WO2013103125A1 - 熱延鋼板およびその製造方法 - Google Patents
熱延鋼板およびその製造方法 Download PDFInfo
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- WO2013103125A1 WO2013103125A1 PCT/JP2012/083918 JP2012083918W WO2013103125A1 WO 2013103125 A1 WO2013103125 A1 WO 2013103125A1 JP 2012083918 W JP2012083918 W JP 2012083918W WO 2013103125 A1 WO2013103125 A1 WO 2013103125A1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
- C25D5/34—Pretreatment of metallic surfaces to be electroplated
- C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
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- 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 hot-rolled steel sheet and a manufacturing method thereof. More specifically, the present invention relates to a high-strength hot-rolled steel sheet excellent in stretch flangeability and low-temperature toughness, and a method for producing the same.
- steel plates used as materials for automobile members such as inner plate members, structural members, and suspension members are stretch flange workability, burring workability, ductility, fatigue durability, impact resistance, or corrosion resistance, depending on the application. It is important how to secure these material characteristics and high strength in a high-order and balanced manner.
- the steel plate used as a material for such a member has a low temperature, particularly in order to ensure impact resistance in cold regions, so that it is difficult to break even if it is subjected to impacts such as collision after being attached to a car as a member after forming.
- This low temperature toughness is defined by vTrs (Charpy fracture surface transition temperature) and the like. Therefore, it is also necessary to consider the impact resistance itself of the steel sheet. That is, low-temperature toughness is required as a very important characteristic in addition to excellent workability for steel sheets used as materials for parts including the above members.
- Patent Documents 1 and 2 disclose the production method thereof, and a method (Patent Document 1) in which a martensite phase having an adjusted aspect ratio is used as a main phase or an average grain.
- Low temperature toughness is improved by a method of finely depositing carbides in ferrite having a diameter of 5 to 10 ⁇ m (Patent Document 2).
- Patent Documents 1 and 2 there is no mention of stretch flangeability, and there is a concern that molding defects may occur when applied to a member that performs burring.
- there is knowledge of improving low temperature toughness in the steel pipe field and the thick plate field there is a similar concern because formability as thin as that of a thin sheet is not required.
- Non-Patent Document 1 discloses that it is effective for bendability and stretch flangeability.
- Non-patent document 2 discloses a technique for improving stretch flangeability. From Non-Patent Documents 1 and 2, it is considered that stretch flangeability can be improved by making the metal structure and rolling texture uniform, but no consideration is given to compatibility between low-temperature toughness and stretch flangeability.
- Patent Document 3 is referred to, and a technique for dispersing an appropriate amount of retained austenite and bainite in a ferrite phase with controlled hardness and particle size is disclosed.
- it is a structure containing 50% or more of soft ferrite, it is difficult to meet the recent demand for higher strength.
- the present invention has been devised in view of the above-mentioned problems, and the object thereof is a hot-rolled steel sheet, in particular, a hot-rolled steel sheet having high strength and excellent stretch flangeability and low-temperature toughness, and the steel sheet.
- An object of the present invention is to provide a production method capable of stably producing the above.
- the present inventors have succeeded in producing a steel sheet excellent in stretch flangeability and low-temperature toughness by optimizing the chemical composition and production conditions of a high-strength hot-rolled steel sheet and controlling the texture and microstructure of the steel sheet.
- the summary is as follows.
- the chemical composition is mass%, Nb: 0.005 to 0.06%, Cu: 0.02 to 1.2%, Ni: 0.01 to 0.6%, Mo: 0.01 to 1%, V: 0.01 to 0.2% and Cr: 0.01 to 2%
- the hot-rolled steel sheet according to (1) above which contains one or more selected from the group consisting of:
- the chemical composition is selected from the group consisting of Mg: 0.0005 to 0.01%, Ca: 0.0005 to 0.01%, and REM: 0.0005 to 0.1% by mass%.
- R value (rC) in a direction perpendicular to the rolling direction is 0.70 or more, and r value (r30) in a direction at 30 ° to the rolling direction is 1.10 or less.
- the primary cooling is water cooling that satisfies the following formula (2) and the cooling amount is 40 ° C. or higher and 140 ° C. or lower
- the secondary cooling is water cooling that starts cooling within 3 seconds after the primary cooling and cools at an average cooling rate of 30 ° C./second or more
- the winding is performed at a temperature CT satisfying the following formula (3):
- T1 (°C) 850 + 10 ⁇ (C + N) ⁇ Mn + 350 ⁇ Nb + 250 ⁇ Ti + 40 ⁇ B + 10 ⁇ Cr + 100 ⁇ Mo + 100 ⁇ V (1) 1 ⁇ t / t1 ⁇ 2.5 (2)
- t1 0.001 ⁇ ⁇ (Tf ⁇ T1) ⁇ P1 / 100 ⁇ 2 ⁇ 0.109 ⁇ ⁇ (Tf ⁇ T1) ⁇ P1 /
- max [] is a function that returns the maximum value among the arguments
- Ms is a temperature determined by the formula (5)
- Tf and P1 in the formula (4) are the steel plate temperature and the reduction ratio (%) at the time of the final reduction in the reduction in one pass of 30% or more in the first temperature range, respectively.
- the rough hot rolling is characterized in that the maximum rolling reduction per pass in a temperature range of 1000 ° C. or more and 1200 ° C. or less is 40% or more and the average particle size of austenite is 200 ⁇ m or less.
- a method for producing a hot-rolled steel sheet comprising subjecting the surface of the hot-rolled steel sheet obtained by the method for producing a hot-rolled steel sheet according to any one of (9) to (11) to plating. .
- a hot-rolled steel sheet particularly a high-strength steel sheet excellent in stretch flangeability and low-temperature toughness can be provided. If this steel plate is used, it becomes easy to process a high-strength steel plate, and it becomes possible to endure the use in a very cold region, so that the industrial contribution is extremely remarkable.
- the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups of the plate surface at the plate thickness central portion which is a steel plate portion partitioned by the 3/8 thickness position and the 5/8 thickness position from the steel plate surface Having an average value of X-ray random intensity ratio of 6.5 or less and a texture where the X-ray random intensity ratio of the ⁇ 332 ⁇ ⁇ 113> crystal orientation is 5.0 or less:
- the definition of these X-ray random intensity ratios is particularly important in the present invention. Measured from the surface of the steel plate, X-ray diffraction of the plate surface is performed at the central portion of the plate thickness, which is a steel plate portion divided by the 3/8 thickness position and the 5/8 thickness position, and a specific crystal orientation is obtained.
- the average value of ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups when the intensity ratio of each orientation with respect to a standard sample (random sample) having a random crystal orientation is 6.5 or less.
- the hole expansion rate ⁇ 140% and tensile strength x hole expansion rate ⁇ 100,000MPa% with a material of strength 780MPa class, the hole expansion rate ⁇ 90% and tensile strength x hole expansion rate ⁇ 70,000 MPa ⁇ % and a material having a strength of 980 MPa class or higher can ensure good stretch flangeability satisfying the hole expansion ratio ⁇ 40% and satisfying the tensile strength ⁇ hole expansion ratio ⁇ 50000 MPa ⁇ %.
- the average value of the X-ray random intensity ratio of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface is preferably 4.0 or less.
- the average value of the X-ray random intensity ratio of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface exceeds 6.5, the anisotropy of the mechanical properties of the steel plate becomes extremely strong, and the specific direction Although the stretch flangeability is improved, the stretch flangeability in a direction different from that is remarkably lowered, and it is difficult to obtain mechanical characteristics satisfying the above-mentioned hole expansion ratio.
- the average value of the X-ray random intensity ratio of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface is less than 0.5.
- the average value of the X-ray random intensity ratios of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface is preferably 0.5 or more.
