/007—Ferrous alloys, e.g. steel alloys containing silver
    • 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
    • C22C38/10—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
    • C22C38/18—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • 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
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present invention relates to a high-strength hot-rolled steel sheet having high tensile strength (TS): 980 MPa or more and excellent workability (particularly bending workability) useful for the use of automobile members and a method for producing the same.
  • TS tensile strength
  • Patent Document 1 proposes a technique for making a steel plate composition containing C: 0.05 to 0.20% by mass%, Nb: 0.1 to 1.0%, and having a solid solution C content of 0.03% or less. ing. And according to the technique proposed in Patent Document 1, by limiting the amount of dissolved C in the component system containing Nb and C, the matrix is a soft ferrite phase and the matrix is a hard second phase. It is said that a certain NbC-dispersed steel sheet structure is obtained, and a wear-resistant steel sheet having excellent bending workability is obtained.
  • the steel sheet composition is in mass%, C: 0.02 to 0.2%, Si: 0.01 to 1.0%, Mn: 0.1 to 2.0%, P: 0.2% or less, sol.Al: 0.001 to 0.5%, Ti: 0.1% or less, Nb: 0.1% or less, V: 0.5% or less, Mo: 0.5% or less, and Ti + Nb: 0.1% or less, steel sheet structure as ferrite main phase structure, and steel sheet surface
  • a technique for defining the average grain size of ferrite at a depth of 1/4 of the plate thickness and the rate of increase of the average grain size at 700 ° C. has been proposed. And according to the technique proposed by patent document 2, it is supposed that the steel plate excellent in workability will be obtained.
  • the technique proposed in Patent Document 1 substantially strengthens the steel sheet by dispersing NbC, and it is difficult to obtain a steel sheet having a tensile strength of 980 MPa or more with the technique using NbC. .
  • the amount of particle dispersion strengthening obtained by dispersing precipitates increases with an increase in the carbonized body volume fraction, but NbC increases the carbonized body volume fraction because its solubility product in steel is small and the atomic density is large. It is because it cannot be done.
  • Ti and V are added as precipitation strengthening elements to steel, but the contents of Ti and V forming carbides are small, or appropriate addition is not made. After all, the tensile strength of the steel sheet does not reach 980 MPa.
  • an object of the present invention is to provide a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more and excellent bending workability.
  • the present inventors focused on a technique for strengthening by dispersing fine carbides in a ferrite single-structure steel plate having good workability.
  • various factors affecting bending workability were studied.
  • the inventors of the present invention are extremely effective to disperse fine carbides in the ferrite phase in order to make the originally soft ferrite phase into a hard ferrite single-structure steel sheet.
  • Ti is the most suitable element.
  • the present inventors examined a means for imparting excellent bending workability while maintaining the steel plate strength of the high strength hot rolled steel plate having a tensile strength of 980 MPa or more to which Ti and V are added in combination as described above.
  • the surface properties of the steel sheet surface ⁇ appearance quality
  • the amount of solid solution elements and voids that are the starting points of voids that reduce the workability of the steel plate are reduced as much as possible. I found out that it was necessary.
  • the tensile strength is 980 MPa or more and It has been found that a hot-rolled steel sheet having excellent bending workability can be obtained.
  • the present invention has been completed based on the above findings, and the gist thereof is as follows.
  • the ferrite phase has an area ratio of 95% or more, the ferrite phase has an average crystal grain size of 8 ⁇ m or less, and the ferrite grain has an average grain size of less than 10 nm, and a tensile strength of 980 MPa.
  • the composition further contains at least one of Mo, W, Zr, and Hf. : 0.05% or less, Zr: 0.05% or less, Hf: High-strength hot-rolled steel sheet excellent in bendability characterized by being limited to 0.05% or less.
  • Heating the steel material subjecting it to hot rolling consisting of rough rolling and finish rolling, cooling after completion of finish rolling, winding, and hot rolling steel sheet,
  • the steel material in mass%, C: 0.06% to 0.1%, Si: 0.09% or less, Mn: 0.7% or more and 1.3% or less, P: 0.03% or less, S: 0.01% or less, Al: 0.1% or less, N: 0.01% or less, Ti: 0.14% to 0.20% V: 0.07% or more and 0.14% or less, with the balance being Fe and inevitable impurities,
  • the heating temperature of the steel material is 1100 ° C. or more and 1350 ° C. or less
  • the finish rolling temperature of the finish rolling is 850 ° C.
  • a method for producing a high-strength hot-rolled steel sheet having excellent bendability characterized by being 20 ° C / s or higher and a coiling temperature of the winding of 550 ° C or higher and 700 ° C or lower.
  • the composition further contains at least one of Mo, W, Zr, and Hf, and the content thereof is Mo: 0.05% or less, W : 0.05% or less, Zr: 0.05% or less, and Hf: 0.05% or less.
  • a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more and excellent bending workability suitable for the use of structural members of automobiles can be obtained.
  • the effect is remarkable such as making it possible, and further application development of the high-strength hot-rolled steel sheet becomes possible, and there is a remarkable industrial effect.
  • the hot-rolled steel sheet of the present invention has a structure in which the area ratio of the ferrite phase is 95% or more, the average crystal grain size of the ferrite phase is 8 ⁇ m or less, and the average grain size of carbides in the ferrite phase crystal grains is less than 10 nm. Have.
  • the matrix metal structure of the hot-rolled steel sheet is preferably a ferrite single-phase structure excellent in workability.
  • a second phase structure such as a bainite phase, martensite phase, cementite, or pearlite is mixed into the steel sheet structure, voids are generated at the interface between the ferrite phase and the second phase structure, which have different hardnesses, and the bending workability of the steel sheet is reduced.
  • it is intended to ensure the desired strength of the steel sheet by precipitating carbides such as Ti and V in the steel sheet, but most of these carbides are finished in the finish rolling in the hot-rolled steel sheet manufacturing process.
