EP3278895A1 - Steel sheet for hot stamping, method for manufacturing same, and hot stamp molded article - Google Patents

Steel sheet for hot stamping, method for manufacturing same, and hot stamp molded article Download PDF

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Publication number
EP3278895A1
EP3278895A1 EP16772842.7A EP16772842A EP3278895A1 EP 3278895 A1 EP3278895 A1 EP 3278895A1 EP 16772842 A EP16772842 A EP 16772842A EP 3278895 A1 EP3278895 A1 EP 3278895A1
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EP
European Patent Office
Prior art keywords
steel sheet
hot
mass
hot stamping
steel
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EP16772842.7A
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German (de)
French (fr)
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EP3278895B1 (en
EP3278895A4 (en
Inventor
Masafumi Azuma
Yoshihiro SUWA
Yusuke Kondo
Koichi Sato
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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 and a method for producing the steel sheet for hot stamping, and a hot stamp formed body that is a formed body of the steel sheet for hot stamping.
  • Weight reduction of the members such as door guard bars and side members of automobiles are being studied to cope with the recent trend of improvement in fuel efficiency, and in terms of a material, increase in strength of a steel sheet is promoted from the viewpoint of strength and crash safety that should be ensured even when the thickness is reduced.
  • strength means both tensile strength and yield strength.
  • formability of a material deteriorates as the strength increases, and therefore in order to realize reduction in weight of the above described members, it is necessary to produce a steel sheet that satisfies both formability and high strength.
  • TRIP Treatment Induced Plasticity
  • Patent Literature 1 and Patent Literature 2 As a method for obtaining high formability simultaneously with high strength, there are TRIP (TRansformation Induced Plasticity) steels taking advantage of martensitic transformation of retained austenite that are described in Patent Literature 1 and Patent Literature 2, and application of TRIP steels has been expanding in recent years.
  • TRIP steels In the steel, however, although deep drawability and elongation are improved at the time of forming, due to a high steel sheet strength, it has a problem of low shape fixability of a member after press forming.
  • Patent Literature 3 In order to form a high strength steel sheet, which is inferior in formability, with good shape fixability, there is a method called hot press that is described in Patent Literature 3 and Patent Literature 4.
  • the method performs forming at a temperature of 200°C to about 500°C at which the steel sheet strength reduces.
  • the method has problems in that even when the forming temperature is increased, the steel sheet strength may still be high in some cases and thus forming is difficult, and in that the steel sheet strength after forming is reduced by heating, and thus predetermined strength cannot be obtained in some cases.
  • the steel sheet which is taken out is exposed to the atmosphere, and thus the technique has a problem of unavoidable formation of scale.
  • the method for electrically heating a steel sheet in the atmosphere has been developed. At the time of heating in the atmosphere, avoidance of oxidation of the steel sheet is difficult, and thus a problem of die wear due to loose scale at the time of hot stamping easily becomes evident. As a result, regular repair of the die is essential.
  • the present invention has an object to provide a steel sheet for hot stamping that is excellent in scale adhesion at the time of hot stamping, without an occurrence of adhesion of a molten metal to a die, a method for manufacturing the steel sheet for hot stamping, and a hot stamp formed body.
  • the present inventors have studied earnestly on methods to solve the above described problems.
  • 0.50 mass% to 3.00 mass% of Si is contained in the steel sheet
  • the amount of rust inhibiting oil that is applied to the steel sheet is set to be within a range of 50 mg/m 2 to 1500 mg/m 2
  • surface roughness of the steel sheet is set as Rz>2.5 ⁇ m.
  • an S content included in the rust inhibiting oil is preferably set at 5 mass% or less.
  • enclosures in the coating oil concentrate into an interface between a base iron and scale, and thereby deteriorate scale adhesion.
  • the present invention is made based on the above described knowledge, and the gist of the present invention is as follows.
  • the steel sheet for hot stamping excellent in scale adhesion at the time of hot stamping, in which adhesion of a molten metal to the die does not occur the method for producing the steel sheet for hot stamping and the hot stamp formed body can be provided.
  • a steel sheet for hot stamping of the present invention contains from 0.5 mass% to 3.0 mass% of Si in the steel sheet, an amount of rust inhibiting oil applied to the steel sheet is in a range of 50 mg/m 2 to 1500 mg/m 2 , and surface roughness of the steel sheet is Rz>2.5 ⁇ m. It is preferable that an S content contained in the rust inhibiting oil be 5 mass% or less.
  • the present inventors have investigated the surface properties of the steel sheets, and influences of various kinds of treatment. As a result, the present inventors have found that although the steel sheets after degreasing show excellent scale adhesion, scale adhesion significantly deteriorates after rust inhibiting oil is applied.
  • the present inventors investigated the relationship between scale adhesion and rust inhibiting oil in more detail it has been found that when an amount of S contained as impurities in the rust inhibiting oil increases, scale tends to detach easily. It is conceivable that S in the rust inhibiting oil has an influence on scale adhesion, although the detailed reason is unclear.
  • rust inhibiting oil such as mineral oil
  • a pickled hot-rolled steel sheet for hot stamping and a cold-rolled steel sheet for hot stamping after cold rolling or annealing in order to restrain rust from occurring in the period from production to use.
  • a steel sheet after pickling has been generally coated with oil of more than 1500 mg/m 2 , assuming that the period from delivery to a customer to use is long.
  • the effect is exhibited by setting the coating oil amount at 50 mg/m 2 to 1500 mg/m 2 .
  • a lower limit of the coating oil amount is set at 50 mg/m 2 , because it is difficult to ensure excellent rust inhibition properties with the coating oil amount less than the coating oil amount of 50 mg/m 2 .
  • the lower limit of the coating oil amount is preferably 100 mg/m 2 or more, and more preferably 200 mg/m 2 or more.
