WO2016158961A1 - ホットスタンプ用鋼板およびその製造方法、並びにホットスタンプ成形体 - Google Patents

ホットスタンプ用鋼板およびその製造方法、並びにホットスタンプ成形体 Download PDF

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WO2016158961A1
WO2016158961A1 PCT/JP2016/060145 JP2016060145W WO2016158961A1 WO 2016158961 A1 WO2016158961 A1 WO 2016158961A1 JP 2016060145 W JP2016060145 W JP 2016060145W WO 2016158961 A1 WO2016158961 A1 WO 2016158961A1
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Prior art keywords
steel sheet
hot stamping
hot
mass
less
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PCT/JP2016/060145
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English (en)
French (fr)
Japanese (ja)
Inventor
東　昌史
嘉宏 諏訪
雄介 近藤
佐藤　浩一
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新日鐵住金株式会社
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Application filed by 新日鐵住金株式会社 filed Critical 新日鐵住金株式会社
Priority to CN201680017529.1A priority Critical patent/CN107427889B/zh
Priority to US15/559,731 priority patent/US20180044754A1/en
Priority to CA2979978A priority patent/CA2979978A1/en
Priority to BR112017020165-8A priority patent/BR112017020165A2/pt
Priority to ES16772842T priority patent/ES2781465T3/es
Priority to RU2017135379A priority patent/RU2683397C1/ru
Priority to MX2017012377A priority patent/MX2017012377A/es
Priority to EP16772842.7A priority patent/EP3278895B1/en
Priority to JP2017510030A priority patent/JP6515356B2/ja
Priority to KR1020177027982A priority patent/KR102000863B1/ko
Publication of WO2016158961A1 publication Critical patent/WO2016158961A1/ja

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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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/04—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing in a continuous process
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
    • B21B45/0239—Lubricating
    • B21B45/0242—Lubricants
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D24/00—Special deep-drawing arrangements in, or in connection with, presses
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F11/00—Inhibiting corrosion of metallic material by applying inhibitors to the surface in danger of corrosion or adding them to the corrosive agent
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B2001/028—Slabs

Definitions

  • the present invention relates to a steel sheet for hot stamping excellent in scale adhesion at the time of hot stamping, a method for producing the same, and a hot stamping shaped body that is a shaped body thereof.
  • Patent Document 6 discloses a technique for suppressing the generation of scale by setting the atmosphere in the heating furnace to a non-oxidizing atmosphere. However, it is necessary to strictly control the atmosphere in the heating furnace, resulting in an increase in equipment cost and inferior productivity.
  • JP 2008-214650 A Japanese Patent Laid-Open No. 1-2230715 JP-A-2-217425 JP 2002-143935 A JP 2003-154413 A JP 2002-18531 A JP 2004-106034 A JP 2002-18531 A JP 2008-240046 A JP 2010-174302 A JP 2008-214650 A
  • the present invention provides a steel sheet for hot stamping that is excellent in scale adhesion at the time of hot stamping and that does not cause adhesion of molten metal to a mold, a method for manufacturing the same, and a hot stamping molded body thereof. With the goal.
  • the present inventors diligently studied a method for solving the above problems.
  • 0.50 mass% to 3.00 mass% of Si is contained in the steel sheet, and the amount of rust preventive oil applied to the steel sheet is 50 mg / m.
  • the surface roughness of the steel sheet is Rz> 2.5 ⁇ m in the range of 2 to 1500 mg / m 2 .
  • S content contained in a rust prevention oil shall be 5 mass% or less.
  • the composition of the steel sheet is mass%, Ni: 0.01% to 2.00% Cu: 0.01% to 2.00% Cr: 0.01% to 2.00%, Mo: 0.01% to 2.00%, Nb: 0.005% to 0.100%, V: 0.005% to 0.100%, and W: 0.005% to 0.100%,
  • composition of the steel sheet is mass%, One of the above-mentioned (1) to (3), which contains one or more selected from the group consisting of REM, Ca, Ce and Mg in a total amount of 0.0003% to 0.0300%
  • a method for producing a steel sheet for hot stamping characterized in that the residual amount of rust preventive oil on the steel sheet surface is limited to 50 mg / m 2 to 1500 mg / m 2 .
  • the method further includes a step of cold-rolling the pickled hot-rolled steel sheet to obtain a cold-rolled steel sheet,
  • the method further includes a step of cold rolling the pickled hot rolled steel sheet and further performing a heat treatment in a continuous annealing facility or a box annealing furnace to obtain a cold rolled steel sheet,
  • the composition of the slab is mass%, Ni: 0.01% to 2.00% Cu: 0.01% to 2.00% Cr: 0.01% to 2.00%, Mo: 0.01% to 2.00%, Nb: 0.005% to 0.100%, V: 0.005% to 0.100%, and W: 0.005% to 0.100%,
  • composition of the slab is mass%, Any one of (1) or two or more selected from the group consisting of REM, Ca, Ce and Mg is contained in a total amount of 0.0003% to 0.0300%.