  • the metal structure of the hot-rolled steel sheet is a ferrite single phase structure, but if the ferrite area ratio is 95% or more even if it is not completely a ferrite single phase, the desired strength (Tensile strength: 980 MPa or more) is obtained, so the area ratio of the ferrite phase is 95% or more. Preferably it is 98% or more.
  • examples of the structure other than the ferrite phase that can be contained in the steel sheet include cementite, pearlite, bainite phase, and martensite phase.
  • the steel sheet properties bending workability, etc.
  • Average grain size of ferrite phase 8 ⁇ m or less
  • the average grain size of ferrite exceeds 8 ⁇ m, it tends to be a mixed grain size microstructure. In the mixed grain structure, stress tends to concentrate on coarse ferrite grains during bending, so that the bending workability of the steel sheet is significantly reduced. Therefore, the upper limit of the average crystal grain size of the ferrite phase is 8 ⁇ m. Preferably it is 6 micrometers or less, More preferably, it is 4.5 micrometers or less.
  • Carbides in ferrite crystal grains in the hot-rolled steel sheet of the present invention it is essential to finely precipitate carbides in the ferrite phase crystal grains from the viewpoint of ensuring strength.
  • Examples of the carbide finely precipitated in the ferrite phase grains in the present invention include Ti carbide, V carbide, and Ti and V composite carbide, or those containing Nb, W, Mo, Hf, and Zr in the carbide. .
  • Most of these carbides are carbides that precipitate at the interface at the same time as the transformation from austenite to ferrite in the cooling process after finish rolling in the hot-rolled steel sheet manufacturing process.
  • Average particle diameter of carbides in ferrite crystal grains less than 10 nm
  • the aforementioned carbides mainly composite carbides of Ti and V
  • the carbides are fine.
  • the average particle size of the carbide dispersed in the ferrite crystal grains is set to less than 10 nm.
  • it is less than 7 nm, More preferably, it is 5 nm or less.
  • C 0.06% or more and 0.1% or less C is combined with Ti, V, or Nb and is finely distributed in the steel sheet as carbides. That is, C is an element that forms fine carbides and remarkably strengthens the ferrite structure, and is an essential element for strengthening the hot-rolled steel sheet. In order to obtain a high-strength steel sheet having a tensile strength of 980 MPa or more, the C content needs to be at least 0.06%.
  • the C content exceeds 0.1%, a large amount of cementite precipitates and the bending workability of the steel sheet is lowered. This is because microvoids are easily generated at the cementite / matrix (ferrite) interface, and these microvoids cause cracks in the bent portion of the steel sheet. Therefore, the C content is set to 0.06% or more and 0.1% or less. Preferably they are 0.07% or more and 0.09% or less.
  • Si 0.09% or less Si is positively contained in conventional high-strength steel sheets as an effective element for improving the steel sheet strength without reducing ductility (elongation).
  • Si is easy to concentrate on the steel sheet surface, and forms firelite (Fe 2 SiO 4 ) on the steel sheet surface. Since this firelite is formed in a wedge shape on the surface of the steel sheet, it becomes a starting point of cracking when the steel sheet is bent. Therefore, in the present invention, it is desirable to reduce the Si content as much as possible, but 0.09% is acceptable, so the upper limit of the Si content is 0.09%. Preferably it is 0.06% or less. Note that the Si content may be reduced to the impurity level.
  • Mn 0.7% or more and 1.3% or less Mn is an element effective for increasing the strength of a hot-rolled steel sheet in order to refine the carbides precipitated in the crystal grains of the ferrite phase.
  • Mn 0.7% or more and 1.3% or less Mn is an element effective for increasing the strength of a hot-rolled steel sheet in order to refine the carbides precipitated in the crystal grains of the ferrite phase.
  • Mn has the effect of lowering the transformation temperature from austenite to ferrite of steel, so by containing a predetermined amount of Mn, the transformation temperature is lowered to the coiling temperature range described later, Carbide can be deposited simultaneously with the winding of the steel sheet. And the carbide
  • the Mn content needs to be at least 0.7%.
  • the Mn content exceeds 1.3%, the workability of the steel sheet due to solute Mn is significantly reduced, so that the desired bending workability cannot be obtained. Therefore, the Mn content is 0.7% or more and 1.3% or less. Preferably they are 0.8% or more and 1.2% or less.
  • P 0.03% or less
  • P is a harmful element that segregates at the grain boundary and becomes the starting point of grain boundary cracking during processing, and degrades the bending workability of the steel sheet, so it is preferably reduced as much as possible. Therefore, in the present invention, the P content is set to 0.03% or less in order to avoid the above problems. Preferably it is 0.02% or less. The P content may be reduced to the impurity level.
  • S 0.01% or less S is present as an inclusion such as MnS in steel. Since the inclusions are hard, the interface between the matrix and the inclusions becomes a starting point of voids during bending of the steel sheet, thereby reducing the bending workability of the steel sheet. Therefore, in the present invention, it is preferable to reduce the S content as much as possible, and set it to 0.01% or less. Preferably it is 0.008% or less. There is no problem even if the S content is zero.
  • Al 0.1% or less
  • Al is an element that acts as a deoxidizer. In order to obtain such an effect, it is desirable to contain 0.02% or more. However, if the Al content exceeds 0.1%, an adverse effect on bending workability due to inclusions such as alumina becomes obvious. Therefore, the Al content is 0.1% or less. Preferably it is 0.08% or less.
  • N 0.01% or less N is combined with Ti, which is a carbide-forming element, at the steelmaking stage to form coarse Ti nitrides, which impede the formation of fine carbides and significantly reduce the steel sheet strength. Furthermore, voids are likely to occur at the interface between the matrix and coarse Ti nitride during bending of the steel sheet, which adversely affects the bending workability of the steel sheet. Therefore, the N content is preferably reduced as much as possible, and is 0.01% or less. Preferably it is 0.008% or less. There is no problem even if the N content is zero.
  • Ti 0.14% or more and 0.20% or less Ti is an element that contributes to increasing the strength of steel sheets by forming carbides with C.
  • the Ti content needs to be 0.14% or more.
  • coarse Ti carbide cannot be dissolved by heating the steel material (slab) before hot rolling, and finally obtained ( Coarse Ti carbide remains on the hot-rolled steel sheet after winding.
  • the Ti content is 0.14% or more and 0.20% or less. Preferably it is 0.15% or more and 0.19% or less.
  • V 0.07% or more and 0.14% or less
  • V is an element that contributes to increasing the strength of steel sheets by forming carbides with C.