  • An upper limit is set at 1500 mg/m 2 to obtain an effect of excellent scale adhesion.
  • the upper limit of the coating oil amount is set at 1500 mg/m 2 because when the coating oil amount exceeds 1500 mg/m 2 , scale adhesion deteriorates.
  • the upper limit is preferably 1000 mg/m 2 , is more preferably 900 mg/m 2 , and far more preferably is 800 mg/m 2 . Further, coated oil on the steel sheet surface burns at the time of heating, and therefore becomes the cause of generating soot. From this, a smaller coating oil amount is more preferable.
  • Scale adhesion illustrated in Fig. 1 was evaluated by a hot shallow drawing test in a cylindrical die of ⁇ 70 mm and a depth of 20 mm. After a steel sheet was heated to a temperature range of 800°C to 1100°C at 50°C/s in an electrical heater, and was retained for 0 seconds to 120 seconds, energization was stopped, the steel sheet was cooled to 650°C by standing to cool, and hot shallow drawing was performed in the above described die.
  • specimens after forming were visually observed, and specimens in which an area where scale was detached accounted for 5% or less were determined as having good (circle) scale adhesion, specimens in which the area where scale was detached accounted for 5 to 15% were determined as poor (triangle), and specimens in which the area where scale was detached accounted for more than 15% were determined as very poor (X).
  • the specimens in which the area where scale was detached accounted for 5% or less were determined as within the range of the present invention.
  • scale adhesion without particularly limiting the heating method.
  • conditions of any of a heating furnace, far-infrared rays, near-infrared rays and electrical heating may be adopted.
  • more excellent scale adhesion can be obtained by thinning scale by controlling the atmosphere in the heating furnace and restraining oxidation of the steel sheet.
  • a shallow drawing test temperature may be in any temperature region as long as a steel sheet can be processed, but in general, a steel sheet for hot stamping has high strength and excellent shape fixability by processing in an austenite region and subsequent die hardening. From this, characteristics evaluation was carried out by hot shallow drawing at 650°C exceeding Ar3.
  • oil coating method electrostatic oil coating, spray, a roll coater and the like are generally used, but the oil coating method is not limited as long as the coating oil amount can be ensured.
  • NOX-RUST530F made by PARKER INDUSTRIES, INC.
  • the kind of oil is not limited.
  • the coating oil amount may be measured by any method as long as the coating oil amount can be measured, the present inventors measured the coating oil amount by the following method.
  • the steel sheet coated with rust inhibiting oil was cut into 150 mm square first, and thereafter, a tape was applied so that a 100 mm by 100 mm region is exposed. Subsequently, the weights of the coating oil and the steel sheet to which seal was carried out (including the weight of the tape) were measured in advance. Subsequently, degreasing was performed by wiping off the rust inhibiting oil on the steel sheet surface with cloth containing acetone, the weight of the degreased steel sheet was measured, the weights before and after degreasing were compared, and thereby the coating oil amount per unit area was calculated. Measurement was carried out at three spots in each of the steel sheets, and an average value of the attached amounts was determined as a coating oil attaching amount of each of the steel sheets.
  • the present inventors investigated the relationship between the S content in the coating oil and a scale detached area ratio as illustrated in Fig. 2 , the present inventors have found that as the S content in the coating oil becomes smaller, the scale adhesion increases, and especially when the S content in the coating oil is 5 mass% or less, the scale detached area becomes substantially 0%. It is conceivable that while the oil contained in the rust inhibiting oil is burned and eliminated during heating, S contained as an impurity remains on the steel sheet surface to concentrate into scale, and thereby deteriorates scale adhesion, although detailed mechanism is unclear. Hence, it is preferable to reduce the content of S contained in the rust inhibiting oil.
  • the S content is preferably 4 mass% or less, and is more preferably 3 mass% or less.
  • the surface roughness of the steel sheet will be described next.
  • the surface roughness of the steel sheet needs to satisfy Rz>2.5 ⁇ m.
  • a result obtained by investigating a relationship between the surface roughness Rz of the steel sheet and scale adhesion is as illustrated in Fig. 1 described above.
  • the effect is generally referred to as an anchor effect.
  • scale that is generated at the time of heating in the present steel sheet is thin.
  • the surface roughness of the steel sheet before hot stamping needs to satisfy Rz>2.5 ⁇ m.
  • Rz ⁇ 2.5 ⁇ m the surface roughness of the steel sheet is small, and the anchor effect is insufficient, and thus excellent scale adhesion at the time of hot stamping cannot be ensured.
  • the effect of the excellent scale adhesion of the present invention can be obtained without particularly providing the upper limit, if scale adhesion is excessively increased, it becomes difficult to remove scale in a downstream process such as shot blast, for example.
  • Rz ⁇ 7.0 ⁇ m It is more preferable to set Rz ⁇ 7.0 ⁇ m. However, even if Rz ⁇ 8.0 ⁇ m is set, it is possible to ensure excellent scale adhesion that is the effect of the present invention. Note that in the steel sheet in which an Si content is less than 0.50 mass%, even if the surface roughness of Rz>2.5 ⁇ m is set, thick Fe scale is formed at the time of heating, and thus even when the irregularities are on the steel sheet surface, the interface between the base iron and the scale becomes flat by excessive oxidation. As a result, the irregularities in the interface between the scale and the base iron are eliminated, and the effect of the excellent scale adhesion that is the effect of the present invention is not exhibited.
  • a contact surface roughness measuring instrument SURFCOM2000DX/SD3 made by TOKYO SEIMITSU CO., LTD
  • the steel sheet for hot stamping of the present invention ensures scale adhesion by control of the irregularities in the interface between the scale and the base iron.