  • the surface of the hot stamping body has Si oxide, FeO, Fe 3 O 4 , and Fe 2 O 3 , and the scale has a thickness of 10 ⁇ m or less (12)
  • the composition of the hot stamping molded body is mass%, Ni: 0.01% to 2.00% Cu: 0.01% to 2.00% Cr: 0.01% to 2.00%, Mo: 0.01% to 2.00%, Nb: 0.005% to 0.100%, V: 0.005% to 0.100%, and W: 0.005% to 0.100%,
  • composition of the hot stamping molded body is mass%, One of the above-mentioned (12) to (14), which contains one or more selected from the group consisting of REM, Ca, Ce and Mg in a total of 0.0003% to 0.0300%
  • the hot stamping molded article as described.
  • a steel sheet for hot stamping that is excellent in scale adhesion at the time of hot stamping and that does not cause adhesion of molten metal to the mold, a manufacturing method thereof, and a hot stamping molded body thereof.
  • FIG. 1 is a diagram showing the relationship between the amount of oil applied to a steel plate and the surface roughness Rz of the steel plate.
  • FIG. 2 is a diagram for explaining that the scale easily peels off as the S concentration in the oil coating increases.
  • FIG. 3 is a diagram showing the relationship between the pickling time and the surface roughness Rz of the steel sheet.
  • FIG. 4A is a photograph showing the microstructure of the surface layer of the hot-rolled steel sheet before pickling.
  • FIG. 4B is a photograph showing the surface layer microstructure after pickling.
  • FIG. 5 is a diagram showing the relationship between the oil coating amount and the thickness of the scale.
  • FIG. 6A is a photograph showing a cross section of the surface of the hot stamping molded body of the example of the present invention.
  • FIG. 6A is a photograph showing a cross section of the surface of the hot stamping molded body of the example of the present invention.
  • FIG. 6B is a photograph showing a cross section of the surface of the hot stamping molded body of the comparative example.
  • FIG. 7 is a diagram for explaining that the number density of irregularities after hot stamping heat treatment is less than 3 when the surface roughness Rz before hot stamping heat treatment is less than 2.5.
  • the steel sheet for hot stamping of the present invention contains 0.5 mass% to 3.0 mass% of Si in the steel sheet, and the amount of rust preventive oil applied to the steel sheet is 50 mg / m 2 to 1500 mg / m. 2 and the surface roughness of the steel sheet is Rz> 2.5 ⁇ m. And preferably, S content contained in antirust oil shall be 5 mass% or less.
  • the present inventors have investigated the surface properties of steel sheets and the effects of various treatments for the purpose of improving the scale adhesion of steel sheets that are not plated (cold-rolled steel sheets or hot-rolled steel sheets).
  • the steel sheet after degreasing showed excellent scale adhesion, but it was found that the scale adhesion deteriorates significantly when rust preventive oil is applied.
  • the relationship between the scale adhesion and the rust preventive oil was investigated, it was found that the scale tends to peel off as the amount of S contained as an impurity in the rust preventive oil increases.
  • S in the rust preventive oil affects the scale adhesion.
  • hot-rolled steel sheets for hot stamping that have been pickled, and cold-rolled steel sheets for hot stamping after cold rolling or annealing are used to prevent the occurrence of rust between production and use. It is necessary to apply anti-rust oil.
  • the steel plate after pickling is generally applied with oil exceeding 1500 mg / m 2 on the assumption that the period from delivery to customer to use becomes long.
  • the present inventors investigated the influence of the amount of oil applied for the purpose of achieving both scale adhesion and rust prevention. As shown in FIG. 1, the range of the amount of oil applied and the surface roughness of the steel sheet was strict. It has been found that the adhesion to the scale is improved by controlling to the above.
  • the effect is exhibited by setting the oil coating amount to 50 mg / m 2 to 1500 mg / m 2 .
  • the reason why the lower limit was set to 50 mg / m 2 was that 50 mg / m 2 was set as the lower limit oil amount because it was difficult to ensure excellent rust prevention properties if less than this oil amount.
  • it is 100 mg / m 2 or more, more preferably 200 mg / m 2 or more.
  • the reason why the upper limit of the oil coating amount is 1500 mg / m 2 is to obtain an excellent effect of scale adhesion. When the oil coating amount exceeds 1500 mg / m 2 , the scale adhesion deteriorates, so the upper limit is 1500 mg / m 2 .
  • the upper limit is 1000 mg / m 2 , more preferably the upper limit is 900 mg / m 2 , and still more preferably the upper limit is 800 mg / m 2 .
  • the oil coating on the surface of the steel plate burns during heating, it causes generation of soot. Also from this, it is preferable that the amount of oil coating is small.
  • the scale adhesion shown in FIG. 1 was evaluated by a hot shallow drawing test using a cylindrical mold having a diameter of 70 mm and a depth of 20 mm.
  • the steel sheet was heated in an electric heating device at a temperature of 50 ° C./s to a temperature range of 800 ° C. to 1100 ° C., held for 0 seconds to 120 seconds, then turned off and allowed to cool to 650 ° C. And was subjected to hot shallow drawing with the above mold.