- the average values of the X-ray random intensity ratios of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface are ⁇ 100 ⁇ ⁇ 011>, ⁇ 116 ⁇ ⁇ 110>, ⁇ 114 ⁇ ⁇ 110>, ⁇ 113 ⁇ ⁇ 110>, ⁇ 112 ⁇ ⁇ 110>, ⁇ 335 ⁇ ⁇ 110> and ⁇ 223 ⁇ ⁇ 110> are arithmetic averages of the X-ray random intensity ratios.
- the X-ray random intensity ratio in each direction is measured using an apparatus such as X-ray diffraction or EBSD (Electron Back Scattering Diffraction).
- X-ray diffraction or EBSD (Electron Back Scattering Diffraction).
- EBSD Electro Back Scattering Diffraction
- the average value of the X-ray random intensity ratios of the ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface is an arithmetic average of the X-ray random intensity ratios of the above-mentioned respective directions. If, however, the X-ray random intensity ratios in all the above directions cannot be obtained, ⁇ 100 ⁇ ⁇ 110>, ⁇ 116 ⁇ ⁇ 110>, ⁇ 114 ⁇ ⁇ 110>, ⁇ 112 ⁇ ⁇ 110> Alternatively, an arithmetic average of the X-ray random intensity ratios in each direction of ⁇ 223 ⁇ ⁇ 110> may be substituted.
- the ⁇ 332 ⁇ ⁇ 113> crystal orientation of the plate surface at the plate thickness center portion which is a steel plate portion partitioned from the steel plate surface by the 3/8 thickness position and the 5/8 thickness position. If the X-ray random intensity ratio is 5.0 or less (preferably 3.0 or less), it satisfies the most recently required tensile strength ⁇ hole expansion ratio ⁇ 50000 required for processing the undercarriage part. Furthermore, it is preferable that the X-ray random intensity ratio of the ⁇ 332 ⁇ ⁇ 113> crystal orientation is 3.0 or less.
- the X-ray random intensity ratio of the ⁇ 332 ⁇ ⁇ 113> crystal orientation is more than 5.0, the anisotropy of the mechanical properties of the steel sheet becomes extremely strong, and the stretch flangeability in a specific direction is improved. The stretch flangeability of the direction different from that falls remarkably, and a hole expansion rate falls.
- the X-ray random intensity ratio of the crystal orientation of ⁇ 332 ⁇ ⁇ 113> is less than 0.5, there is a concern about deterioration of hole expansibility. . Therefore, the X-ray random intensity ratio of the crystal orientation of ⁇ 332 ⁇ ⁇ 113> is preferably 0.5 or more.
- Samples to be subjected to X-ray diffraction are obtained by reducing the thickness of the steel sheet from the surface to a predetermined thickness by mechanical polishing, etc., and then removing the strain by chemical polishing or electrolytic polishing, and at the same time the thickness of 3/8 to 5/8. What is necessary is just to adjust and measure a sample according to the above-mentioned method so that a suitable surface may become a measurement surface in the range.
- the above-mentioned limitation of the X-ray intensity is satisfied not only in the vicinity of the plate thickness 1 ⁇ 2 but also as much as possible, so that the hole expandability is further improved.
- the material properties of the entire steel sheet can be generally represented by measuring at the center of the plate thickness, which is a steel plate portion partitioned by 3/8 thickness position and 5/8 thickness position from the steel sheet surface. Therefore, this shall be specified.
- the crystal orientation represented by ⁇ hkl ⁇ ⁇ uvw> indicates that the normal direction of the plate surface is parallel to ⁇ hkl> and the rolling direction is parallel to ⁇ uvw>.
- the r value (rC) in the direction perpendicular to the rolling direction is 0.70 or more, and the r value (r30) in the rolling direction and 30 ° is 1.10 or less:
- satisfying the following mechanical characteristics makes it possible to secure even better stretch flangeability. Therefore, it is preferable to satisfy the following mechanical characteristics.
- R value (rC) in the direction perpendicular to the rolling direction rC is preferably 0.70 or more.
- the upper limit of the r value is not particularly defined, but is preferably 1.10 or less because better hole expansibility can be obtained.
- R value (r30) in the direction of 30 ° with respect to the rolling direction r30 is preferably 1.10 or less.
- the lower limit of the r value in this direction is not particularly defined, but is preferably 0.70 or more because better hole expandability can be obtained.
- the r value (rL) in the rolling direction is 0.70 or more, and the r value (r60) at 60 ° with respect to the rolling direction is 1.10 or less:
- satisfying the following mechanical characteristics makes it possible to secure even better stretch flangeability. Therefore, it is preferable to satisfy the following mechanical characteristics.
- R value (rL) in rolling direction rL is preferably 0.70 or more.
- the upper limit of the rL value is not particularly defined, but it is preferable to set rL to 1.10 or less because better hole expansibility can be obtained.
- R value (r60) in the direction of 60 ° with respect to the rolling direction r60 is preferably 1.10 or less. Although the lower limit of the r60 value is not particularly defined, more excellent hole expandability can be obtained by setting r60 to 0.70 or more.
- Each r value described above is evaluated by a tensile test using a JIS No. 5 tensile test piece.
- the tensile strain is usually in the range of 5 to 15% in the case of a high-strength steel plate, and may be evaluated in the range of uniform elongation.
- the average crystal grain size, ferrite, and retained austenite are defined using the EBSP-OIM (Electron Back Scatter Diffraction Pattern-Orientation Image Microscopy (trademark)) method.
- the EBSP-OIM method irradiates an electron beam onto a highly inclined sample in a scanning electron microscope (SEM), shoots the Kikuchi pattern formed by backscattering with a high-sensitivity camera, and processes the computer image. It consists of a device and software that measure the crystal orientation of the glass in a short time.
- the EBSP method can quantitatively analyze the microstructure and crystal orientation of the surface of the bulk sample, and the analysis area is an area that can be observed with an SEM. Depending on the resolution of the SEM, analysis can be performed with a minimum resolution of 20 nm. The analysis takes several hours and is performed by mapping tens of thousands of points to be analyzed in a grid at equal intervals.
- the crystal orientation distribution in the sample and the size of the crystal grains can be seen.
- An azimuth difference between adjacent measurement points can be calculated from the measurement information, and an average value thereof is referred to as a KAM (Kernel average misorientation) value.
- the grain is visualized from an image mapped by defining the orientation difference of the crystal grain as 15 ° which is a threshold value of a large tilt grain boundary generally recognized as a crystal grain boundary, and the average crystal grain The diameter was determined. Further, ferrite having an average KAM value within 1 ° within a crystal grain surrounded by a 15 ° large-angle grain boundary was defined as ferrite. This is because ferrite is a high-temperature transformation phase and has a small transformation strain. Furthermore, what was identified as austenite by the EBSP method was defined as retained austenite.
- Tempered martensite or lower bainite as defined in the present invention is a structure that transforms from austenite at 350 ° C. or lower when the Ms point is 350 ° C. or lower when the Ms point is higher than 350 ° C., When this structure is observed by TEM, cementite or metastable iron carbide precipitates in multiple variants in the same lath. On the other hand, cementite or metastable iron carbide precipitated in the same lath as a single variant was defined as upper bainite. This is probably because the driving force for precipitation of cementite is smaller than that of tempered martensite or lower bainite.
- single-phase or multi-phase structures such as precipitation-strengthened ferrite, bainite, and martensite are used in order to increase the strength.
- the total area ratio of martensite and lower bainite is more than 85% by area and the average crystal grain size is 12.0 ⁇ m or less, the hardness difference between these structures is more preferably below a certain level. It has been found that, when reduced, stress concentration at the tissue interface is reduced, and stretch flangeability and low temperature toughness are improved. If the sum of the fractions of the tempered martensite structure and the lower martensite is more than 85%, it is more preferable because the balance between strength and elongation is good.