  • the scale can be scale mainly composed of an Si oxide, Fe 3 O 4 , Fe 2 O 3 and FeO.
  • An Si oxide exists in the interface between base iron and iron scale (FeO, Fe 2 O 3 , Fe 2 O 3 ), and thereby controls a thickness of the iron scale.
  • the scale needs to contain an Si oxide. Since the main object is to control the thickness of the iron oxide, even if the Si oxide is very thin, it is sufficient if the Si oxide exists, and even with 1 nm, the Si oxide exhibits the effect.
  • Composition analysis of the scale of the formed body was carried out by X-ray diffraction by cutting out the sheet from a bottom of the cylindrical portion of a shallow drawn specimen piece. From a peak intensity ratio of the respective oxides, volume ratios of the respective Fe oxides were measured. The Si oxide existed very thinly, and the volume ratio was less than 1%, and thus quantitative evaluation in X-ray diffraction was difficult. However, it is possible to confirm that an Si oxide exists in the interface between the scale and the base iron by line analysis of EPMA (Electron Probe Micro Analyzer).
  • EPMA Electro Probe Micro Analyzer
  • the thickness of the scale is preferably 10 ⁇ m or less.
  • the thickness of the scale is 10 ⁇ m or less.
  • the thickness of the scale is more preferably 7 ⁇ m or less, and is more preferably 5 ⁇ m or less.
  • the thickness of the scale is achieved by controlling the coating oil amount within the predetermined range simultaneously with controlling the Si content of the steel sheet within a predetermined range.
  • Fig. 5 illustrates a relationship between the coating oil amount and the scale thickness.
  • Fig. 6A shows a photograph of an interface between a base iron and scale of a formed body excellent in scale adhesion
  • Fig. 6B shows a photograph of an interface between a base iron and scale inferior in scale adhesion. Since the irregularities contribute to enhancement in scale adhesion at the time of hot stamping, and thus excellent scale adhesion can be ensured by controlling the irregularities within the above described range. Irregularities of less than 0.2 ⁇ m provide an insufficient anchor effect, and provide inferior scale adhesion.
  • irregularities of 8.0 ⁇ m or more scale adhesion is so strong that scale is difficult to remove in the subsequent scale removal process, for example, by shot blast or wet blast, and therefore it is preferable to make the irregularities in the interface between scale and the base iron 8.0 ⁇ m or less.
  • the irregularities are more preferably 6.0 ⁇ m or less, and more preferably 4.0 ⁇ m or less. Note that even if the irregularities exceed 8.0 ⁇ m, excellent scale adhesiveness that is the effect of the present invention can be ensured.
  • the number of irregularities of 0.2 ⁇ m to 8.0 ⁇ m per 100 ⁇ m is less than three, an improvement effect of scale adhesion is not sufficient, and thus the number of irregularities per 100 ⁇ m is set at three or more. It is possible to ensure excellent scale adhesion which is the effect of the present invention without particularly setting an upper limit of the number of irregularities per 100 ⁇ m.
  • the irregularities of the formed body are correlated with the surface roughness Rz of the steel sheet as illustrated in Fig. 7 , and are controllable by setting the steel sheet surface roughness as Rz>2.5 ⁇ m.
  • C represents an element that is contained to enhance the strength of the steel sheet. If a C content is less than 0.100%, tensile strength of 1180 MPa or more cannot be ensured, and a formed body with high strength which is the object of hot stamp cannot be ensured. When the C content exceeds 0.600%, weldability and processibility become insufficient, and thus the C content is set at 0.100% to 0.600%.
  • the C content is preferably 0.100% to 0.550%, and is more preferably 0.150% to 0.500%. However, if the strength of the formed body is not required, excellent scale adhesion can be ensured even if the C content is less than 0.150%.
  • Si enhances scale adhesion by controlling the scale composition at the time of hot stamping, and therefore Si is an essential element. If the Si content is less than 0.50%, the thickness of Fe scale cannot be controlled, and excellent scale adhesion cannot be ensured. Consequently, it is necessary to set the Si content at 0.50% or more. Further, when application to a member which is difficult to form at the time of hot stamping is considered, it is preferable to increase the Si content. Accordingly, the Si content is preferably 0.70% or more, and is more preferably 0.90% or more. Meanwhile, Si increases an Ae3 point, and the heating temperature necessary to make martensite a main phase, and thus if the Si is excessively contained, productivity and economic efficiency are reduced. Hence, an upper limit of the Si content is set as 3.00%. The upper limit of the Si content is preferably 2.5%, and the upper limit is more preferably 2.0%. However, it is possible to ensure excellent scale adhesion excepting productivity and economic efficiency.
  • Mn delays ferrite transformation in a cooling process at the time of hot stamping, and makes a hot stamp formed body into a structure having a martensite main phase, and thus it is necessary to contain 1.20% or more of Mn. If the Mn content is less than 1.20%, martensite cannot be made a main phase, and it is difficult to ensure high strength which is an object of the hot stamp formed body, and thus a lower limit of the Mn content is set as 1.20%. However, if the strength of the formed body is not required, excellent scale adhesion can be ensured even if the Mn content is less than 1.20%.
  • the Mn content is preferably within a range of 1.50% to 3.50%, and is more preferably within a range of 2.00% to 3.00%.
  • Ti is an element that combines with N to form TiN, and thereby restrains B from being a nitride to enhance hardenability. The effect becomes remarkable when a Ti content is 0.005% or more, and thus the Ti content is set as 0.005% or more. However, when the Ti content exceeds 0.100%, a Ti carbide is formed, an amount of C that contributes to strengthening martensite is reduced, and reduction in strength is caused, and thus an upper limit of the Ti content is set as 0.100%.
  • the C content is preferably within a range of 0.005% to 0.080%, and is more preferably within a range of 0.005% to 0.060%.