  • the molded specimen is visually observed, and the scale peel-off area is 5% or less, the scale adhesion is good ( ⁇ ), the scale peel-off area is 5-15%, the scale is bad ( ⁇ ), the scale A case where the peeled area was more than 15% was regarded as poor (x).
  • the area where the scale peeled off was 5% or less within the scope of the present invention.
  • the heating method is not particularly limited, and scale adhesion can be evaluated.
  • any conditions of a heating furnace, far infrared rays, near infrared rays, and energization heating may be used.
  • the further excellent scale adhesiveness can be obtained by controlling the atmosphere in a heating furnace, suppressing the oxidation of a steel plate, and making a scale thin.
  • the shallow drawing test temperature may be any temperature range as long as the steel sheet can be processed, but in general, the hot stamping steel sheet has high strength and excellent strength by processing in the austenite area and subsequent die quenching. It has a shape freezing property. From this, characteristic evaluation was performed by hot shallow drawing at 650 ° C., which exceeds Ar 3.
  • oiling method electrostatic oiling, spraying, roll coater, etc. are generally used, but the oiling method is not limited as long as the amount of oiling can be secured.
  • the oil type is not specified.
  • NOX-RUST530F manufactured by Parker Kosan Co., Ltd.
  • the species is not limited.
  • the oil coating amount may be measured by any method as long as it can be measured, but the present inventors measured by the following method. First, the steel plate coated with rust preventive oil was cut into 150 mm squares, and then a tape was attached so that a 100 mm ⁇ 100 mm region was exposed. Then, the weight of the oil coating and the steel plate (including the weight of the tape) that has been sealed is measured in advance. Next, degrease by wiping off the rust preventive oil on the steel sheet surface with a cloth soaked with acetone, measure the weight of the degreased steel sheet, and compare the weight before and after degreasing to obtain the amount of oil per unit area. Was calculated. Each steel plate was carried out at three locations, and the average value of the adhesion amount was defined as the oil adhesion amount of each steel plate.
  • the present inventors investigated the relationship between the S content in the oil and the scale peeling area ratio. As the S content in the oil decreased, the scale adhesion improved. In particular, it has been found that when the S content in the oil coating is 5% by mass or less, the scale peeling area is almost 0%. Although the detailed mechanism is unknown, the oil contained in the rust preventive oil does not burn during heating, but the S contained as an impurity remains on the surface of the steel sheet and concentrates in the scale, degrading the scale adhesion. It is thought that For this reason, it is preferable to reduce the S content contained in the rust preventive oil.
  • the surface roughness of the steel sheet In order to ensure scale adhesion, the surface roughness of the steel sheet needs to be Rz> 2.5 ⁇ m.
  • the results obtained by investigating the relationship between the surface roughness Rz of the steel sheet and the scale adhesion are as shown in FIG.
  • the unevenness is formed at the interface between the base iron and the scale, and the adhesion is further improved.
  • This effect is generally called the anchor effect.
  • the scale produced during heating with this steel sheet is thin. As a result, the steel sheet having a thin scale is affected by the surface state of the ground iron, so that a scale having irregularities is formed.
  • the surface roughness of the steel sheet before hot stamping needs to be Rz> 2.5 ⁇ m.
  • Rz ⁇ 2.5 ⁇ m the surface roughness of the steel sheet is small and the anchor effect is insufficient, so that excellent scale adhesion during hot stamping cannot be ensured.
  • the upper limit of the scale adhesion of the present invention can be obtained without any particular provision, but if the scale adhesion is excessively improved, it is difficult to remove the scale in a subsequent process such as shot blasting. It becomes. Therefore, it is preferable that Rz ⁇ 8.0 ⁇ m. More preferably, Rz ⁇ 7.0 ⁇ m. However, even if Rz ⁇ 8.0 ⁇ m, it is possible to ensure excellent scale adhesion which is an effect of the present invention.
  • SURFCOM2000DX / SD3 manufactured by Tokyo Seimitsu Co., Ltd.
  • the scale may be a scale mainly composed of Si oxide, Fe 3 O 4 , Fe 2 O 3 , and FeO.
  • the Si oxide is present at the interface between the ground iron and the iron-based scale (FeO, Fe 2 O 3 , Fe 2 O 3 ), thereby controlling the thickness of the iron-based scale. For this reason, it is necessary to include Si oxide in the scale. Since the main purpose is to control the thickness of the iron-based oxide, it is sufficient that the Si oxide exists even if it is very thin. For example, even if it is 1 nm, the effect is exhibited.
  • composition analysis of the scale of the molded body was performed by X-ray diffraction after cutting a plate from the bottom of the cylindrical portion of the shallow drawing test piece. From the peak intensity ratio of each oxide, the volume fraction of each Fe-based oxide was measured. Since the Si oxide was very thin and the volume fraction was less than 1%, quantitative evaluation by X-ray diffraction was difficult. However, it is possible to confirm the presence of Si oxide at the interface between the scale and the ground iron by EPMA (Electron-Probe-Micro-Analyzer) line analysis.