- the average value of hardness when measuring Vickers hardness of 100 points or more using a micro Vickers with a load of 0.098N (10 gf) is E (HV0.01)
- the standard deviation of hardness is ⁇ ( HV0.01), ⁇ (HV0.01) / E (HV0.01) is 0.08 or less
- ferrite is included in an area of 5 area% or more. 55,000 MPa ⁇ %, tensile strength ⁇ total elongation ⁇ 14000 MPa ⁇ %, and vTrs ⁇ ⁇ 40 ° C. are satisfied because excellent mechanical properties satisfying both stretch flangeability and total elongation can be obtained.
- the tensile strength is 980 MPa class or more, and the tensile strength ⁇ hole expansion rate ⁇ 60000 MPa ⁇ % and vTrs ⁇ ⁇ 40 ° C. are satisfied.
- the lower limit of ⁇ (HV0.01) / E (HV0.01) is not particularly defined, but is usually 0.03 or more.
- C 0.01 to 0.2%
- C (carbon) is an element having an effect of improving the strength of the steel sheet.
- the C content is less than 0.01%, it is difficult to obtain the effect by the above action. Therefore, the C content is 0.01% or more.
- the C content exceeds 0.2%, the ductility is lowered, and iron-based carbides such as cementite (Fe 3 C) that becomes the crack starting point of the secondary shear surface during the punching process increase, It causes deterioration of stretch flangeability. Therefore, the C content is 0.2% or less.
- Si 0.001% to 2.5%
- Si is an element having an effect of improving the strength of the steel sheet, and also serves as a deoxidizer for molten steel. If the Si content is less than 0.001%, it is difficult to obtain the effect by the above action. Therefore, the Si content is 0.001% or more.
- Si also has the effect of suppressing precipitation of iron-based carbides such as cementite, thereby improving strength and hole expandability. From such a viewpoint, the Si content is preferably set to 0.1% or more. On the other hand, even if the Si content exceeds 2.5%, the effect of increasing the strength of the steel sheet is saturated. Therefore, the Si content is 2.5% or less.
- the Si content is preferably 1.2% or less.
- Mn 0.10 to 4.0%
- Mn manganese
- Mn has the effect of improving the strength of the steel sheet by solid solution strengthening and quenching strengthening.
- the Mn content is 0.10% or more.
- Mn has the effect
- the Mn content is preferably 1% or more, more preferably 2% or more.
- Mn also has the effect
- the Mn content ([Mn]) and the S content ([S]) satisfy the [Mn] / [S] ⁇ 20 content.
- the Mn content is 4.0% or less.
- P 0.10% or less
- P phosphorus
- the P content is 0.10% or less. From the viewpoint of hole expansibility and weldability, the P content is preferably 0.02% or less.
- S 0.030% or less
- S sulfur
- the S content is 0.030% or less. From the viewpoint of hole expansibility, the S content is preferably 0.010% or less, and more preferably 0.005% or less.
- Al 0.001 to 2.0%
- Al (aluminum) has the effect
- the Al content is less than 0.001%, it is difficult to obtain the effect by the above action. Therefore, the Al content is 0.001% or more.
- Al, like Si, also has the effect of suppressing the precipitation of iron-based carbides such as cementite, thereby improving the strength and hole expandability. From such a viewpoint, the Al content is preferably 0.016% or more.
- the Al content is preferably 0.016% or more.
- the Al content exceeds 2.0%, the effect of the deoxidation action is saturated, which is economically disadvantageous. Moreover, a crack may be caused at the time of hot rolling. Therefore, the Al content is 2.0% or less.
- the Al content is preferably 0.06% or less. More preferably, it is 0.04% or less.
- N is an element generally contained as an impurity. If the N content exceeds 0.01%, cracking occurs during hot rolling, and the aging resistance deteriorates. Therefore, the N content is 0.01% or less. From the viewpoint of aging resistance, the N content is preferably 0.005% or less.
- Ti (0.005 + 48/14 [N] +48/32 [S])% ⁇ Ti ⁇ 0.3%:
- Ti (titanium) is an element having an action of improving the strength of the steel sheet by precipitation strengthening or solid solution strengthening. Ti content is less than (0.005 + 48/14 [N] +48/32 [S])% determined by N content [N] (unit:%) and S content [S] (unit:%) Then, it is difficult to obtain the effect by the above action. Accordingly, the Ti content is (0.005 + 48/14 [N] +48/32 [S])% or more. On the other hand, even if the Ti content exceeds 0.3%, the effect of the above action is saturated and disadvantageous economically. Therefore, the Ti content is 0.3% or less.
- Nb, Cu, Ni, Mo, V, Cr: Nb (niobium), Cu (copper), Ni (nickel), Mo (molybdenum), V (vanadium), and Cr (chromium) are elements having an action of improving the strength of the steel sheet by precipitation strengthening or solid solution strengthening. . Accordingly, one or more of these elements can be appropriately contained as necessary.
- Nb content is over 0.06%
- Cu content is over 1.2%
- Ni content is over 0.6%
- Mo content is over 1%
- V content is over 0.2%
- the Nb content is 0 to 0.06%
- the Cu content is 0 to 1.2%
- the Ni content is 0 to 0.6%
- the Mo content is 0 to 1%
- the V content is 0 to 0.2%
- Cr content is 0-2%.
- Nb 0.005% or more
- Cu 0.02% or more
- Mo 0.01% or more
- V 0.00. It is preferable to satisfy any of 01% or more and Cr: 0.01% or more.
- Mg, Ca, REM Mg (magnesium), Ca (calcium), and REM (rare earth elements) are elements that have the effect of improving the workability by controlling the form of non-metallic inclusions that become the starting point of fracture and cause the workability to deteriorate. It is. Accordingly, one or more of these elements may be appropriately contained as necessary. However, even if the Mg content exceeds 0.01%, the Ca content exceeds 0.01%, and the REM content exceeds 0.1%, the effect by the above action is saturated and economically disadvantageous. Therefore, the Mg content is 0 to 0.01%, the Ca content is 0 to 0.01%, and the REM content is 0 to 0.1%. In addition, in order to acquire the effect by the said action more reliably, it is preferable to make content of any element of Mg, Ca, and REM 0.0005% or more.
- B (boron) is an element that segregates at the grain boundary in the same way as C and has the effect of increasing the grain boundary strength. That is, by segregating at the grain boundary as solid solution B as in the case of solid solution C, it works effectively in realizing prevention of fracture surface cracking. And even if C precipitates in the grains as carbides and solid solution C at the grain boundaries decreases, B segregates at the grain boundaries, thereby making it possible to compensate for the decrease in C grain boundaries. Therefore, you may contain B suitably as needed.
- the B content is 0 to 0.002% or less.
- B is an element that is likely to cause slab cracking in the cooling step after continuous casting. From this viewpoint, the B content is preferably 0.0015% or less.
- B content shall be 0.0002% or more.
- B also has the effect of improving the hardenability and facilitating the formation of a continuous cooling transformation structure that is a preferred microstructure for burring properties.
- the balance is iron (Fe) and impurities.
- Impurities may contain Zr, Sn, Co, Zn, and W, but there is no problem if the content of these elements is 1% or less in total.
- a surface-treated steel sheet may be provided by providing a plating layer on the surface of the steel sheet described above for the purpose of improving corrosion resistance.
- the plating layer may be an electroplating layer or a hot dipping layer.
- Examples of the electroplating layer include electrogalvanizing and electro-Zn—Ni alloy plating.