  • B enhances hardenability at the time of hot stamping, and contributes to making a main phase of martensite.
  • the effect is remarkable when a B content is 0.0005% or more, and thus it is necessary to set the B content at 0.0005% or more.
  • the B content exceeds 0.0100%, the effect is saturated, an iron boride is precipitated, and the effect of hardenability of B is lost, and thus an upper limit of the B content is set at 0.0100%.
  • the B content is preferably within a range of 0.0005% to 0.0080%, and is more preferably within a range of 0.0005% to 0.0050%.
  • an upper limit of a P content is set at 0.100%.
  • a more preferable upper limit is 0.050%.
  • an upper limit of an S content is set at 0.0100%.
  • a lower limit of the S content is set at 0.0001% because it is economically disadvantageous from the viewpoint of productivity and cost of dephosphorization.
  • the S content is preferably within a range of 0.0001% to 0.0070%, and is more preferably within a range of 0.0003% to 0.0050%.
  • Al acts as a deoxidizer, and thus an Al content is set as 0.005% or more.
  • an Al content is set as 0.005% or more.
  • the Al content is less than 0.005%, a sufficient deoxidization effect cannot be obtained, and a large amount of enclosure (oxide) exist in the steel sheet. These enclosures become starting points of destruction at the time of hot stamping, and the causes of breakage, and therefore are not preferable.
  • the effect becomes remarkable when the Al content reaches 0.005% or more, and thus it is necessary to set the Al content at 0.005% or more.
  • the Al content exceeds 1.000%, the Ac3 point is increased and a heating temperature at the time of hot stamping is increased.
  • hot stamp is a technique of obtaining a formed body with high strength having a complicated shape by heating a steel sheet to an austenite single phase region, and subjecting the steel sheet to hot die press excellent in formability, and rapidly cooling by using a die.
  • the Ac3 point is significantly increased, increase in the heating temperature required for austenite single phase region heating is caused, and productivity is reduced. Consequently, it is necessary to set an upper limit of the Al content at 1.000%.
  • the Al content is preferably within a range of 0.005% to 0.500%, and is more preferably within a range of 0.005% to 0.300%.
  • N is an element that forms coarse nitrides and deteriorates bendability and hole-expandability.
  • an N content exceeds 0.0100%, bendability and hole-expandability are significantly deteriorated, and thus an upper limit of the N content is set at 0.0100%.
  • the N content is preferably 0.0070 or less, and is more preferably 0.0050% or less.
  • the N content is more preferably 0.0005% or more.
  • O forms an oxide and exists as an enclosure.
  • the steel sheet of the present invention further contains the following elements in accordance with necessity.
  • Ni, Cu, Cr and Mo are elements that contribute to increase in strength by enhancing hardenability at the time of hot stamping, and making a main phase of martensite.
  • the effect becomes remarkable by containing 0.01% or more of each one kind or two or more kinds selected from a group consisting of Ni, Cu, Cr and Mo, and thus contents of the elements are preferably 0.01% respectively.
  • contents of the elements are preferably set at 2.00%.
  • Nb, V and W are elements that strengthen fine grains by inhibiting growth of austenite at the time of hot stamping, and contribute to increase in strength and enhancement in tenacity.
  • one kind or two or more kinds selected from a group consisting of these elements may be contained.
  • the effect becomes more remarkable when 0.005% or more of each of the elements are contained, and thus it is preferable that 0.005% or more of each of the elements be contained.
  • Nb, V and W carbides are formed, an amount of C that contributes to strengthening martensite is reduced, and reduction in strength is caused.
  • Each of the elements is preferably in a range of 0.005% to 0.090%.
  • 0.0003% to 0.0300% of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg may be further contained in total.
  • REM, Ca, Ce and Mg are elements that enhance strength and contribute to improvement of the material.
  • the total of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg is less than 0.0003%, a sufficient effect cannot be obtained, and thus it is preferable to set a lower limit of the total at 0.0003%.
  • the total of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg exceeds 0.0300%, castability and hot workability are likely to be deteriorated, and thus it is preferable to set an upper limit of the total at 0.0300%.
  • REM is an abbreviation of Rare Earth Metal, and refers to an element belonging to a lanthanoid system. In the present invention, REM is often added in misch metal, and besides Ce, elements of a lanthanoid system are sometimes contained in combination.
  • the effect of the present invention becomes apparent even when elements of a lanthanoid system other than La and Ce are contained as unavoidable impurities, and the effect of the present invention becomes apparent even when the other elements such as metals are contained as impurities.
  • the effect of the present invention can be exhibited by any of a pickled hot-rolled steel sheet, a cold-rolled steel sheet obtained by cold-rolling a hot-rolled steel sheet, or a cold-rolled steel sheet to which annealing is applied after cold rolling.
  • steel sheets are heated to an austenite region exceeding 800°C at the time of hot stamping, and therefore exhibit performance as steel sheets for hot stamping having excellent scale adhesion that is the effect of the present invention without particularly limiting the microstructure.
  • the strength of the steel sheets is preferably as low as possible in order to reduce wear and tear of dies, cutting edges of cutters, or punching dies. Consequently, the microstructure of the steel sheet for hot stamping is preferably ferrite and pearlite structures, or a bainite structure and a structure obtained by tempering martensite.
  • the microstructure of the formed body preferably has a martensite main phase.
  • a volume ratio of martensite that is a main phase is preferably made 60% or more. Martensite may be subjected to tempering after hot stamping, and made tempered martensite. As the structure other than martensite, bainite, ferrite, pearlite, cementite and retained austenite may be contained. Further, even if the martensite volume rate is less than 60%, it is possible to ensure the excellent scale adhesion of the present invention.