  • V is effective for increasing the strength of the steel sheet because it combines with Ti to form a fine composite carbide.
  • the V content needs to be 0.07% or more.
  • V content when the V content is higher than the Ti content, V becomes difficult to precipitate and the amount of V remaining in the steel sheet as a solid solution state increases. Since V in a solid solution state deteriorates the bending workability of the steel sheet, the V content needs to be Ti content or less, that is, 0.14% or less. Therefore, the V content is 0.07% or more and 0.14% or less. Preferably they are 0.08% or more and 0.13% or less.
  • Nb 0.01% or more and 0.05% or less
  • the above is the basic component in the present invention.
  • Nb 0.01% or more and 0.05% or less may be further contained.
  • Nb has the effect of inhibiting the recrystallization of austenite grains before transformation from austenite to ferrite in the hot rolling process when producing a hot rolled steel sheet having a ferrite single-phase structure substantially to make an unrecrystallized structure There is. In the non-recrystallized structure, strain energy due to hot rolling is easily accumulated, and the number of nucleation sites of the ferrite phase increases.
  • the Nb content is preferably set to 0.01% or more.
  • the Nb content is preferably 0.05% or less. More preferably, it is 0.02% or more and 0.04% or less.
  • Mo 0.05% or less
  • W 0.05% or less
  • Zr 0.05% or less
  • Hf 0.05% or less
  • Mo, W, Zr, and Hf are elements that form carbides and contribute to increasing the strength of the steel sheet, but a large amount remains as a solid solution. These solid solution elements deteriorate the workability of the matrix and adversely affect the bending workability of the steel sheet.
  • Mo, W, Zr, and Hf have a low rate of precipitation with respect to the content, and a large amount remains in the steel sheet as a solid solution element. For this reason, it is desirable to reduce these contents as much as possible, but 0.05% is acceptable, so the upper limit was set to 0.05%. Preferably it is 0.03% or less. Note that the contents of Mo, W, Zr, and Hf may be zero.
  • a plating layer By forming a plating layer on the surface, the corrosion resistance of the hot-rolled steel sheet is improved, and it becomes possible to apply it to automobile parts used in severe corrosive environments.
  • the type of the plating layer is not particularly limited, and any of an electroplating layer and an electroless plating layer can be applied.
  • the alloy component of the plating layer is not particularly limited, and a hot dip galvanized layer, an alloyed hot dip galvanized layer and the like can be mentioned as suitable examples, but of course, it is not limited to these, and any conventionally known one can be applied. is there.
  • a steel material (steel slab) having the above composition is heated, subjected to hot rolling consisting of rough rolling and finish rolling, cooled after completion of finish rolling, and wound into a hot rolled steel sheet. Then, the heating temperature of the steel material is 1100 ° C. or more and 1350 ° C. or less, the finish rolling temperature of the finish rolling is 850 ° C. or more, and the cooling is started within 3 seconds after finishing the finish rolling, and the average cooling of the cooling The speed is 20 ° C./s or more, and the winding temperature of the winding is 550 ° C. or more and 700 ° C. or less.
  • the method for melting steel is not particularly limited, and a known melting method such as a converter or an electric furnace can be employed. Further, secondary refining may be performed in a vacuum degassing furnace. Thereafter, the slab (steel material) is preferably formed by a continuous casting method from the viewpoint of productivity and quality, but the slab may be formed by a known casting method such as an ingot-bundling rolling method or a thin slab continuous casting method. .
  • Heating temperature of steel material 1100 ° C or higher and 1350 ° C or lower
  • the steel material (steel slab) obtained as described above is subjected to rough rolling and finish rolling.
  • the steel material is heated prior to rough rolling. It is necessary to form a substantially homogeneous austenite phase and dissolve coarse carbides.
  • the heating temperature of the steel material is below 1100 ° C, coarse carbides do not dissolve, so the amount of carbides that are finely dispersed in the cooling and winding process after hot rolling is reduced, and the hot rolling finally obtained is reduced.
  • the strength of the steel sheet is significantly reduced.
  • the heating temperature exceeds 1350 ° C., the scale bites and deteriorates the surface appearance quality of the steel sheet.
  • the heating temperature of the steel material is set to 1100 ° C to 1350 ° C. Preferably they are 1150 degreeC or more and 1320 degrees C or less.
  • the steel material is heated. Direct rolling may be performed without any problem.
  • the rough rolling conditions are not particularly limited.
  • Finish rolling temperature 850 ° C or more
  • the finish rolling temperature is 850 ° C. or higher.
  • it is 870 degreeC or more.
  • the upper limit of the finish rolling temperature is not particularly defined, but the finish rolling temperature is determined by the slab reheating temperature, the sheet feed speed, and the steel plate thickness. Therefore, the upper limit of the finish rolling temperature is substantially 990 ° C. or less.
  • carbides are generated by strain-induced precipitation because the strain energy accumulated in the austenite phase is large. Since this carbide precipitates at a high temperature and is easy to coarsen, it is difficult to obtain a fine precipitate when strain-induced precipitation occurs. Therefore, in the present invention, for the purpose of suppressing strain-induced precipitation, it is necessary to start forced cooling immediately after the end of hot rolling, and cooling is started within 3 seconds at the latest after finishing rolling. Preferably it is within 2 seconds.
  • Average cooling rate 20 ° C./s or more
  • the longer the time that the steel sheet after finish rolling is maintained at a high temperature the more easily the coarsening of the carbide by strain-induced precipitation proceeds.
  • the austenite ⁇ ferrite transformation is suppressed by containing a predetermined amount of Mn in the steel sheet, but if the cooling rate is low, the ferrite transformation starts at a high temperature, and the carbide tends to become coarse. Therefore, it is necessary to rapidly cool after finish rolling, and in order to avoid the above problem, it is necessary to cool at an average cooling rate of 20 ° C./s or more.
  • a preferable average cooling rate is 40 ° C./s or more.
  • the cooling rate after finishing rolling is excessively increased, it is difficult to control the coiling temperature and it is difficult to obtain stable hot-rolled steel sheet strength. preferable.