- Examples of the hot dip plating layer include hot dip galvanizing, alloyed hot dip galvanizing, hot dip aluminum plating, hot dip Zn-Al alloy plating, hot dip Zn-Al-Mg alloy plating, hot dip Zn-Al-Mg-Si alloy plating, etc.
- the amount of plating adhesion is not particularly limited, and may be the same as the conventional one.
- Manufacturing method of hot-rolled steel sheet Next, the manufacturing method of the hot rolled steel sheet of the present invention will be described.
- the hardness difference between structures is small and the r value in each direction satisfies a predetermined condition. Details of manufacturing conditions for satisfying these conditions are described below.
- the production method prior to hot rolling is not particularly limited. That is, following the smelting by blast furnace or electric furnace, etc., various secondary smelting is performed to adjust the chemical composition as described above, and then, in addition to normal continuous casting, casting by ingot method, thin slab casting, etc. It may be cast into a steel ingot or slab by the method. In the case of continuous casting, after cooling to low temperature once, it may be heated again and then hot rolled, or the cast slab may be continuously hot rolled. Scrap may be used as a raw material.
- the high-strength steel sheet having excellent stretch flangeability and low temperature brittleness according to the present invention can be obtained when the following requirements are satisfied.
- T1 temperature T1 (°C) 850 + 10 ⁇ (C + N) ⁇ Mn + 350 ⁇ Nb + 250 ⁇ Ti + 40 ⁇ B + 10 ⁇ Cr + 100 ⁇ Mo + 100 ⁇ V ...
- the average value of the X-ray random intensity ratios of ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation groups on the plate surface at the plate thickness center portion divided by the / 8 thickness position and the 3/8 thickness position, ⁇ 332 ⁇ ⁇ 113> crystallographic X-ray random intensity ratio can be controlled, thereby dramatically improving the hole expandability of the final product.
- the T1 temperature itself can be obtained by the empirical formula shown in the above formula (1). Based on the T1 temperature, the inventors have empirically found that recrystallization in the austenitic region of each steel is promoted. In order to obtain better hole expansibility, it is important to accumulate strain due to large reduction in the first temperature range, and the maximum reduction rate per pass in the first temperature range is 30% or more, in other words, In the first temperature range, it is essential to perform the rolling in one pass at a rolling reduction of 30% or more at least once and to make the total rolling reduction to be 50% or more. Furthermore, it is more preferable that the total rolling reduction is 70% or more. On the other hand, if the reduction ratio exceeds 90%, temperature reduction and excessive rolling load will be applied, so the total reduction ratio is preferably 90% or less.
- the first temperature of T1 ° C. to (T1 + 30) ° C. is set to 0 to 30%. If the total rolling reduction in the second temperature range is greater than 30%, the recrystallized austenite grains will expand, and if the retention time is short, the recrystallization will not proceed sufficiently and the hole expandability will deteriorate. End up.
- the reduction ratio is 0%, that is, low-pressure rolling in the second temperature range is It is better not to do it.
- the manufacturing method of the present invention is a method for improving the hole expandability by controlling the texture of the product by recrystallizing austenite uniformly and finely in finish rolling.
- the time from the final reduction of the reduction in one pass of 30% or more in the first temperature range to the start of primary cooling greatly affects stretch flangeability and low temperature toughness.
- the time t (second) from the final reduction pass in one pass of 30% or more in the first temperature range to the start of primary cooling is the steel plate temperature under the final reduction in one pass of 30% or more in the first temperature range.
- the following formula (2) is satisfied with respect to Tf (° C.) and the rolling reduction P1 (%). If t / t1 is less than 1, recrystallization is suppressed and a predetermined texture cannot be obtained. If t / t1 exceeds 2.5, coarsening proceeds and elongation and low-temperature brittleness are remarkably reduced.
- t1 is a time (second) determined by the following equation (4).
- t1 0.001 ⁇ ⁇ (Tf ⁇ T1) ⁇ P1 / 100 ⁇ 2 ⁇ 0.109 ⁇ ⁇ (Tf ⁇ T1) ⁇ P1 / 100 ⁇ +3.1 (4)
- the primary cooling amount (cooling temperature change), which is the difference between the steel plate temperature at the start of cooling in the primary cooling and the steel plate temperature at the end of cooling, is 40 ° C. or higher and 140 ° C. or lower. If the primary cooling amount is less than 40 ° C., it is difficult to suppress the coarsening of the austenite grains, and as a result, the low temperature toughness deteriorates. On the other hand, when the primary cooling amount exceeds 140 ° C., recrystallization becomes insufficient and it becomes difficult to obtain a predetermined texture.
- the average cooling rate in primary cooling is preferably 30 ° C./second or more.
- the upper limit of the average cooling rate in the primary cooling is not particularly limited, but is preferably 2000 ° C./second or less.
- the cooling is started within 3 seconds, and the secondary cooling is performed by water cooling at an average cooling rate of 30 ° C./second or more.
- secondary cooling is water cooling performed between the start of secondary cooling and the start of winding, and the average cooling rate of secondary cooling is the average cooling rate in the water cooling, as will be described later.
- the calculation is performed excluding the period during which the water cooling is interrupted.
- the temperature range from 500 ° C. to 800 ° C. (two-phase range of ferrite and austenite) during the secondary cooling
- the water cooling may be interrupted within 15 seconds or less.
- the interruption of water cooling here is performed in order to promote ferrite transformation in the two-phase region.
- the interruption time of water cooling exceeds 15 seconds, the ferrite area ratio exceeds 15% and the hardness difference between structures increases. As a result, stretch flangeability and low temperature toughness may deteriorate. Therefore, when water cooling is interrupted in the middle of secondary cooling, it is desirable that the time be 15 seconds or less.
- the temperature range for interrupting water cooling is preferably 500 ° C. or higher and 800 ° C. or lower in order to facilitate the ferrite transformation, and the time for interrupting water cooling is preferably 1 second or longer. From the viewpoint of productivity, the time for interrupting the water cooling is more preferably 10 seconds or less.
- winding is performed at a winding temperature CT (° C.) that satisfies the following formula (3).
- CT winding temperature
- the temperature should be less than 300 ° C. It is desirable to wind up.
- Ms is determined by the following formula (5), and the element symbol in the following formula (5) indicates the content (mass%) of each element in the steel.
- Ms (°C) 561-474 ⁇ C-33 ⁇ Mn-17 ⁇ Ni-21 ⁇ Mo (5)
- the austenite grain size after rough hot rolling that is, before finish hot rolling is important, and the austenite grain size before finish hot rolling is small.
- the average particle diameter (equivalent circle average diameter) of austenite is 200 ⁇ m or less, the above-mentioned preferred value can be obtained.
- the maximum reduction rate per pass in the temperature range of 1000 ° C. or more and 1200 ° C. or less by rough hot rolling should be 40% or more.
- the reduction in one pass with a reduction rate of 40% or more may be performed at least once. Therefore, in the rough hot rolling, it is preferable that the maximum rolling reduction per pass in the temperature range of 1000 ° C. or more and 1200 ° C. or less is 40% or more and the average particle size of austenite is 200 ⁇ m or less.
- the austenite grains can be made finer as the rolling reduction is larger and the number of rolling down is larger.
- the austenite average particle size is preferably 100 ⁇ m or less.
- rough hot rolling exceeding 10 passes may cause a decrease in temperature or excessive scale formation, and reduction in one pass with a reduction rate of more than 70% will cause the inclusions to stretch and deteriorate the hole expandability. It may be a cause. Therefore, it is desirable that the reduction in one pass with a reduction rate of 40% or more is 10 passes or less and the maximum reduction rate is 70% or less.
- the recrystallization of austenite in the finish hot rolling process is promoted, and the hole expandability is improved by making the rC and r30 values suitable values. Is realized. This is presumably due to the function of the austenite grain boundary after rough hot rolling (that is, before finishing hot rolling) as one of the recrystallization nuclei during finish hot rolling.