  • the following methods are used in identification of the microstructures (tempered martensite, martensite, bainite, ferrite, pearlite, retained austenite and a remaining structure) composing the steel sheet structure, confirmation of existence positions, and measurement of area ratios.
  • the present inventors determined the sheet thickness section parallel with the rolling direction of the steel sheet as an observation surface, extracted a specimen, polished the observation surface, performed nital etching, observed a range of thickness of 1/8 to 3/8 with 1/4 of the sheet thickness as a center with a field emission scanning electron microscope (FE-SEM: Field Emission Scanning Electron Microscope), measured an area fraction, and the area fraction was taken as a volume fraction.
  • FE-SEM Field Emission Scanning Electron Microscope
  • a slab having the same component composition as the component composition of the aforementioned steel sheet is cast first.
  • a continuously cast slab the slab produced by a thin slab caster or the like can be used.
  • the method for manufacturing the steel sheet of the present invention is adapted to a process like continuous casting-direct rolling (CC-DR) that performs hot rolling immediately after casting.
  • the slab heating temperature is preferably set at 1100°C or higher.
  • the slab heating temperature in a temperature region of lower than 1100°C causes reduction in the finishing rolling temperature, and thus strength at the time of finishing rolling tends to be high. As a result, there is the possibility that rolling becomes difficult, a poor shape of the steel sheet after rolling is caused, and thus the slab heating temperature is preferably set at 1100°C or higher.
  • the finishing rolling temperature is preferably set at the Ar3 transformation point or higher.
  • a rolling load becomes high, and there is the possibility that rolling becomes difficult, and a poor shape of the steel sheet after rolling is caused, and thus a lower limit of the finishing rolling temperature is preferably set at the Ar3 transformation point.
  • An upper limit of the finishing rolling temperature does not have to be particularly set, but if the finishing rolling temperature is set to be excessively high, the slab heating temperature has to be made excessively high in order to ensure the temperature, and thus the upper limit of the finishing rolling temperature is preferably 1100°C.
  • the coiling temperature is preferably set at 700°C or lower.
  • the coiling temperature exceeds 700°C, the thickness of the oxides formed on the steel sheet surface is excessively increased, and the pickling property is deteriorated, and thus the coiling temperature higher than 700°C is not preferable.
  • a lower limit of the coiling temperature is preferably set at 400°C.
  • the coiling temperature is lower than 400°C, the strength of the hot-rolled steel sheet extremely increases, and a sheet fracture and a poor shape at the time of cold rolling are easily caused, and thus the lower limit of the coiling temperature is preferably set at 400°C.
  • the hot-rolled steel sheet which is coiled is intended to be softened by heating the coiled hot-rolled steel sheet in the box type annealing furnace or the continuous annealing facility, the steel sheet may be coiled at a low temperature of lower than 400°C. Note that at the time of hot-rolling, rough-rolled sheets may be bonded to one another and finishing rolling may be continuously performed. Further, the rough-rolled sheet may be coiled temporarily.
  • pickling is applied to the hot-rolled steel sheet which is produced in this way for 30 seconds or more in an aqueous solution with an temperature of 80°C to 100°C in which a concentration of acid is 3 mass% to 20 mass% and an inhibitor is included.
  • pickling under the present conditions is extremely important, and in order to control the surface roughness Rz of the steel sheet to more than 2.5 ⁇ m, pickling under the above described conditions is necessary.
  • an aqueous solution of a hydrochloric acid, a sulfuric acid or the like as an acid is generally used, and an aqua regia or the like may be used.
  • the temperature of the aqueous solution is set at 80°C to lower than 100°C, because with a temperature lower than 80°C, a reaction rate is low, and it takes a long time to bring the surface roughness of the hot-rolled steel sheet into a proper range. Meanwhile, heating at a temperature of 100°C or higher is dangerous and is not preferable because the solution boils and splashes although the reaction of pickling has no problem.
  • the reason why the concentration of the acid is set at 3 mass% to 20 mass% is to control the surface roughness Rz of the hot-rolled steel sheet within the proper range.
  • the concentration of the acid is less than 3 mass%, it takes a long time to control the irregularities on the surface by pickling.
  • the concentration of the acid exceeds 20 mass%, a pickling tank is damaged significantly and facility management becomes difficult, and thus it is not preferable.
  • a preferable range of the concentration of the acid is a range of 5 mass% to 15 mass%.
  • the reason why the pickling time period is set at 30 seconds or more is to stably give predetermined irregularities (irregularities of Rz>2.5 ⁇ m) to the steel sheet surface by pickling.
  • the pickling tank is divided into a plurality of tanks, if a pickling time period of some of the pickling tanks or a total pickling time period satisfies the above described conditions, the surface roughness Rz of the hot-rolled steel sheet can be brought into the range of the present invention, even if concentrations or temperatures of the individual pickling tanks differ from one another. Further, pickling may be carried out by being divided into a plurality of times.
  • hydrochloric acid including an inhibitor was used, but the effect of the present invention can be obtained by using another acid such as hydrochloric acid using no inhibitor, a sulfuric acid, and a nitric acid, or a composite of these acids, as long as the surface roughness Rz can be controlled by pickling.
  • the irregularities formed by pickling of the hot-rolled steel sheet also remain even after temper rolling, cold rolling or annealing is carried out, and thus it is extremely important to control the pickling conditions, and give irregularities to the sheet surface after pickling. Consequently, temper rolling may be carried out to the hot-rolled steel sheet after pickling.
  • cold rolling is preferably performed with roll roughness Rz for cold rolling within a range of 1.0 ⁇ m to 20.0 ⁇ m, and the cold rolling roll also includes temper rolling roll.
  • Cold rolling is applied to the hot-rolled steel sheet pickled under the conditions as above at a draft of 30% to 80%, and the steel sheet may be passed through a continuous annealing facility.