  • EPMA Electro-Probe-Micro-Analyzer
  • the thickness of the scale is preferably 10 ⁇ m or less. If the thickness of the scale is 10 ⁇ m or less, the scale adhesion is further improved. If the thickness of the scale exceeds 10 ⁇ m, the scale tends to be peeled off due to thermal stress acting during cooling during hot stamping. On the other hand, after that, in a scale removal process such as shot blasting or wet blasting, cracks occur between Fe-based scales, and the scales existing outside peel off. As a result, there was a problem that it was inferior in scale removability. For this reason, the thickness of the scale is preferably 10 ⁇ m or less. More preferably, it is 7 micrometers or less, More preferably, it is 5 micrometers or less. The thickness of the scale is achieved by controlling the Si content of the steel sheet within a predetermined range and simultaneously controlling the oil coating amount within a predetermined range. FIG. 5 shows the relationship between the oil coating amount and the scale thickness.
  • FIG. 6A shows a photograph of the interface between the base metal and the scale of the molded article having excellent scale adhesion
  • FIG. 6B shows a photograph of the interface between the ground iron and scale having inferior scale adhesion. Since this unevenness contributes to the improvement of scale adhesion at the time of hot stamping, excellent scale adhesion can be ensured by controlling to the above range. With unevenness of less than 0.2 ⁇ m, the anchor effect is not sufficient and the scale adhesion is poor.
  • the thickness is 0.0 ⁇ m or less. More preferably, it is 6.0 micrometers or less, More preferably, it is 4.0 micrometers or less. However, even if the unevenness exceeds 8.0 ⁇ m, excellent scale adhesion which is the effect of the present invention can be ensured.
  • corrugation of a molded object has correlation with the surface roughness Rz of a steel plate, and can be controlled by setting it as the surface roughness Rz> 2.5micrometer of a steel plate.
  • C 0.100% to 0.600%
  • C is an element contained for increasing the strength of the steel sheet. If the C content is less than 0.100%, a tensile strength of 1180 MPa or more cannot be ensured, and a high-strength molded article that is the object of hot stamping cannot be ensured. On the other hand, if the C content exceeds 0.600%, weldability and workability become insufficient, so the C content is set to 0.100% to 0.600%. Preferably it is 0.100% to 0.550%, more preferably 0.150% to 0.500%. However, if the strength of the molded body is not required, excellent scale adhesion can be ensured even if the C content is less than 0.150%.
  • Si 0.50% to 3.00% Si is an essential element because it improves the scale adhesion by controlling the scale composition during hot stamping. If the Si content is less than 0.50%, the thickness of the Fe-based scale cannot be controlled, and excellent scale adhesion cannot be ensured. For this reason, the Si content needs to be 0.50% or more. Further, when considering application to a member having severe molding at the time of hot stamping, it is preferable to increase the Si content. Accordingly, the Si content is preferably 0.70% or more, more preferably 0.90% or more. On the other hand, Si increases the Ae3 point and increases the heating temperature necessary for making martensite as the main phase. Therefore, if it is excessively contained, productivity and economy are lowered. For this reason, the upper limit of the Si content is 3.00%. Preferably, the upper limit of the Si content is 2.5%, more preferably the upper limit is 2.0%. However, excellent scale adhesion can be ensured except for productivity and economy.
  • Mn 1.20% to 4.00%
  • Mn needs to be contained in an amount of 1.20% or more in order to delay the ferrite transformation in the cooling process during hot stamping and to make the hot stamping compact into a martensite main phase. If the Mn content is less than 1.20%, martensite cannot be used as the main phase, and it is difficult to ensure high strength, which is the purpose of the hot stamped molded article, so the lower limit of the Mn content is 1.20%. To do. However, if the strength of the molded body is not required, excellent scale adhesion can be ensured even if the Mn content is less than 1.20%.
  • the Mn content exceeds 4.00%, the effect is saturated and embrittlement occurs, and cracking occurs during casting, cold rolling, or hot rolling, so the upper limit of the Mn content is 4 0.000%.
  • the Mn content is preferably in the range of 1.50% to 3.50%, more preferably in the range of 2.00% to 3.00%.
  • Ti 0.005% to 0.100%
  • Ti is an element that suppresses B from becoming a nitride and improves hardenability by combining with N to form TiN. Since this effect becomes significant when the Ti content is 0.005% or more, the Ti content is set to 0.005% or more. However, if the Ti content exceeds 0.100%, Ti carbide is formed, the amount of C contributing to the strengthening of martensite is reduced and the strength is reduced, so the upper limit of the Ti content is 0.100. %.
  • the C content is in the range of 0.005% to 0.080%, more preferably in the range of 0.005% to 0.060%.
  • B 0.0005% to 0.0100% B improves the hardenability at the time of hot stamping and contributes to making the main phase martensite. Since this effect becomes remarkable when the B content is 0.0005% or more, the B content needs to be 0.0005% or more. On the other hand, if the B content exceeds 0.0100%, the effect is saturated and iron boride precipitates and loses the effect of B hardenability. Therefore, the upper limit of the B content is 0.0100%. %.