- the confirmation of the austenite grain size after the rough hot rolling is performed by quenching the plate piece before entering the finish hot rolling as much as possible, specifically, the plate piece at a cooling rate of 10 ° C./second or more.
- the structure of the cross section of the plate piece is etched to make the austenite grain boundary stand up and measured with an optical microscope.
- 20 fields of view or more are measured by image analysis or a point count method at a magnification of 50 times or more.
- the obtained hot-rolled steel sheet may be subjected to a skin pass or cold rolling with a rolling reduction of 10% or less inline or offline.
- it is good also as a surface treatment steel plate by providing a plating layer on the surface of a steel plate as needed.
- the plating layer may be an electroplating layer or a hot dipping layer, and the treatment method may be a conventional method.
- these steels are reheated as they are or once cooled to room temperature to a temperature range of 900 ° C. to 1300 ° C., and then hot rolled under the conditions shown in Table 2-1 and Table 2-2. Then, it was cooled under the conditions shown in Table 2-1 and Table 2-2 to obtain a hot rolled steel sheet having a thickness of 2.3 to 3.4 mm.
- the hot-rolled steel sheet thus obtained is pickled, and then subjected to skin pass rolling with a rolling reduction of 0.5%, partly subjected to hot dip galvanizing treatment and further alloying treatment, and used for material evaluation. did.
- the alphabetical letters prefixed to the test numbers in Table 2-1, Table 2-2, Table 3-1 and Table 3-2 indicate the steel types in Table 1.
- Table 1 shows the chemical composition of each steel
- Tables 2-1 and 2-2 show the production conditions of each hot-rolled steel sheet.
- Table 3-1 and Table 3-2 show the steel structure, grain size, and mechanical properties of each hot-rolled steel sheet (r value in each direction, tensile strength TS, elongation EL, hole expansion ratio ⁇ , brittle ductility transition). Temperature vTrs). The tensile test conformed to JIS Z 2241 and the hole expansion test conformed to Japan Iron and Steel Federation standard JFS T1001.
- the X-ray random intensity ratio is 0.5 ⁇ m pitch from the steel plate surface to the center of the plate thickness between 3/8 and 5/8 thickness positions of the cross section parallel to the rolling direction and the plate thickness direction using the above-mentioned EBSD. Measured with The r value in each direction was measured by the method described above. The Vickers hardness was measured with a load of 0.098 N (10 gf) using a micro Vickers tester. The Charpy test was performed according to JIS Z 2242, and the steel plate was processed into a 2.5 mm sub-size test piece.
Abstract
Description
すなわち、上記部材を始めとする部品の素材として用いられる鋼板には、優れた加工性に加えて低温靭性が非常に重要な特性として求められている。
しかしながら、特許文献1および2においては、伸びフランジ性については何ら言及されておらず、バーリング加工を行うような部材に適用した場合に成形不良が生じることが懸念される。また、鋼管分野、厚板分野においても低温靭性向上の知見があるものの、薄板ほどの成形性は必要とされないため、同様の懸念がある。
非特許文献1、2より、金属組織や圧延集合組織を均一化することにより伸びフランジ性を向上させられると考えられるが、低温靭性と伸びフランジ性の両立については配慮されていない。
C :0.01~0.2%、
Si:0.001~2.5%、
Mn:0.10~4.0%、
P :0.10%以下、
S :0.030%以下、
Al:0.001~2.0%、
N :0.01%以下、
Ti:(0.005+48/14[N]+48/32[S])%≦Ti≦0.3%、
Nb:0~0.06%、
Cu:0~1.2%、
Ni:0~0.6%、
Mo:0~1%、
V :0~0.2%、
Cr:0~2%、
Mg:0~0.01%、
Ca:0~0.01%、
REM:0~0.1%、
B:0~0.002%、
残部はFeおよび不純物からなる化学組成を有し、
鋼板表面から板厚の3/8厚み位置と5/8厚み位置とで区画された鋼板部分である板厚中心部において、板面の{100}<011>~{223}<110>方位群のX線ランダム強度比の平均値が6.5以下であるとともに、{332}<113>の結晶方位のX線ランダム強度比が5.0以下である集合組織を有し、
焼き戻しマルテンサイト、マルテンサイトおよび下部ベイナイトの合計面積率が85%超であるとともに、平均結晶粒径が12.0μm以下であるミクロ組織を有することを特徴とする熱延鋼板。
Nb:0.005~0.06%、
Cu:0.02~1.2%、
Ni:0.01~0.6%、
Mo:0.01~1%、
V :0.01~0.2%および
Cr:0.01~2%
からなる群から選択された1種または2種以上を含有するものであることを特徴とする上記(1)に記載の熱延鋼板。