  • a draft is less than 30%, it becomes difficult to keep the shape of the steel sheet flat, and ductility of the finished product deteriorates, and thus a lower limit of the draft is preferably set at 30%.
  • a rolling load becomes excessively large, and cold rolling becomes difficult, and thus an upper limit of the draft is preferably set at 80%.
  • the draft is more preferably 40% to 70%. The effect of the present invention becomes apparent even without particularly specifying the number of times of rolling pass and the draft of each pass, and thus it is not necessary to specify the number of times of rolling pass, and the draft at each pass.
  • the cold-rolled steel sheet may be passed through the continuous annealing line.
  • An object of the treatment is to soften the steel sheet which is highly strengthened by cold-rolling, and thus any conditions may be adopted as long as the condition is such that the steel sheet is softened.
  • the annealing temperature is in a range of 550°C to 750°C, dislocation introduced at the time of cold rolling is released by recovery, recrystalization, or phase transformation, and thus annealing is preferably performed in this temperature region.
  • the steel sheet for hot stamping excellent in scale adhesion of the present invention can be obtained.
  • oil coating is carried out.
  • electrostatic oiling, spray, a roll coater and the like are generally used, and as long as a coating oil amount in a range of 50 mg/m 2 to 1500 mg/m 2 can be ensured, the method is not limited.
  • coating of a predetermined amount of oil was carried out by an electrostatic oiling machine. Further, as long as the coating oil amount in the range of 50 mg/m 2 to 1500 mg/m 2 can be ensured, a rust inhibitor in an amount equal to or larger than the coating oil amount may be applied, and degreasing may be performed.
  • the excellent scale adhesion that is the effect of the present invention and a rust inhibition property can be made compatible without particularly limiting the hot stamping conditions.
  • compatibility of excellent performance of the tensile strength of 1180 MPa or more and productivity is achieved.
  • heating is preferably performed to a temperature region of 800°C to 1100°C at a heating rate of 2°C/second or more.
  • the heating rate is preferably 5°C/second or more, and is more preferably 10°C/second or more. Further, increase of the heating rate is also effective for the purpose of enhancing productivity.
  • the annealing temperature at the time of performing hot stamping is preferably within the range of 800°C to 1100°C. By performing annealing in this temperature region, it is possible to make the structure into an austenite single phase structure, and the structure can be made into a structure having martensite as a main phase by cooling that is performed subsequently.
  • the annealing temperature at this time is lower than 800°C, the structure at the time of annealing is made into a ferrite and austenite structures, the ferrite grows in the cooling process, the ferrite volume ratio exceeds 10%, and the tensile strength of the hot stamp formed body becomes lower than 1180 MPa. Consequently, a lower limit of the annealing temperature is preferably set at 800°C.
  • the annealing temperature is more preferably in a range of 830°C to 1050°C.
  • retention After heating, retention may be performed in the temperature region of 800°C to 1100°C.
  • melting of carbides included in the steel sheet is possible, and contribution is made to increase in the strength of the steel sheet and enhancement in hardenability.
  • Retention includes residence, heating removal and cooling removal in the present temperature region. Since the object is to melt the carbides, the object is achieved as long as the residence time period in the present temperature region is ensured.
  • the limitation on the retention time period is not particularly provided, 1000 seconds is preferably set as an upper limit, because when the retention time period is 1000 seconds or more, the scale thickness becomes excessively large, and scale adhesion is deteriorated.
  • a temperature of 800°C to 700°C is preferably reduced at an average cooling rate of 5°C/second or more.
  • 700°C is a die cooling start temperature
  • the reason why the temperature of 800°C to 700°C is reduced at 5°C/second or more is to avoid ferrite transformation, bainite transformation and pearlite transformation, and make the structure into a martensite main phase.
  • the cooling rate is less than 5°C/second, these soft structures are formed, and it is difficult to ensure the tensile strength of 1180 MPa or more. Meanwhile, the effect of the present invention is exhibited without particularly setting the upper limit of the cooling rate.
  • the effect of the present invention can be exhibited without particularly limiting the cooling method. That is, the effect of the present invention can be exhibited by either one of cooling using a die or die cooling using water cooling in combination.
  • the finished sheet thickness of the hot-rolled steel sheet provided for hot stamping as the hot-rolled steel sheet was made 1.6 mm.
  • the sheet thickness of the hot-rolled steel sheet provided for cold rolling was made 3.2 mm.
  • pickling was carried out under the conditions in Table 2 thereafter, and cold rolling was performed, the sheet thickness was made 50% (3.2 mm ⁇ 1.6 mm).
  • annealing was performed for some of the steel sheets in a continuous annealing facility, and the steel sheets were made into cold-rolled steel sheets.
  • NOX-RUST503F made by PARKER INDUSTRIES, INC.
  • NOX503F made by PARKER INDUSTRIES, INC.
  • the steel sheets were cut into a predetermined size, after which, electrical heating was performed to 900°C at 50°C/second, retention for 10 seconds at 900°C was carried out, thereafter, standing to cool for 10 seconds was performed, and hardening was performed in the above described hot shallow drawing dies at a temperature of 650°C or higher. Visual observation of the obtained hot stamp formed bodies was performed, and the steel sheets without detachment of scale were determined as the steel sheets excellent in scale adhesion.
  • *2 means that Mn was excessively high, many fractures occurred in casting and hot rolling time, and no hot-rolled steel sheet was able to be produced.
  • *3 means that at the time of hot stemping, a feature with the enclosure as the starting point occurred, and the tenslie test was not be able to be carried out with the formed
  • the tensile test pieces which were in conformity with JIS Z 2201 were extracted, the tensile test was performed in conformity with JIS Z 2241, and the maximum tensile strength was measured.
  • the formed bodies having the maximum tensile strength of 1180 MPa or more were determined as the formed bodies of the present invention.