  • Winding temperature 550 ° C. or higher and 700 ° C. or lower If the winding temperature is lower than 550 ° C., a sufficient amount of carbide cannot be obtained, and the steel sheet strength decreases. On the other hand, when the coiling temperature exceeds 700 ° C., the precipitated carbide is coarsened, so that the steel sheet strength is lowered. Accordingly, the coiling temperature range is 550 ° C. or higher and 700 ° C. or lower. Preferably they are 580 degreeC or more and 680 degrees C or less.
  • the hot-rolled steel sheet after being rolled by hot rolling does not change its properties even if the scale is attached to the surface or the scale is removed by pickling.
  • the above-described excellent characteristics are exhibited in any state.
  • the hot-rolled steel sheet after winding may be plated to form a plating layer on the surface of the hot-rolled steel sheet.
  • the hot-rolled steel sheet of the present invention has little material fluctuation even when subjected to heat treatment up to 740 ° C. for a short time. Therefore, for the purpose of imparting corrosion resistance to the steel sheet, the hot-rolled steel sheet of the present invention can be plated, and a plating layer can be provided on the surface thereof. Since it can be manufactured even at a heating temperature of 740 ° C. or lower in the plating process, the effect of the present invention described above is not impaired even if the hot-rolled steel sheet of the present invention is plated.
  • the type of the plating layer is not particularly limited, and any of an electroplating layer and an electroless plating layer can be applied.
  • the alloy component of the plating layer is not particularly limited, and a hot dip galvanized layer, an alloyed hot dip galvanized layer and the like can be mentioned as suitable examples, but of course, it is not limited to these, and any conventionally known one can be applied. is there.
  • the plating method is not particularly limited, and any conventionally known method can be applied.
  • a method of immersing and pulling up the steel plate in a plating bath may be used.
  • the steel plate surface may be heated in a furnace such as a gas furnace to perform the alloying treatment.
  • the ferrite phase area ratio is 95% or more, the average grain size of the ferrite phase is 8 ⁇ m or less, the ferrite phase of the ferrite phase A hot-rolled steel sheet having a structure in which the carbide average particle diameter in the crystal grains is less than 10 nm is obtained.
  • the solid solution elements and coarse inclusions present in the steel sheet are reduced, and the strength is increased, so that the high strength hot rolling excellent in bending workability is achieved. It can be a steel plate.
  • the content of carbide forming elements (Ti and V, or even Nb, W, Mo, Hf, Zr) contained in the steel sheet is optimized, and the production conditions for the hot rolled steel sheet are specified. .
  • the above-mentioned carbide having an average particle diameter of less than 10 nm can be sufficiently precipitated in the ferrite crystal grains, and the tensile strength of the hot-rolled steel sheet is increased to 980 MPa or more while maintaining excellent bending workability. be able to.
  • the present invention is preferably applied to a hot rolled steel sheet having a tensile strength of 1100 MPa or less, and more preferably applied to a hot rolled steel sheet having a tensile strength of 1052 MPa or less.
  • a steel material (steel slab) having a composition shown in Table 1 and having a thickness of 250 mm was hot rolled under the hot rolling conditions shown in Table 2 to obtain a hot rolled steel sheet having a thickness of 1.4 to 3.2 mm.
  • the cooling rate described in Table 2 is an average cooling rate from the finish rolling temperature to the winding temperature.
  • a part of the obtained hot-rolled steel sheet is passed through a hot dip galvanizing line with an annealing temperature of 720 ° C, and then immersed in a 460 ° C plating bath (plating composition: Zn-0.13 mass% Al).
  • a hot-dip galvanized material (GI material) was used.
  • Samples are taken from the hot-rolled steel sheet (hot-rolled steel sheet, GI material, GA material) obtained as described above, and subjected to structure observation, tensile test, and bending test.
  • the area ratio of the ferrite phase and the type of structure other than the ferrite phase The area ratio, the average crystal grain size of the ferrite phase, the average grain size of the carbide, the yield strength, the tensile strength, the elongation, and the critical bending radius were obtained.
  • the test method was as follows.
  • the area ratio of the ferrite phase was evaluated by the following method. The central portion of the plate thickness in the cross section parallel to the rolling direction was photographed for 10 fields of view by corroding the appearance of corrosion by 5% nital 400 times with a scanning optical microscope.
  • the ferrite phase is a structure having a form in which corrosion marks and cementite are not observed in the grains. Further, using polygonal ferrite, bainitic ferrite, acicular ferrite, and granular ferrite as ferrite, the area ratio of the ferrite phase, the average grain size of the ferrite phase, and the average grain size of the carbide in the crystal grains of the ferrite phase were derived.
  • the area ratio of the ferrite phase was obtained by separating the ferrite phase from the ferrite phase other than the ferrite phase such as bainite and martensite by image analysis, and obtaining the area ratio of the ferrite phase with respect to the observation field. At this time, the grain boundary observed as a linear form was counted as a part of the ferrite phase.
  • Table 3 shows the area ratio of the obtained ferrite phase.
  • the average crystal grain size of the ferrite phase was obtained by enlarging the above 400 times and taking three representative photographs by drawing three horizontal lines and three vertical lines, respectively, by a cutting method in accordance with ASTM E 112-10. Was the final average crystal grain size. Table 3 shows the average crystal grain size obtained.
  • the average particle size of the carbides in the ferrite phase grains was measured using a transmission electron microscope (magnification: 135000 times) by preparing a sample from the center of the thickness of the obtained hot rolled steel sheet using a thin film method. It calculated
  • All examples of the present invention are hot-rolled steel sheets having a tensile strength of TS: 980 MPa or more, excellent bending workability, and both strength and workability. On the other hand, it was found that the comparative example out of the scope of the present invention did not ensure a predetermined high strength or did not obtain good bending workability.
  • a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more and excellent bending workability suitable for the use of structural members of automobiles can be obtained. It becomes possible to achieve both.