  • the B content is preferably in the range of 0.0005% to 0.0080%, more preferably in the range of 0.0005% to 0.0050%.
  • P 0.100% or less
  • P is an element that segregates in the central part of the plate thickness of the steel sheet and also an element that embrittles the weld. Therefore, the upper limit of the P content is 0.100%. A more preferred upper limit is 0.050%.
  • the P content is preferably low, and the lower limit is not particularly defined, and the effect of the present invention is exhibited. However, reducing P to less than 0.001% is economical from the viewpoint of de-P productivity and cost. Therefore, the lower limit is preferably set to 0.001%.
  • the upper limit of the S content is 0.0100%.
  • the lower limit of the S content is set to 0.0001%.
  • the S content is preferably in the range of 0.0001% to 0.0070%, more preferably in the range of 0.0003% to 0.0050%.
  • Al 0.005% to 1.000% Since Al acts as a deoxidizer, the Al content is set to 0.005% or more. If the Al content is less than 0.005%, a sufficient deoxidation effect cannot be obtained, and a large amount of inclusions (oxides) are present in the steel sheet. These inclusions are not preferable because they become a starting point of breakage during hot stamping and cause breakage. Since this effect becomes remarkable when the Al content is 0.005% or more, the Al content needs to be 0.005% or more. On the other hand, if the Al content exceeds 1.000%, the Ac3 point is increased and the heating temperature during hot stamping is increased.
  • hot stamping is a high-strength that has a complicated shape by heating a steel plate to an austenite single-phase region, and performing hot mold pressing and quenching using a die that excels in formability.
  • This is a technique for obtaining a strong molded body.
  • Al is contained in a large amount, the Ac3 point is remarkably improved, the heating temperature necessary for the austenite single-phase region heating is increased, and the productivity is lowered.
  • the upper limit of the Al content needs to be 1.000%.
  • the Al content is preferably in the range of 0.005% to 0.500%, more preferably in the range of 0.005% to 0.300%.
  • N 0.0100% or less
  • N is an element that forms coarse nitrides and degrades bendability and hole expandability. If the N content exceeds 0.0100%, the bendability and hole expansibility deteriorate significantly, so the upper limit of the N content is 0.0100%.
  • the N content is preferably 0.0070 or less, more preferably 0.0050% or less.
  • the lower limit of the N content is not particularly required. However, if the N content is reduced to less than 0.0001%, the manufacturing cost is greatly increased, so 0.0001% is a practical lower limit. From the viewpoint of manufacturing cost, the N content is more preferably 0.0005% or more.
  • the steel sheet of the present invention further contains the following elements as necessary.
  • Ni, Cu, Cr, and Mo are elements that contribute to high strength by increasing the hardenability during hot stamping and making the main phase martensite. Since this effect becomes remarkable by containing 0.01% or more of one or more selected from the group consisting of Ni, Cu, Cr, and Mo, the content of these elements is Each is preferably 0.01%. If the content of each element exceeds a predetermined amount, the weldability, hot workability, etc. may deteriorate, or the strength of the steel sheet for hot stamping may be too high, resulting in production trouble.
  • the upper limit of the element content is preferably 2.00%.
  • Nb, V, and W are elements that reinforce fine grains by suppressing the growth of austenite during hot stamping and contribute to an increase in strength and an improvement in toughness. From this, you may contain 1 type, or 2 or more types chosen from the group which consists of these elements. Since this effect becomes remarkable when each element contains 0.005% or more, it is preferable that these elements contain 0.005% or more. If these elements are contained in excess of 0.100%, Nb, V, and W carbides are formed, and the amount of C that contributes to the strengthening of martensite is reduced, causing a decrease in strength. It is not preferable. Preferably, it is in the range of 0.005% to 0.090%, respectively.
  • Total of one or more selected from the group consisting of REM, Ca, Ce, and Mg 0.0003% to 0.0300%
  • a total of 0.0003% to 0.0300% of one or more selected from the group consisting of REM, Ca, Ce, and Mg may be contained.
  • REM, Ca, Ce, and Mg are elements that improve the strength and contribute to the improvement of the material. If the total of one or more selected from the group consisting of REM, Ca, Ce, and Mg is less than 0.0003%, a sufficient effect cannot be obtained, so the lower limit of the total is 0.0003%. It is preferable to do.
  • REM is an abbreviation for Rare Earth Metal and refers to an element belonging to the lanthanoid series.
  • REM is often added by misch metal, and may contain a lanthanoid series element in combination with Ce in addition to Ce.
  • the present invention even if a lanthanoid series element other than La and Ce is included as an unavoidable impurity, the effects of the present invention are exhibited, and even if other elements such as metals are contained as impurities, the present invention The effect of.
  • the features of the microstructure of the hot stamping steel plate and hot stamping molded body of the present invention will be described. If the chemical composition, the surface roughness of the steel sheet, and the amount of oil coating satisfy the scope of the present invention, the pickled hot-rolled steel sheet, the cold-rolled steel sheet obtained by cold-rolling the hot-rolled steel sheet, or after cold-rolling The effect of the present invention can be exhibited with any of the cold-rolled steel sheets that have been annealed.