前記仕上熱間圧延は、下記式(1)で規定される温度T1に対して、(T1+30)℃以上(T1+200)℃以下の第1温度域における1パス当たりの最大圧下率が30%以上、前記第1温度域における合計圧下率が50%以上、T1℃以上(T1+30)℃未満の第2温度域における合計圧下率が0~30%であるとともに、前記第1温度域または前記第2温度域で圧延を完了するものであり、
前記一次冷却は、下記式(2)を満たすとともに、冷却量が40℃以上140℃以下である水冷却であり、
前記二次冷却は、前記一次冷却後3秒以内に冷却を開始し、30℃/秒以上の平均冷却速度で冷却する水冷却であり、
前記巻き取りは、下記式(3)を満たす温度CTで巻き取るものである
ことを特徴とする熱延鋼板の製造方法:
T1(℃)=850+10×(C+N)×Mn+350×Nb+250×Ti+40×B+10×Cr+100×Mo+100×V
・・・ (1)
1≦t/t1≦2.5 ・・・ (2)
CT(℃)≦max[Ms,350] ・・・ (3)
t1=0.001×{(Tf-T1)×P1/100}2-0.109×{(Tf-T1)×P1/100}+3.1 ・・・ (4)
Ms(℃)=561-474×C-33×Mn-17×Ni-21×Mo ・・・ (5)
ここで、
式(1)および式(5)における各元素記号は、各元素の鋼中の含有量(質量%)、
式(2)におけるtは、前記第1温度域における30%以上の1パスでの圧下のうちの最終圧下から一次冷却開始までの時間(秒)、t1は前記式(4)によって決定される時間(秒)、
式(3)におけるmax[ ]は引数のうち最大の値を返す関数、Msは前記式(5)によって決定される温度であり、
式(4)におけるTfおよびP1は、それぞれ前記第1温度域における30%以上の1パスでの圧下のうちの最終圧下時の、鋼板温度および圧下率(%)である。
これらのX線ランダム強度比の規定は、本発明で特に重要である。
鋼板表面から測定して、板厚の3/8厚み位置と5/8厚み位置とで区画された鋼板部分である板厚中心部において板面のX線回折を行い、特定の結晶方位をもたず、ランダムな結晶方位をもつ標準試料(ランダム試料)に対する各方位の強度比を求めたときの、{100}<011>~{223}<110>方位群の平均値を6.5以下とすることにより、強度590MPа級の材料で穴拡げ率≧140%でかつ引張強度×穴拡げ率≧100000MPa・%、強度780MPа級の材料で穴拡げ率≧90%でかつ引張強度×穴拡げ率≧70000MPa・%、そして、強度980MPа級以上の材料で穴拡げ率≧40%でかつ引張強度×穴拡げ率≧50000MPa・%を満たす良好な伸びフランジ性を確保することが可能となる。なお、板面の{100}<011>~{223}<110>方位群のX線ランダム強度比の平均値は4.0以下であることが好ましい。
上記{332}<113>の結晶方位のX線ランダム強度比が5.0超であると、鋼板の機械的特性の異方性が極めて強くなり、特定方向の伸びフランジ性は向上するものの、それとは異なる方向の伸びフランジ性の低下が著しくなり、穴拡げ率が低下する。一方、現行の一般的な連続熱間圧延工程では実現が難しいが、上記{332}<113>の結晶方位のX線ランダム強度比が0.5未満になると穴拡げ性の劣化が懸念される。したがって、上記{332}<113>の結晶方位のX線ランダム強度比は0.5以上とすることが好ましい。
なお、{hkl}<uvw>で表される結晶方位とは、板面の法線方向が<hkl>に平行で、圧延方向が<uvw>と平行であることを示している。
上述した集合組織に加えて、以下の機械特性を満足することによりさらに良好な伸びフランジ性を確保することが可能となる。したがって、以下の機械特性を満足させることが好ましい。
rCは0.70以上であることが好ましい。なお、このr値の上限は特に定めないが、1.10以下とすることで、より優れた穴拡げ性を得ることができるので好ましい。
r30は1.10以下であることが好ましい。なお、この方向のr値の下限は特に定めないが、0.70以上とすることで、より優れた穴拡げ性を得ることができるので好ましい。
上述した集合組織に加えて、以下の機械特性を満足することによりさらに良好な伸びフランジ性を確保することが可能となる。したがって、以下の機械特性を満足させることが好ましい。
rLは0.70以上であることが好ましい。なお、rL値の上限は特に定めないが、rLを1.10以下とすることで、より優れた穴拡げ性を得ることができるので好ましい。
r60は、1.10以下であることが好ましい。r60値の下限は特に定めないが、r60を0.70以上とすることで、より優れた穴拡げ性を得ることができる。
まず、平均結晶粒径および組織の同定手法について述べる。
本発明では平均結晶粒径およびフェライト、さらに残留オーステナイトをEBSP-OIM(Electron Back Scatter Diffraction Pattern-Orientation Image Microscopy、商標)法を用いて定義している。
結晶方位の構造から相の同定が出来る他、多結晶材料では試料内の結晶方位分布や結晶粒の大きさを見ることができる。測定情報から、隣り合う測定点間の方位差を計算することができ、その平均値をKAM(Kernel average misorientation)値という。
一方でセメンタイトまたは准安定鉄炭化物が同一ラス内にシングルバリアントで析出したものを上部ベイナイトと定義した。これはセメンタイト析出の駆動力が焼き戻しマルテンサイトまたは下部ベイナイトと比較して小さいためと考えられる。
同様に組織をTEMで観察した際、セメンタイトまたは准安定炭化物の析出が観察されないものをマルテンサイトと定義した。
なお、これらの組織分率はTEM写真は20000倍の倍率で10視野以上撮影し、点算法で求めたものである。
なお、これらの組織が鋼板の100%を占めても伸びフランジ性および低温靭性の劣化は起こらないため、組織分率の上限は指定しない。
延性を向上させることを重視する場合には、面積率で15%未満のフェライトを含有させてもよい。
次に、本発明の熱延鋼板の化学組成の限定理由を説明する。なお、含有量を示す「%」は「質量%」を意味する。
C(炭素)は、鋼板の強度を向上させる作用を有する元素である。C含有量が0.01%未満では、上記作用による効果を得ることが困難である。したがって、C含有量は0.01%以上とする。一方、C含有量が0.2%超では、延性の低下を招くとともに、打ち抜き加工時の二次せん断面の割れ起点となるセメンタイト(Fe3C)等の鉄系炭化物が増加してしまい、伸びフランジ性の劣化を招く。したがって、C含有量は、0.2%以下とする。
Si(珪素)は、鋼板の強度を向上させる作用を有する元素であり、溶鋼の脱酸剤としての役割も果たす。Si含有量が0.001%未満では上記作用による効果を得ることが困難である。したがって、Si含有量は0.001%以上とする。また、Siは、セメンタイト等の鉄系炭化物の析出を抑制し、これにより強度と穴拡げ性とを向上させる作用をも有する。斯かる観点からは、Si含有量は0.1%以上とすることが好ましい。一方、Si含有量を2.5%超としても鋼板の強度を高める作用による効果は飽和してしまう。したがって、Si含有量は、2.5%以下とする。なお、セメンタイト等の鉄系炭化物の析出を抑制することによる強度と穴拡げ性とをより有効に向上させる観点から、Si含有量は1.2%以下とすることが好適である。
Mn(マンガン)は、固溶強化および焼入れ強化により鋼板の強度を向上させる作用を有する。Mn含有量が0.10%未満では、上記作用による効果を得ることが困難である。したがって、Mn含有量は0.10%以上とする。また、Mnは、オーステナイト域温度を低温側に拡大させて焼入れ性を向上させ、バーリング性に優れるマルテンサイトや下部ベイナイト等の低温変態組織の形成を容易にする作用を有する。斯かる観点からは、Mn含有量は1%以上とすることが好ましく、より好ましくは2%以上である。さらに、Mnは、Sによる熱間割れの発生を抑制する作用をも有する。斯かる観点からは、Mn含有量([Mn])とS含有量([S])とが [Mn]/[S]≧20を満足するMn量を含有させることが好ましい。一方、Mn含有量を4.0%超としても鋼板の強度を向上させる作用による効果は飽和してしまう。したがって、Mn含有量は4.0%以下とする。
P(燐)は、一般に不純物として含有される元素である。P含有量が0.10%超では、熱間圧延時に割れを惹き起こし、また、粒界に偏析して低温靭性を低下させるとともに、加工性や溶接性も低下させる。したがって、P含有量は0.10%以下とする。穴拡げ性や溶接性の観点からは、P含有量は0.02%以下とすることが好ましい。
S(硫黄)は、一般に不純物として含有される元素である。S含有量が0.030%超では、熱間圧延時に割れを惹き起こし、また、鋼中にA系介在物を生成させて穴拡げ性を劣化させる。したがって、S含有量は0.030%以下とする。穴拡げ性の観点からは、S含有量は0.010%以下とすることが好ましく、0.005%以下とすることがさらに好ましい。