Landscapes

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

Abstract

L'invention a pour objectif de fournir une tôle en acier laminée à chaud hautement résistante et le procédé de fabrication cette tôle qui combine d'excellentes propriétés de résistance et d'usinage (tout particulièrement, propriétés d'usinage par flexion). Afin d'atteindre cet objectif, l'objet de l'invention est caractéristique en ce qu'il présente une structure spécifique dans laquelle le rapport de surface d'une phase ferrite est supérieur ou égal à 95%, le diamètre moyen de grain cristallin dans la phase ferrite est inférieur ou égal à 8µm, et le diamètre de particule moyen d'un carbure à l'intérieur de grains cristallins dans la phase de ferrite est inférieur à 10nm. La résistance à la traction de l'objet de l'invention, est supérieure ou égale à 980MPa.
PCT/JP2013/000257 2012-01-26 2013-01-21 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci WO2013111556A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP2013555188A JP5565534B2 (ja) 2012-01-26 2013-01-21 高強度熱延鋼板及びその製造方法
KR1020147019785A KR20140103340A (ko) 2012-01-26 2013-01-21 고강도 열연 강판 및 그 제조 방법
US14/374,124 US20150030880A1 (en) 2012-01-26 2013-01-21 High-strength hot-rolled steel sheet and method for producing same
EP13740782.1A EP2808413B1 (fr) 2012-01-26 2013-01-21 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci
CN201380005846.8A CN104053806B (zh) 2012-01-26 2013-01-21 高强度热轧钢板及其制造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2012-013592 2012-01-26
JP2012013592 2012-01-26

Publications (1)

Publication Number Publication Date
WO2013111556A1 true WO2013111556A1 (fr) 2013-08-01

Family

ID=48873288

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2013/000257 WO2013111556A1 (fr) 2012-01-26 2013-01-21 Tôle en acier laminée à chaud hautement résistante, et procédé de fabrication de celle-ci

Country Status (6)

Country Link
US (1) US20150030880A1 (fr)
EP (1) EP2808413B1 (fr)
JP (1) JP5565534B2 (fr)
KR (1) KR20140103340A (fr)
CN (1) CN104053806B (fr)
WO (1) WO2013111556A1 (fr)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103469115A (zh) * 2013-08-07 2013-12-25 安徽蓝博旺机械集团合诚机械有限公司 叉车转向节用铸钢材料及其制备方法
CN105349912A (zh) * 2015-12-16 2016-02-24 常熟市凯波冶金建材机械设备厂 燃气轮机用轴承座
CN105838990A (zh) * 2015-11-30 2016-08-10 武汉钢铁(集团)公司 一种锌铁合金镀层冷成形钢板的生产方法
CN109898034A (zh) * 2017-12-08 2019-06-18 江苏赛尔亚环保科技有限公司 一种除臭设备用箱体材料
WO2021187238A1 (fr) * 2020-03-19 2021-09-23 日本製鉄株式会社 Tôle d'acier
US11274355B2 (en) 2017-02-16 2022-03-15 Nippon Steel Corporation Hot rolled steel sheet and method for producing same