  • the microstructure is not particularly limited, and the performance as a steel sheet for hot stamping having excellent scale adhesion which is an effect of the present invention is as follows. Demonstrated. However, when performing mechanical cutting and cold punching of a steel plate prior to hot stamping, the strength of the steel plate should be as low as possible in order to reduce wear of the die, cutting machine blade, or punching die. Is preferred. From this, it is preferable that the microstructure of the steel sheet for hot stamping is a ferrite and pearlite structure, or a structure obtained by tempering a bainite structure and martensite.
  • the microstructure of the molded body is preferably martensite as the main phase.
  • the volume ratio of martensite as the main phase is 60% or more.
  • the martensite may be tempered martensite by tempering after hot stamping. As a structure other than martensite, bainite, ferrite, pearlite, cementite, and retained austenite may be included. Even if the martensite volume fraction is less than 60%, the excellent scale adhesion of the present invention can be ensured.
  • the following methods are used to identify the microstructure (tempered martensite, martensite, bainite, ferrite, pearlite, retained austenite, and remaining structure) constituting the steel sheet structure, confirm the existing position, and measure the area ratio.
  • a scanning electron microscope SEM: Scanning Electron Microscope
  • SEM Scanning Electron Microscope
  • TEM transmission electron microscope
  • the inventors have collected a sample with a cross section of the plate thickness parallel to the rolling direction of the steel plate as an observation surface, polished the observation surface, etched by nital, and 1/8 to about 1/4 of the plate thickness.
  • the area of 3/8 thickness was observed with a field emission scanning electron microscope (FE-SEM: Field ⁇ Emission Electron Microscope), and the area fraction was measured.
  • the volume fraction of retained austenite was measured by performing X-ray diffraction using a plane parallel to the plate surface of the base steel sheet and a thickness of 1/4 as an observation surface, and measuring the volume fraction.
  • a slab having the same component composition as that of the steel plate described above is cast.
  • a continuously cast slab or a thin slab caster can be used.
  • the steel sheet manufacturing method of the present invention is suitable for a process such as continuous casting-direct rolling (CC-DR) in which hot rolling is performed immediately after casting.
  • CC-DR continuous casting-direct rolling
  • Slab heating temperature is preferably 1100 ° C. or higher. Since the slab heating temperature in the temperature range below 1100 ° C. causes a decrease in the finish rolling temperature, the strength during finish rolling tends to be high. As a result, rolling may be difficult, or the shape of the steel sheet after rolling may be deteriorated, so the slab heating temperature is preferably 1100 ° C. or higher.
  • the finish rolling temperature is preferably not less than the Ar3 transformation point. If the finish rolling temperature is lower than the Ar3 transformation point, the rolling load becomes high, and rolling may become difficult or the shape of the steel sheet after rolling may be deteriorated. Therefore, the lower limit of the finish rolling temperature is Ar3 transformation. It is preferable to make it a point.
  • the upper limit of the finish rolling temperature is not particularly required, but if the finish rolling temperature is excessively increased, the slab heating temperature must be excessively increased in order to secure the temperature. Therefore, the upper limit of the finish rolling temperature is 1100. ° C is preferred.
  • the winding temperature is preferably 700 ° C. or lower.
  • the coiling temperature exceeds 700 ° C., the thickness of the oxide formed on the steel sheet surface is excessively increased and the pickling property is deteriorated, which is not preferable.
  • the rolled hot-rolled steel sheet is softened by heating in a box-type annealing furnace or continuous annealing equipment, it may be wound at a low temperature of less than 400 ° C.
  • rough rolling sheets may be joined to each other during hot rolling to continuously perform finish rolling. Moreover, you may wind up a rough rolling board once.
  • the hot-rolled steel sheet thus manufactured is subjected to pickling for 30 seconds or more in an aqueous solution having a temperature of 80 ° C. or higher and lower than 100 ° C. and containing an inhibitor and containing 3% by mass to 20% by mass of acid.
  • pickling under these conditions is extremely important.
  • pickling under the above conditions is necessary.
  • the acid is generally an aqueous solution such as hydrochloric acid or sulfuric acid, and may be aqua regia.
  • the reason why the temperature of the aqueous solution was set to 80 ° C. or more and less than 100 ° C. is that when the temperature is less than 80 ° C., the reaction rate is slow, and it takes a long time to bring the surface roughness of the hot-rolled steel sheet to an appropriate range. On the other hand, heating at a temperature of 100 ° C. or higher is dangerous and unpreferable because the solution is boiled and scattered although there is no problem with the pickling reaction.
  • the reason that the acid concentration is set to 3% by mass to 20% by mass is to control the surface roughness Rz of the hot-rolled steel sheet within an appropriate range.
  • the acid concentration is less than 3% by mass, it takes a long time to control surface unevenness by pickling.
  • the acid concentration exceeds 20% by mass the pickling tank is greatly damaged, and equipment management becomes difficult, which is not preferable.
  • a preferable range of the acid concentration is in the range of 5 to 15% by mass.