Al(アルミニウム)は、鋼の精錬工程において溶鋼を脱酸して鋼を健全化する作用を有する。Al含有量が0.001%未満では、上記作用による効果を得ることが困難である。したがって、Al含有量は0.001%以上とする。Alはまた、Siと同様にセメンタイト等の鉄系炭化物の析出を抑制し、これにより強度と穴拡げ性とを向上させる作用をも有する。斯かる観点からは、Al含有量は0.016%以上とすることが好ましい。一方、Al含有量を2.0%超としても、上記脱酸作用による効果は飽和してしまい、経済的に不利となる。また、熱間圧延時に割れを惹き起こす場合がある。したがって、Al含有量は2.0%以下とする。鋼中における非金属介在物の生成を抑制し、延性および低温靭性を向上させる観点からは、Al含有量は0.06%以下とすることが好ましい。さらに好ましくは0.04%以下である。
N(窒素)は、一般に不純物として含有される元素である。N含有量が0.01%超では、熱間圧延時に割れを惹き起こし、また、耐時効性を劣化させる。したがって、N含有量は0.01%以下とする。耐時効性の観点からはN含有量は0.005%以下とすることが好ましい。
Ti(チタン)は、析出強化または固溶強化により鋼板の強度を向上させる作用を有する元素である。Ti含有量が、N含有量[N](単位:%)およびS含有量[S](単位:%)によって決定される(0.005+48/14[N]+48/32[S])%未満では、上記作用による効果を得ることが困難である。したがって、Ti含有量は(0.005+48/14[N]+48/32[S])%以上とする。一方、Ti含有量を0.3%超としても、上記作用による効果は飽和して経済的に不利となる。したがって、Ti含有量は0.3%以下とする。
Nb(ニオブ)、Cu(銅)、Ni(ニッケル)、Mo(モリブデン)、V(バナジウム)およびCr(クロム)は、析出強化または固溶強化により鋼板の強度を向上させる作用を有する元素である。したがって、これらの元素の1種または2種以上を必要に応じて適宜含有させることができる。しかし、Nb含有量を0.06%超、Cu含有量を1.2%超、Ni含有量を0.6%超、Mo含有量が1%超、V含有量を0.2%超およびCr含有量を2%超としても、上記作用による効果は飽和して経済的に不利となる。したがって、Nb含有量は0~0.06%、Cu含有量は0~1.2%、Ni含有量は0~0.6%、Mo含有量は0~1%、V含有量は0~0.2%、Cr含有量は0~2%とする。なお、上記作用による効果をより確実に得るには、Nb:0.005%以上、Cu:0.02%以上、Ni:0.01%以上、Mo:0.01%以上、V:0.01%以上およびCr:0.01%以上のいずれかを満足させることが好ましい。
Mg(マグネシウム)、Ca(カルシウム)およびREM(希土類元素)は、破壊の起点となって加工性を劣化させる原因となる非金属介在物の形態を制御し、加工性を向上させる作用を有する元素である。したがって、これらの元素の1種または2種以上を必要に応じて適宜含有させてもよい。しかし、Mg含有量を0.01%超、Ca含有量を0.01%超、REM含有量を0.1%超としても、上記作用による効果は飽和して、経済的に不利となる。したがって、Mg含有量は0~0.01%、Ca含有量は0~0.01%、REM含有量は、0~0.1%とする。なお、上記作用による効果をより確実に得るには、Mg、CaおよびREMのいずれか元素の含有量を0.0005%以上とすることが好ましい。
B(硼素)は、Cと同様に粒界に偏析し、粒界強度を高める作用を有する元素である。すなわち、固溶Cと同様に固溶Bとして粒界に偏析することにより、破断面割れの防止を実現するうえで有効に作用する。そして、Cが炭化物として粒内に析出して粒界における固溶Cが減少したとしても、Bが粒界に偏析することで、Cの粒界における減少を補償することが可能となる。したがって、Bを必要に応じて適宜含有させてもよい。しかし、B含有量を0.002%超とすると、熱間圧延におけるオーステナイトの再結晶が過度に抑制され、未再結晶オーステナイトからのγ→α変態集合組織を強め、等方性を劣化させる恐れがある。したがって、B含有量は、0~0.002%以下とする。Bは、連続鋳造後の冷却工程におけるスラブ割れを惹き起こすことが懸念される元素であり、斯かる観点からはB含有量を0.0015%以下とすることが好ましい。なお、上記作用による効果をより確実に得るには、B含有量は0.0002%以上とすることが好ましい。また、Bは、焼入れ性を向上させ、バーリング性にとって好ましいミクロ組織である連続冷却変態組織の形成を容易にする作用をも有する。
不純物としては、Zr、Sn、Co、Zn、Wが含有される場合があるが、これらの元素の含有量が合計で1%以下であれば問題ない。
上述した鋼板の表面には、耐食性の向上等を目的としてめっき層を備えさせて表面処理鋼板としてもよい。めっき層は電気めっき層であってもよく溶融めっき層であってもよい。電気めっき層としては、電気亜鉛めっき、電気Zn-Ni合金めっき等が例示される。溶融めっき層としては、溶融亜鉛めっき、合金化溶融亜鉛めっき、溶融アルミニウムめっき、溶融Zn-Al合金めっき、溶融Zn-Al-Mg合金めっき、溶融Zn-Al-Mg-Si合金めっき等が例示される。めっき付着量は特に制限されず、従来と同様でよい。また、めっき後に適当な化成処理(例えば、シリケート系のクロムフリー化成処理液の塗布と乾燥)を施して、耐食性をさらに高めることも可能である。また、有機皮膜形成、フィルムラミネート、有機塩類/無機塩類処理を施すことも可能である。
次に本発明の熱延鋼板の製造方法について述べる。
優れた伸びフランジ性および低温靭性を実現するためには、所定の集合組織を形成させることならびに焼き戻しマルテンサイト、マルテンサイトおよび下部ベイナイトを主体とする組織とすることが重要である。さらに、組織間硬度差が小さいことや各方向のr値が所定の条件を満足することが好ましい。これらを満たすための製造条件の詳細を以下に記す。
T1(℃)=850 +10×(C+N)×Mn +350×Nb +250×Ti +40×B +10×Cr +100×Mo +100×V
・・・ 式(1)
を基準に、(T1+30)℃以上(T1+200)℃以下の第1温度域で大きな圧下率で大圧下圧延による加工を行い、T1℃以上(T1+30)℃未満の第2温度域で圧下を行わないか小さな圧下率で軽圧下圧延による加工を行い、前記第1温度域または前記第2温度域で圧延を完了することにより最終製品の局部変形能を確保できる。
さらに良好な穴拡げ性を得るためには、第1温度域で大圧下による歪を蓄積することが重要で、第1温度域における1パス当たりの最大圧下率を30%以上、換言すれば、第1温度域において圧下率30%以上の1パスでの圧下を少なくとも1回以上行い、かつ圧下率の合計を50%以上とすることは必須である。さらには、圧下率の合計を70%以上とすることがより好ましい。一方、前記圧下率の合計が90%を超える圧下率とすると、温度確保や過大な圧延負荷を加えることとなるため、前記圧下率の合計は90%以下とすることが好ましい。
上記第1温度域における30%以上の1パスでの最終圧下パスから、一次冷却開始までの時間t(秒)は、第1温度域における30%以上の1パスでの最終圧下の、鋼板温度Tf(℃)と圧下率P1(%)に対して、下記式(2)を満たすようにする。
t/t1が1に満たないと再結晶が抑制されて所定の集合組織が得られず、t/t1が2.5を超えると、粗粒化が進み、伸びと低温脆性が著しく低下する。
1≦t/t1≦2.5 ・・・ (2)
ここで、t1とは下記の式(4)で決定される時間(秒)である。
t1=0.001×{(Tf-T1)×P1/100}2-0.109×{(Tf-T1)×P1/100}+3.1 ・・・ (4)
一次冷却終了から二次冷却開始までの間は、水冷却を行わないため高温域に保持されることになるが、一次冷却を行った後、3秒を超えて二次冷却を開始するか、あるいは、一次冷却を行った後、3秒以内に30℃/秒未満の平均冷却速度で二次冷却を行うと、仕上げ圧延完了から巻き取り開始までの二次冷却中に、フェライト、パーライト、上部ベイナイト等の高温変態相の組織分率が15%を超え、所望の組織分率および組織間硬度差が得られず、特に低温靭性が劣化してしまう。二次冷却における平均冷却速度の上限は特に定めないが、冷却設備の能力上、300℃/秒以下が妥当な平均冷却速度である。
CT(℃)≦max[Ms,350] ・・・ (3)
ここで、Msは下記式(5)により決定され、下記式(5)中の元素記号は各元素の鋼中の含有量(質量%)を示す。
Ms(℃)=561-474×C-33×Mn-17×Ni-21×Mo ・・・ (5)