Families Citing this family (60)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013115205A1 (fr) * 2012-01-31 2013-08-08 Ｊｆｅスチール株式会社 Acier laminé à chaud pour rebord de générateur de puissance et son procédé de fabrication
JP5915412B2 (ja) * 2012-06-29 2016-05-11 Ｊｆｅスチール株式会社 曲げ性に優れた高強度熱延鋼板およびその製造方法
JP5821864B2 (ja) * 2013-01-31 2015-11-24 Ｊｆｅスチール株式会社 バーリング加工性に優れた高強度熱延鋼板およびその製造方法
JP5637225B2 (ja) * 2013-01-31 2014-12-10 Ｊｆｅスチール株式会社 バーリング加工性に優れた高強度熱延鋼板およびその製造方法
JPWO2015102050A1 (ja) 2014-01-06 2017-03-23 新日鐵住金株式会社 鋼材およびその製造方法
MX2016008809A (es) * 2014-01-06 2016-09-08 Nippon Steel & Sumitomo Metal Corp Miembro formado en caliente y proceso para manufacturar el mismo.
CN104131224A (zh) * 2014-07-25 2014-11-05 合肥市东庐机械制造有限公司 一种耐磨抗冲击性合金钢及其制造方法
CN107406947B (zh) * 2015-03-25 2020-02-14 杰富意钢铁株式会社 高强度钢板及其制造方法
CN104928575A (zh) * 2015-05-13 2015-09-23 唐山钢铁集团有限责任公司 355MPa级汽车用冷成形镀锌热轧基板及其生产方法
CN105114426A (zh) * 2015-07-15 2015-12-02 江苏永昊高强度螺栓有限公司 一种耐腐蚀螺栓
CN105088061A (zh) * 2015-08-20 2015-11-25 无锡贺邦金属制品有限公司 一种镜面模具钢
CN105401096A (zh) * 2015-11-13 2016-03-16 太仓旺美模具有限公司 一种高硬度耐热金属材料
CN105385960A (zh) * 2015-11-26 2016-03-09 佛山市高明区杨和金属材料专业镇技术创新中心 一种热轧板的生产工艺
CN105543660A (zh) * 2015-12-28 2016-05-04 常熟市双灵船舶设备有限公司 多轮滑车
CN105543717A (zh) * 2016-01-12 2016-05-04 杭州科技职业技术学院 一种用于汽车制动泵活塞的合金材料及制备方法
CN105543670A (zh) * 2016-01-26 2016-05-04 安徽同盛环件股份有限公司 一种高硬度高强度合金钢及制备方法
CN105755376A (zh) * 2016-03-31 2016-07-13 苏州睿昕汽车配件有限公司 一种耐高温汽车配件合金钢材料及其制备方法
CN105755384A (zh) * 2016-03-31 2016-07-13 苏州睿昕汽车配件有限公司 一种汽车配件用合金材料及其制备方法
CN105755402A (zh) * 2016-03-31 2016-07-13 苏州睿昕汽车配件有限公司 一种耐高温汽车配件合金钢材料及其制备方法
CN105986153A (zh) * 2016-03-31 2016-10-05 苏州睿昕汽车配件有限公司 一种汽车配件用合金材料及其制备方法
US10436557B2 (en) * 2016-04-18 2019-10-08 Ammo Technologies, Inc. Armor-piercing projectile
CN106119725A (zh) * 2016-05-09 2016-11-16 林淑录 一种海洋钻井平台燃油系统用合金材料及其制备方法
CN105970103A (zh) * 2016-05-18 2016-09-28 安徽合矿机械股份有限公司 一种掺锆元素合金钢材料
CN105803335A (zh) * 2016-05-18 2016-07-27 安徽合矿机械股份有限公司 一种高耐热刹车片用合金钢材料
CN106119669A (zh) * 2016-06-28 2016-11-16 无锡新大力电机有限公司 一种制造永磁电机外壳的方法
CN106148829A (zh) * 2016-07-27 2016-11-23 江苏和信石油机械有限公司 一种钻进钻杆用高性能合金钢
CN106148836A (zh) * 2016-07-27 2016-11-23 江苏和信石油机械有限公司 一种高强度合金钢及其在钻进钻杆中的应用
CN106148828A (zh) * 2016-07-27 2016-11-23 江苏和信石油机械有限公司 一种合金钢及其用于制备钻进钻杆的用途
CN106148812A (zh) * 2016-07-27 2016-11-23 江苏和信石油机械有限公司 一种耐腐蚀的钻进钻杆用钢
CN106244913A (zh) * 2016-07-27 2016-12-21 江苏和信石油机械有限公司 一种钻进钻杆合金钢
CN106148837A (zh) * 2016-08-12 2016-11-23 安徽祥宇钢业集团有限公司 一种含纳米钛的不锈钢管及其制备方法
CN107058856B (zh) * 2017-01-24 2019-01-22 河北高新泵业有限公司 一种液相变质剂和制备高铬铸铁的方法
CN107419197A (zh) * 2017-04-18 2017-12-01 浙江益大特钢有限公司 一种耐热不锈钢无缝钢管及制造方法
CN107058888A (zh) * 2017-05-27 2017-08-18 苏州铭晟通物资有限公司 一种金属五金钢材
CN107419184A (zh) * 2017-06-09 2017-12-01 太仓东旭精密机械有限公司 一种高性能五金件