  • the reason for the pickling time being 30 s or more is to stably impart predetermined irregularities (irregularities of Rz> 2.5 ⁇ m or more) to the steel sheet surface by pickling.
  • predetermined irregularities irregularities of Rz> 2.5 ⁇ m or more
  • hot rolling is performed.
  • the surface roughness Rz of the steel sheet can be within the scope of the present invention.
  • pickling may be carried out in a plurality of times.
  • hydrochloric acid containing an inhibitor was used.
  • other acids such as hydrochloric acid, sulfuric acid, nitric acid without using an inhibitor may be used as long as the surface roughness Rz can be controlled by pickling. Even if these are composites, the effects of the present invention can be obtained.
  • temper rolling may be performed on the hot-rolled steel sheet after pickling.
  • the roll roughness Rz for cold rolling is preferably cold-pressed in the range of 1.0 ⁇ m to 20.0 ⁇ m, and the cold rolling roll includes a temper rolling roll.
  • the hot-rolled steel sheet pickled under the above conditions may be cold-rolled at a reduction rate of 30% to 80% and passed through a continuous annealing facility. If the rolling reduction is less than 30%, it becomes difficult to keep the shape of the steel plate flat, and the ductility of the final product is deteriorated. Therefore, the lower limit of the rolling reduction is preferably 30%. On the other hand, if the rolling reduction exceeds 80%, the rolling load becomes too large and cold rolling becomes difficult, so the upper limit of the rolling reduction is preferably 80%. More preferably, the rolling reduction is 40% to 70%. Note that even if the number of rolling passes and the rolling reduction for each pass are not particularly defined, the effect of the present invention is exhibited. Therefore, it is not necessary to define the number of rolling passes and the rolling reduction for each pass.
  • the cold-rolled steel sheet may be passed through a continuous annealing line. Since the purpose of this treatment is to soften a steel plate that has been strengthened by cold rolling, any conditions may be used as long as the steel plate softens. For example, if the annealing temperature is in the range of 550 ° C. to 750 ° C., the dislocations introduced during cold rolling are released by recovery, recrystallization, or phase transformation, so annealing can be performed in this temperature range. preferable.
  • the steel sheet for hot stamping excellent in scale adhesion of the present invention can be obtained even if annealing is performed in a box furnace.
  • oiling is performed.
  • electrostatic oiling, spraying, roll coater and the like are generally used, but the method is not limited as long as the oil amount in the range of 50 mg / m 2 to 1500 mg / m 2 can be secured.
  • a predetermined amount of oiling was carried out with an electrostatic oiling machine.
  • degreasing may be performed by applying an antirust agent in an amount larger than that.
  • the hot stamping conditions are not particularly limited, and it is possible to achieve both excellent scale adhesion and rust prevention, which are the effects of the present invention. For example, it is possible to achieve both the excellent performance of a tensile strength of 1180 MPa or more and the productivity by manufacturing by the following manufacturing method.
  • the heating rate is 5 ° C./second or more, and further preferably 10 ° C./second or more.
  • the increase in the heating rate is also effective for increasing the productivity.
  • the annealing temperature when performing hot stamping is preferably in the range of 800 ° C to 1100 ° C.
  • the annealing temperature at this time is less than 800 ° C.
  • the structure at the time of annealing becomes a ferrite and austenite structure, and this ferrite grows in the cooling process, the ferrite volume ratio exceeds 10%, and the tensile strength of the hot stamping body Is less than 1180 MPa.
  • the lower limit of the annealing temperature is preferably 800 ° C.
  • the annealing temperature exceeds 1100 ° C., not only the effect is saturated, but also the scale thickness is greatly increased, and there is a concern that the scale adhesiveness is lowered. Therefore, it is preferable to perform annealing at 1100 ° C. or lower. More preferably, the annealing temperature is in the range of 830 ° C to 1050 ° C.
  • the holding may be held in a temperature range of 800 ° C. to 1100 ° C. after heating.
  • the carbide contained in the steel plate can be dissolved, which contributes to an increase in strength of the steel plate and improvement in hardenability.
  • Holding includes residence in this temperature range, heat removal, and heat removal. Since the purpose is to dissolve the carbide, the object can be achieved by securing the residence time in this temperature range.
  • the holding time it is preferable to set the upper limit to 1000 s because the scale thickness becomes excessive and the scale adhesion deteriorates when the holding time is 1000 s or more.
  • 700 ° C. is the mold cooling start temperature
  • 800 ° C. to 700 ° C. being 5 ° C./second or more avoids ferrite transformation, bainite transformation, and pearlite transformation, and makes the structure a martensite main phase. Because.
  • the cooling rate is less than 5 ° C./second, these soft structures are formed, and it is difficult to secure a tensile strength of 1180 MPa or more.
  • the effect of the present invention is exhibited without any particular limitation on the upper limit of the cooling rate.
  • the reason why the temperature range for cooling at 5 ° C./second or more is set to 800 ° C. to 700 ° C. is that a structure that causes a decrease in strength such as ferrite may be formed in this temperature range.