  • Composition analyses of the scales of the formed bodies were carried out by X-ray diffraction by cutting out sheets from the bottoms of the cylindrical portions of the shallow drawing test pieces. From the peak strength ratios of the respective oxides, the volume ratios of the respective Fe oxides were measured. The Si oxides were present very thinly and the volume ratio was less than 1%, and thus quantitative evaluation by X-ray diffraction was difficult. However, it could be confirmed that the Si oxides were present in the interface between the scale and the base iron by the line analysis of EPMA.
  • the formed bodies satisfying the conditions of the present invention were able to make excellent rust inhibition properties and excellent scale adhesion compatible.
  • the formed bodies that do not satisfy the conditions of the invention were inferior in scale adhesion, or inferior in corrosion resistance.
  • the steel sheet excellent in scale adhesion at the time of hot stamping can be provided, the problems of wear and tear of the die at the time of hot stamping, plating adhesion to the die, and indentation flaws accompanying it can be solved, and thus the present invention can bring about significant enhancement in productivity, and has an industrially large value.

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Abstract

A steel sheet for hot stamping includes a composition including at least, in mass%, C: 0.100% to 0.600%, Si: 0.50% to 3.00%, Mn: 1.20% to 4.00%, Ti: 0.005% to 0.100%, B: 0.0005% to 0.0100%, P: 0.100% or less, S: 0.0001% to 0.0100%, Al: 0.005% to 1.000%, and N: 0.0100% or less, with a balance of Fe and impurities, surface roughness of the steel sheet satisfies Rz>2.5 µm, and 50 mg/m2 to 1500 mg/m2 of coating oil is applied to a surface.

Description

    TECHNICAL FIELD
  • The present invention relates to a steel sheet for hot stamping excellent in scale adhesion at the time of hot stamping and a method for producing the steel sheet for hot stamping, and a hot stamp formed body that is a formed body of the steel sheet for hot stamping.
    • BACKGROUND ART
  • Weight reduction of the members such as door guard bars and side members of automobiles are being studied to cope with the recent trend of improvement in fuel efficiency, and in terms of a material, increase in strength of a steel sheet is promoted from the viewpoint of strength and crash safety that should be ensured even when the thickness is reduced. Hereinafter, strength means both tensile strength and yield strength. However, formability of a material deteriorates as the strength increases, and therefore in order to realize reduction in weight of the above described members, it is necessary to produce a steel sheet that satisfies both formability and high strength. As a method for obtaining high formability simultaneously with high strength, there are TRIP (TRansformation Induced Plasticity) steels taking advantage of martensitic transformation of retained austenite that are described in Patent Literature 1 and Patent Literature 2, and application of TRIP steels has been expanding in recent years. In the steel, however, although deep drawability and elongation are improved at the time of forming, due to a high steel sheet strength, it has a problem of low shape fixability of a member after press forming.
  • In order to form a high strength steel sheet, which is inferior in formability, with good shape fixability, there is a method called hot press that is described in Patent Literature 3 and Patent Literature 4. The method performs forming at a temperature of 200°C to about 500°C at which the steel sheet strength reduces. However, when forming of the high strength steel sheet of 780 MPa or more is considered, the method has problems in that even when the forming temperature is increased, the steel sheet strength may still be high in some cases and thus forming is difficult, and in that the steel sheet strength after forming is reduced by heating, and thus predetermined strength cannot be obtained in some cases.
  • As a method for solving the problems, there exists a method called hot stamping that cuts a soft steel sheet in a predetermined size, thereafter, heats the steel sheet to an austenite single phase region at 800°C or higher, thereafter performs press forming in the austenite single phase region as disclosed in Patent Literature 5, and thereafter performs hardening. As a result, it is possible to manufacture a member that has high strength of 980 MPa or more and is excellent in shape fixability.
  • However, in hot stamping, a steel sheet is inserted into a heating furnace, or is heated to a high temperature exceeding 800°C by electrical heating or far-infrared heating in the atmosphere, and thus hot stamping has a problem of scale generated on a steel sheet surface. A die may be worn out due to the generated scale released at the time of hot stamping, and therefore it is required that scale adhesion should be excellent at the time of hot stamping. As a technique that solves these problems, there is known a technique of restraining generation of scale by making an atmosphere in the heating furnace a non-oxidation atmosphere in Patent Literature 6, for example. However, it is necessary to implement atmosphere control in the heating furnace strictly, and thus facility cost increases, and productivity is reduced. Further, the steel sheet which is taken out is exposed to the atmosphere, and thus the technique has a problem of unavoidable formation of scale. In addition, in recent years, for the purpose of enhancing productivity of hot stamping, the method for electrically heating a steel sheet in the atmosphere has been developed. At the time of heating in the atmosphere, avoidance of oxidation of the steel sheet is difficult, and thus a problem of die wear due to loose scale at the time of hot stamping easily becomes evident. As a result, regular repair of the die is essential.
  • There is known a technique of restraining wear of a die caused by loose scale by using, in hot stamping, a steel sheet with zinc plating or Al plating applied to a steel sheet surface as the steel sheet that solves these problems. However, since zinc plating or Al plating are melted into a liquid phase at the time of heating, the technique has a problem of zinc or Al adhering to the inside of the heating furnace and the die at the time of conveyance of the steel sheet or the time of pressing. A deposit of adhering zinc or Al has a problem of causing indentation flaws of a hot stamp formed body, and adhering to the formed body to worsen the outer appearance. Consequently, it is necessary to repair the die regularly.
  • Consequently, it is required to develop a steel sheet for hot stamping in which scale does not detach at the time of hot stamping, and adhesion of a molten metal to a die does not occur.