CN107326287A (zh) * 2017-06-09 2017-11-07 太仓东旭精密机械有限公司 一种机械零部件用钢
KR101940919B1 (ko) 2017-08-08 2019-01-22 주식회사 포스코 우수한 강도와 연신율을 갖는 열연강판 및 제조방법
RU2648426C1 (ru) * 2017-08-24 2018-03-26 Акционерное общество "Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения", АО "НПО "ЦНИИТМАШ" Хладостойкая сталь
CN107740000A (zh) * 2017-08-30 2018-02-27 宁波亿润汽车零部件有限公司 一种安全气囊电子控制单元支架及其制备方法
CN107739988A (zh) * 2017-08-30 2018-02-27 宁波亿润汽车零部件有限公司 一种汽车排气管支架及其制备方法
CN107829045A (zh) * 2017-09-05 2018-03-23 宁波市新光货架有限公司 一种耐磨金属货架的加工方法
CN109536847B (zh) * 2017-09-21 2020-12-08 上海梅山钢铁股份有限公司 屈服强度390MPa级焊管用热轧钢板及其制造方法
CN107739999A (zh) * 2017-09-28 2018-02-27 江苏晶王新材料科技有限公司 一种高强度金属材料
CN107747055A (zh) * 2017-09-28 2018-03-02 江苏晶王新材料科技有限公司 一种抗磨轻金属材料
CN107906268B (zh) * 2017-10-27 2019-09-27 合肥紫金钢管股份有限公司 一种户外建筑施工用高强度耐候性直缝埋弧焊钢管
CN107883073B (zh) * 2017-10-27 2019-09-27 合肥紫金钢管股份有限公司 一种预应力混凝土管桩施工用直缝埋弧焊钢管
CN107829031A (zh) * 2017-11-21 2018-03-23 安徽金阳金属结构工程有限公司 一种大断面h型钢及其生产工艺
CN107937808A (zh) * 2017-11-21 2018-04-20 安徽金阳金属结构工程有限公司 一种热轧h型钢及其生产工艺
CN107904510A (zh) * 2017-11-21 2018-04-13 重庆文理学院 一种综合高性能的热作模具钢及其制备方法
CN107868910A (zh) * 2017-11-21 2018-04-03 安徽金阳金属结构工程有限公司 一种耐低温韧性h型钢及其生产工艺
RU2651071C1 (ru) * 2017-11-27 2018-04-18 Юлия Алексеевна Щепочкина Сплав на основе железа
RU2650957C1 (ru) * 2017-11-27 2018-04-18 Юлия Алексеевна Щепочкина Сплав на основе железа
CN107904475A (zh) * 2017-12-11 2018-04-13 四川才阁机械有限公司 一种稳定性高的高性能金属材料
RU2660786C1 (ru) * 2017-12-19 2018-07-09 Юлия Алексеевна Щепочкина Сплав на основе железа
CN108265229A (zh) * 2017-12-27 2018-07-10 柳州璞智科技有限公司 一种关节机器人用金属材料及其制备方法
RU2663954C1 (ru) * 2018-02-13 2018-08-13 Юлия Алексеевна Щепочкина Сплав на основе железа
CN108644592A (zh) * 2018-05-28 2018-10-12 倍德力能源装备（江苏）有限公司 一种高精准度恒力支吊架
CN109182927B (zh) * 2018-11-01 2019-11-08 晋大纳米科技（厦门）有限公司 一种强抗菌性能马氏体不锈钢及其热处理方法与应用
CN112593139A (zh) * 2020-12-10 2021-04-02 泉州市泉兴五金艺品有限公司 一种铁制工艺品配方及其制备工艺
CN113913683A (zh) * 2021-09-01 2022-01-11 宁波市明立紧固件有限公司 一种高强度螺母材料及其制备方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0257634A (ja) * 1988-08-23 1990-02-27 Sumitomo Metal Ind Ltd 高強度鋼板の製造方法及びその加工品の熱処理方法
JP2004143518A (ja) * 2002-10-23 2004-05-20 Sumitomo Metal Ind Ltd 熱延鋼板
JP2005002406A (ja) * 2003-06-11 2005-01-06 Sumitomo Metal Ind Ltd 高強度熱延鋼板とその製造方法
JP2006161112A (ja) * 2004-12-08 2006-06-22 Sumitomo Metal Ind Ltd 高強度熱延鋼板とその製造方法
JP2007262429A (ja) 2006-03-27 2007-10-11 Jfe Steel Kk 曲げ加工性に優れた耐摩耗鋼板
JP2008189978A (ja) 2007-02-02 2008-08-21 Sumitomo Metal Ind Ltd 熱延鋼板及びその製造方法
JP2008285741A (ja) * 2007-05-21 2008-11-27 Sumitomo Metal Ind Ltd 高強度熱延鋼板及びその製造方法
JP2009052139A (ja) * 2007-07-31 2009-03-12 Jfe Steel Kk 高強度鋼板
JP2010275594A (ja) * 2009-05-29 2010-12-09 Jfe Steel Corp 自動車部材用高張力溶接鋼管
JP2011225980A (ja) * 2010-03-31 2011-11-10 Jfe Steel Corp 加工性に優れた高張力熱延鋼板およびその製造方法