  • the cooling at this time is not limited to continuous cooling, and the effect of the present invention is exhibited as long as the average cooling rate is 5 ° C./second or more even if holding and heating in this temperature range.
  • the effect of the present invention can be exhibited without any particular limitation on the cooling method. That is, the effect of the present invention can be exhibited by either cooling using a mold or mold cooling combined with water cooling.
  • the conditions in the examples are one example of conditions used for confirming the feasibility and effects of the present invention, and the present invention is based on this one example of conditions. It is not limited.
  • the present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
  • the finishing board thickness of the hot-rolled steel plate used for a hot stamp as a hot-rolled steel plate was 1.6 mm.
  • the thickness of the hot-rolled steel sheet used for cold rolling was set to 3.2 mm. Thereafter, pickling was performed under the conditions shown in Table 2, and the thickness was 50% (3.2 mm ⁇ 1.6 mm) when cold rolling was performed. Then, about some steel plates, it annealed with the continuous annealing equipment, and was set as the cold-rolled steel plate.
  • NOX-RUST503F Parker Kosan
  • NOX503F Parker Kosan
  • the steel sheet is cut into a predetermined size, then heated to 900 ° C. at 50 ° C./second, held at 900 ° C. for 10 seconds, then allowed to cool for 10 s, and 650 ° C. or higher. Quenching was performed with the above-mentioned hot shallow drawing die at a temperature of. The obtained hot stamping body was visually observed, and a steel plate without scale peeling was used as a steel plate excellent in scale adhesion.
  • a steel sheet that was kept at room temperature for 30 days and did not generate rust on the steel sheet surface was defined as a steel sheet with excellent rust prevention.
  • hot stamping was performed under the above conditions, and tensile properties were evaluated. The evaluation results are shown in Table 3.
  • the molded article of the present invention has a maximum tensile strength of 1180 MPa or more.
  • the composition analysis of the scale of the compact was carried out by X-ray diffraction after cutting a plate from the bottom of the cylindrical portion of the shallow drawn specimen. From the peak intensity ratio of each oxide, the volume fraction of each Fe-based oxide was measured. Since the Si oxide was very thin and the volume fraction was less than 1%, quantitative evaluation by X-ray diffraction was difficult. However, it was confirmed by the line analysis of EPMA that it exists at the interface between the scale and the ground iron. The unevenness evaluation of the interface between the scale formed on the formed body and the ground iron was performed by embedding and polishing the steel sheet cut out from the above position, and then SEM observation was performed at 3000 times from a cross section perpendicular to the rolling direction. Each test piece was observed with 5 visual fields, and the number density of irregularities in the range of 0.2 ⁇ m to 1.0 ⁇ m per 100 ⁇ m length was measured.
  • Those satisfying the conditions of the present invention were able to achieve both excellent rust prevention and excellent scale adhesion. Those not satisfying the conditions of the invention were inferior in scale adhesion or inferior in corrosion resistance.
  • the present invention it is possible to provide a steel plate having excellent scale adhesion at the time of hot stamping, and to solve the problems of die wear during hot stamping, plating adhesion to the die, and indentation flaws associated therewith. Therefore, it is possible to bring about a significant improvement in productivity and industrially great value.

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PCT/JP2016/060145 2015-03-31 2016-03-29 ホットスタンプ用鋼板およびその製造方法、並びにホットスタンプ成形体 WO2016158961A1 (ja)

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CN201680017529.1A CN107427889B (zh) 2015-03-31 2016-03-29 热冲压用钢板及其制造方法、以及热冲压成型体
US15/559,731 US20180044754A1 (en) 2015-03-31 2016-03-29 Steel sheet for hot stamping and method for producing steel sheet for hot stamping, and hot stamp formed body
CA2979978A CA2979978A1 (en) 2015-03-31 2016-03-29 Steel sheet for hot stamping and method for producing steel sheet for hot stamping, and hot stamp formed body
BR112017020165-8A BR112017020165A2 (pt) 2015-03-31 2016-03-29 chapa de aço para estampagem a quente e método para produção de chapa de aço para estampagem a quente e corpo formado por estampagem a quente
ES16772842T ES2781465T3 (es) 2015-03-31 2016-03-29 Lámina de acero para estampado en caliente, método para su fabricación, y cuerpo moldeado por estampado en caliente
RU2017135379A RU2683397C1 (ru) 2015-03-31 2016-03-29 Стальной лист для горячей штамповки, способ производства стального листа для горячей штамповки, а также формируемое горячей штамповкой тело
MX2017012377A MX2017012377A (es) 2015-03-31 2016-03-29 Lamina de acero para estampado en caliente, metodo para producir lamina de acero para estampado en caliente, y articulo moldeado por estampado en caliente.
EP16772842.7A EP3278895B1 (en) 2015-03-31 2016-03-29 Steel sheet for hot stamping, method for manufacturing same, and hot stamp molded article
JP2017510030A JP6515356B2 (ja) 2015-03-31 2016-03-29 ホットスタンプ用鋼板およびその製造方法、並びにホットスタンプ成形体
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