したがって、粗熱間圧延は、1000℃以上1200℃以下の温度域における1パス当たりの最大圧下率が40%以上であり、オーステナイトの平均粒径を200μm以下とするものであることが好ましい。
さらには、必要に応じて鋼板の表面にめっき層を備えさせて表面処理鋼板としてもよい。めっき層は電気めっき層であってもよく溶融めっき層であってもよく、その処理方法は常法によればよい。
実施例として、表1に示す化学組成を有する、鋼A~Pの本発明の請求項を満たす適合鋼、および鋼a~eの比較鋼を用いて検討した。
なお、引張試験はJIS Z 2241に、穴拡げ試験は日本鉄鋼連盟規格JFS T1001にそれぞれ準拠した。X線ランダム強度比は前述のEBSDを用いて圧延方向および板厚方向に平行な断面について、鋼板表面から板厚の3/8~5/8厚み位置間の板厚中心部を0.5μmピッチで測定した。また、各方向のr値については、前述した方法により測定した。ビッカース硬さはマイクロビッカース試験機を用いて、荷重0.098N(10gf)で測定した。シャルピー試験はJIS Z 2242に準拠して行い、鋼板を2.5mmサブサイズ試験片に加工して行った。
Claims (12)
- 質量%で、
C :0.01~0.2%、
Si:0.001~2.5%、
Mn:0.10~4.0%、
P :0.10%以下、
S :0.030%以下、
Al:0.001~2.0%、
N :0.01%以下、
Ti:(0.005+48/14[N]+48/32[S])%≦Ti≦0.3%、
Nb:0~0.06%、
Cu:0~1.2%、
Ni:0~0.6%、
Mo:0~1%、
V :0~0.2%、
Cr:0~2%、
Mg:0~0.01%、
Ca:0~0.01%、
REM:0~0.1%、
B:0~0.002%、
残部はFeおよび不純物からなる化学組成を有し、
鋼板表面から板厚の3/8厚み位置と5/8厚み位置とで区画された鋼板部分である板厚中心部において、板面の{100}<011>~{223}<110>方位群のX線ランダム強度比の平均値が6.5以下であるとともに、{332}<113>の結晶方位のX線ランダム強度比が5.0以下である集合組織を有し、
焼き戻しマルテンサイト、マルテンサイトおよび下部ベイナイトの合計面積率が85%超であるとともに、平均結晶粒径が12.0μm以下であるミクロ組織を有することを特徴とする熱延鋼板。 - 前記化学組成が、質量%で、
Nb:0.005~0.06%、
Cu:0.02~1.2%、
Ni:0.01~0.6%、
Mo:0.01~1%、
V :0.01~0.2%および
Cr:0.01~2%
からなる群から選択された1種または2種以上を含有するものであることを特徴とする請求項1に記載の熱延鋼板。 - 前記化学組成が、質量%で、Mg:0.0005~0.01%、Ca:0.0005~0.01%およびREM:0.0005~0.1%からなる群から選択された1種または2種以上を含有するものであることを特徴とする請求項1または請求項2に記載の熱延鋼板。
- 前記化学組成が、質量%で、B:0.0002~0.002%を含有するものであることを特徴とする請求項1~3のいずれか1項に記載の熱延鋼板。
- 荷重0.098Nのビッカース硬さを100点以上測定した際の硬さの平均値をE(HV0.01)、標準偏差をσ(HV0.01)としたとき、σ(HV0.01)/E(HV0.01)が0.08以下であるミクロ組織を有することを特徴とする請求項1~4のいずれか1項に記載の熱延鋼板。
- 圧延方向と直角方向のr値(rC)が0.70以上および圧延方向に対し30°の方向のr値(r30)が1.10以下である機械特性を有することを特徴とする請求項1~5のいずれか1項に記載の熱延鋼板。
- 圧延方向のr値(rL)が0.70以上および圧延方向に対し60°の方向のr値(r60)が1.10以下である機械特性を有することを特徴とする請求項1~6のいずれか1項に記載の熱延鋼板。
- 鋼板の表面に、めっき層を備えることを特徴とする請求項1~7のいずれか1項に記載の熱延鋼板。
- 請求項1~7のいずれか1項に記載の化学組成を有するスラブに、粗熱間圧延、仕上熱間圧延、一次冷却および二次冷却を順次施して巻き取ることにより熱延鋼板とする熱延鋼板の製造方法において、
前記仕上熱間圧延は、下記式(1)で規定される温度T1に対して、(T1+30)℃以上(T1+200)℃以下の第1温度域における1パス当たりの最大圧下率が30%以上、前記第1温度域における合計圧下率が50%以上、T1℃以上(T1+30)℃未満の第2温度域における合計圧下率が0~30%であるとともに、前記第1温度域または前記第2温度域で圧延を完了するものであり、
前記一次冷却は、下記式(2)を満たすとともに、冷却量が40℃以上140℃以下である水冷却であり、
前記二次冷却は、前記一次冷却後3秒以内に冷却を開始し、30℃/秒以上の平均冷却速度で冷却する水冷却であり、
前記巻き取りは、下記式(3)を満たす温度CTで巻き取るものである
ことを特徴とする熱延鋼板の製造方法:
T1(℃)=850+10×(C+N)×Mn+350×Nb+250×Ti+40×B+10×Cr+100×Mo+100×V
・・・ (1)
1≦t/t1≦2.5 ・・・ (2)
CT(℃)≦max[Ms,350] ・・・ (3)
t1=0.001×{(Tf-T1)×P1/100}2-0.109×{(Tf-T1)×P1/100}+3.1 ・・・ (4)
Ms(℃)=561-474×C-33×Mn-17×Ni-21×Mo ・・・ (5)
ここで、
式(1)および式(5)における各元素記号は、各元素の鋼中の含有量(質量%)、
式(2)におけるtは、前記第1温度域における30%以上の1パスでの圧下のうちの最終圧下から一次冷却開始までの時間(秒)、t1は前記式(4)によって決定される時間(秒)、
式(3)におけるmax[ ]は引数のうち最大の値を返す関数、Msは前記式(5)によって決定される温度であり、
式(4)におけるTfおよびP1は、それぞれ前記第1温度域における30%以上の1パスでの圧下のうちの最終圧下時の、鋼板温度および圧下率(%)である。 - 前記粗熱延圧延は、1000℃以上1200℃以下の温度域における1パス当たりの最大圧下率が40%以上であり、オーステナイトの平均粒径を200μm以下とするものであることを特徴とする請求項9に記載の熱延鋼板の製造方法。
- 前記仕上熱間圧延の(T1+30℃)以上(T1+150℃)以下の温度域における最大加工発熱量が18℃以下であることを特徴とする請求項9または請求項10に記載の熱延鋼板の製造方法。
- 請求項9~11のいずれか1項に記載の熱延鋼板の製造方法により得られた熱延鋼板の表面にめっき処理を施すことを特徴とする熱延鋼板の製造方法。
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JPWO2013103125A1 (ja) | 2015-05-11 |
KR101617115B1 (ko) | 2016-04-29 |
TW201335383A (zh) | 2013-09-01 |
CA2860165C (en) | 2016-12-06 |
MX2014008124A (es) | 2014-09-15 |
ES2663747T3 (es) | 2018-04-16 |
BR112014016420A2 (pt) | 2017-06-13 |
EP2801637A1 (en) | 2014-11-12 |
MX359273B (es) | 2018-09-21 |
RU2014132066A (ru) | 2016-02-27 |
PL2801637T3 (pl) | 2018-07-31 |
US10087499B2 (en) | 2018-10-02 |
US20150017471A1 (en) | 2015-01-15 |
BR112014016420A8 (pt) | 2017-07-04 |
CN104040009A (zh) | 2014-09-10 |
JP5621942B2 (ja) | 2014-11-12 |
RU2587003C2 (ru) | 2016-06-10 |
EP2801637B1 (en) | 2018-02-07 |
EP2801637A4 (en) | 2016-04-20 |
CA2860165A1 (en) | 2013-07-11 |
TWI488977B (zh) | 2015-06-21 |
KR20140098841A (ko) | 2014-08-08 |
ES2663747T9 (es) | 2018-09-20 |
CN104040009B (zh) | 2016-05-18 |
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