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4528275B2 (ja) * 2006-03-20 2010-08-18 新日本製鐵株式会社 伸びフランジ性に優れた高強度熱延鋼板
JP2010053434A (ja) * 2008-08-29 2010-03-11 Nakayama Steel Works Ltd 延性に優れた高強度熱延薄鋼板およびその製造方法
JP5041083B2 (ja) * 2010-03-31 2012-10-03 Ｊｆｅスチール株式会社 加工性に優れた高張力溶融亜鉛めっき鋼板およびその製造方法

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0257634A (ja) * 1988-08-23 1990-02-27 Sumitomo Metal Ind Ltd 高強度鋼板の製造方法及びその加工品の熱処理方法
JP2004143518A (ja) * 2002-10-23 2004-05-20 Sumitomo Metal Ind Ltd 熱延鋼板
JP2005002406A (ja) * 2003-06-11 2005-01-06 Sumitomo Metal Ind Ltd 高強度熱延鋼板とその製造方法
JP2006161112A (ja) * 2004-12-08 2006-06-22 Sumitomo Metal Ind Ltd 高強度熱延鋼板とその製造方法
JP2007262429A (ja) 2006-03-27 2007-10-11 Jfe Steel Kk 曲げ加工性に優れた耐摩耗鋼板
JP2008189978A (ja) 2007-02-02 2008-08-21 Sumitomo Metal Ind Ltd 熱延鋼板及びその製造方法
JP2008285741A (ja) * 2007-05-21 2008-11-27 Sumitomo Metal Ind Ltd 高強度熱延鋼板及びその製造方法
JP2009052139A (ja) * 2007-07-31 2009-03-12 Jfe Steel Kk 高強度鋼板
JP2010275594A (ja) * 2009-05-29 2010-12-09 Jfe Steel Corp 自動車部材用高張力溶接鋼管
JP2011225980A (ja) * 2010-03-31 2011-11-10 Jfe Steel Corp 加工性に優れた高張力熱延鋼板およびその製造方法

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103469115A (zh) * 2013-08-07 2013-12-25 安徽蓝博旺机械集团合诚机械有限公司 叉车转向节用铸钢材料及其制备方法
CN105838990A (zh) * 2015-11-30 2016-08-10 武汉钢铁(集团)公司 一种锌铁合金镀层冷成形钢板的生产方法
CN105349912A (zh) * 2015-12-16 2016-02-24 常熟市凯波冶金建材机械设备厂 燃气轮机用轴承座
US11274355B2 (en) 2017-02-16 2022-03-15 Nippon Steel Corporation Hot rolled steel sheet and method for producing same
CN109898034A (zh) * 2017-12-08 2019-06-18 江苏赛尔亚环保科技有限公司 一种除臭设备用箱体材料
WO2021187238A1 (fr) * 2020-03-19 2021-09-23 日本製鉄株式会社 Tôle d'acier
JPWO2021187238A1 (fr) * 2020-03-19 2021-09-23
CN115298342A (zh) * 2020-03-19 2022-11-04 日本制铁株式会社 钢板
JP7277860B2 (ja) 2020-03-19 2023-05-19 日本製鉄株式会社 鋼板
CN115298342B (zh) * 2020-03-19 2023-11-17 日本制铁株式会社 钢板

Also Published As

Publication number Publication date
KR20140103340A (ko) 2014-08-26
EP2808413B1 (fr) 2017-04-26
JP5565534B2 (ja) 2014-08-06
CN104053806B (zh) 2018-07-10
CN104053806A (zh) 2014-09-17
EP2808413A4 (fr) 2016-05-04
US20150030880A1 (en) 2015-01-29
JPWO2013111556A1 (ja) 2015-05-11
EP2808413A1 (fr) 2014-12-03

Similar Documents

Publication Publication Date Title
JP5565534B2 (ja) 高強度熱延鋼板及びその製造方法
JP5610094B2 (ja) 熱延鋼板およびその製造方法
JP4635525B2 (ja) 深絞り性に優れた高強度鋼板およびその製造方法
JP6086081B2 (ja) 表面性状に優れた高強度冷延鋼板およびその製造方法
WO2011162412A1 (fr) Tôle d'acier laminée à chaud hautement résistante présentant une excellente capacité à former des bords par étirage et son procédé de production
JP5915412B2 (ja) 曲げ性に優れた高強度熱延鋼板およびその製造方法
JP5892147B2 (ja) 高強度熱延鋼板およびその製造方法
JP5884472B2 (ja) 伸びフランジ性に優れた高強度熱延鋼板およびその製造方法
WO2017169869A1 (fr) Plaque d'acier mince et plaque d'acier plaquée, procédé de fabrication de plaque d'acier laminée à chaud, procédé de fabrication de plaque d'acier très dur laminée à froid, procédé de fabrication de plaque d'acier mince et procédé de fabrication de plaque d'acier plaquée
JP6275510B2 (ja) 高強度熱延鋼板およびその製造方法
WO2014119259A1 (fr) Tôle d'acier laminée à chaud à haute résistance et procédé de fabrication associé
JP5978614B2 (ja) 打ち抜き性に優れた高強度熱延鋼板およびその製造方法
JP6224704B2 (ja) 高強度熱延鋼板の製造方法
WO2014119260A1 (fr) Tôle d'acier à haute résistance laminée à chaud et son procédé de production
JP6131872B2 (ja) 高強度薄鋼板およびその製造方法
JP6052503B2 (ja) 高強度熱延鋼板とその製造方法
JP6086080B2 (ja) 高強度冷延鋼板およびその製造方法
JP6320792B2 (ja) 高強度熱延鋼板およびその製造方法
JP5644964B2 (ja) 高強度熱延鋼板およびその製造方法
JP5861434B2 (ja) 打ち抜き性に優れた高強度熱延鋼板およびその製造方法
JP6123551B2 (ja) 耐疲労性およびスリット加工後の形状凍結性に優れた高強度熱延鋼板およびその製造方法
JP6086078B2 (ja) 伸びフランジ性に優れた高強度冷延鋼板およびその製造方法
JP2013047381A (ja) 伸びフランジ性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP6086077B2 (ja) 加工性に優れた高強度冷延鋼板およびその製造方法
WO2024105999A1 (fr) Tôle d'acier laminée à chaud et son procédé de production

Legal Events

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

Ref document number: 13740782

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2013555188

Country of ref document: JP

Kind code of ref document: A

REEP Request for entry into the european phase

Ref document number: 2013740782

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2013740782

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 20147019785

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 14374124

Country of ref document: US

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: IDP00201405048

Country of ref document: ID