    • CITATION LIST PATENT LITERATURES
    • Patent Literature 1: Japanese Laid-open Patent Publication No. 01-230715
    • Patent Literature 2: Japanese Laid-open Patent Publication No. 02-217425
    • Patent Literature 3: Japanese Laid-open Patent Publication No. 2002-143935
    • Patent Literature 4: Japanese Laid-open Patent Publication No. 2003-154413
    • Patent Literature 5: Japanese Laid-open Patent Publication No. 2002-18531
    • Patent Literature 6: Japanese Laid-open Patent Publication No. 2004-106034
    • Patent Literature 7: Japanese Laid-open Patent Publication No. 2002-18531
    • Patent Literature 8: Japanese Laid-open Patent Publication No. 2008-240046
    • Patent Literature 9: Japanese Laid-open Patent Publication No. 2010-174302
    • Patent literature 10: Japanese Laid-open Patent Publication No. 2008-214650
    SUMMARY OF THE INVENTION TECHNICAL PROBLEM
  • In the light of the aforementioned problems, the present invention has an object to provide a steel sheet for hot stamping that is excellent in scale adhesion at the time of hot stamping, without an occurrence of adhesion of a molten metal to a die, a method for manufacturing the steel sheet for hot stamping, and a hot stamp formed body.
    • SOLUTION TO PROBLEM
  • The present inventors have studied earnestly on methods to solve the above described problems. As a result, with the intention to improve scale adhesion of a steel sheet, 0.50 mass% to 3.00 mass% of Si is contained in the steel sheet, the amount of rust inhibiting oil that is applied to the steel sheet is set to be within a range of 50 mg/m2 to 1500 mg/m2, and surface roughness of the steel sheet is set as Rz>2.5 µm. Further, an S content included in the rust inhibiting oil is preferably set at 5 mass% or less. Thereby, it has been found that scale adhesion at the time of heating and at the time of hot stamping is improved. In general, enclosures in the coating oil concentrate into an interface between a base iron and scale, and thereby deteriorate scale adhesion. However, it has been found out that it is possible to ensure scale adhesion by using restriction on an enclosure amount, and an anchor effect using irregularities on the steel sheet surface in combination.
  • The present invention is made based on the above described knowledge, and the gist of the present invention is as follows.
    1. (1) A steel sheet for hot stamping including a composition containing,
      • in mass%,
      • C: 0.100% to 0.600%;
      • Si: 0.50% to 3.00%;
      • Mn: 1.20% to 4.00%;
      • Ti: 0.005% to 0.100%;
      • B: 0.0005% to 0.0100%;
      • P: 0.100% or less;
      • S: 0.0001% to 0.0100%;
      • Al: 0.005% to 1.000%;
      • N: 0.0100% or less;
      • Ni: 0% to 2.00%;
      • Cu: 0% to 2.00%;
      • Cr: 0% to 2.00%;
      • Mo: 0% to 2.00%;
      • Nb: 0% to 0.100%;
      • V: 0% to 0.100%;
      • W: 0% to 0.100%, and
      • a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
      • with a balance being Fe and impurities,
      • wherein surface roughness of the steel sheet satisfies Rz>2.5 µm, and coating oil in an amount of 50 mg/m2 to 1500 mg/m2 is applied onto a surface.
    2. (2) The steel sheet for hot stamping according to (1) described above,
      wherein an amount of S contained in the coating oil which is applied onto the steel sheet is 5% or less in mass%.
    3. (3) The steel sheet for hot stamping according to (1) or (2) described above,
      wherein the composition of the steel sheet contains, in mass%,
      one kind or two or more kinds selected from a group consisting of
      • 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%.
    4. (4) The steel sheet for hot stamping according to any one of (1) to (3) described above,
      wherein the composition of the steel sheet contains, in mass %,
      a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
    5. (5) A method for producing a steel sheet for hot stamping, including
      • a step of casting a slab containing,
      • in mass%,
      • C: 0.100% to 0.600%,
      • Si: 0.50% to 3.00%,
      • Mn: 1.20% to 4.00%,
      • Ti: 0.005% to 0.100%,
      • B: 0.0005% to 0.0100%,
      • P: 0.100% or less,
      • S: 0.0001% to 0.0100%,
      • Al: 0.005% to 1.000%,
      • N: 0.0100% or less,
      • Ni: 0% to 2.00%,
      • Cu: 0% to 2.00%,
      • Cr: 0% to 2.00%,
      • Mo: 0% to 2.00%,
      • Nb: 0% to 0.100%,
      • V: 0% to 0.100%,
      • W: 0% to 0.100%, and
      • a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
      • with a balance being Fe and impurities, and hot rolling the slab directly or by allowing the slab to cool and heating the slab to obtain a hot-rolled steel sheet,
      • a step of pickling the hot-rolled steel sheet for 30 seconds or more in an aqueous solution having a temperature of 80°C to lower than 100°C and including an inhibitor with a concentration of an acid being 3 mass% to 20 mass%, and
      • a step of applying a rust inhibiting oil to the steel sheet after carrying out the pickling,
      • wherein a rust inhibiting oil remaining amount on a steel sheet surface is limited to 50 mg/m2 to 1500 mg/m2.
    6. (6) The method for producing a steel sheet for hot stamping according to (5) described above, wherein the rust inhibiting oil is applied to the hot-rolled steel sheet which has been pickled.
    7. (7) The method for producing a steel sheet for hot stamping according to (5) described above, further including a step of cold rolling the hot-rolled steel sheet which has been pickled to obtain a cold-rolled steel sheet,
      wherein the rust inhibiting oil is applied to the cold-rolled steel sheet.
    8. (8) The method for producing a steel sheet for hot stamping according to (5) described above, further including a step of cold rolling the hot-rolled steel sheet which has been pickled, and further performing thermal treatment in a continuous annealing facility or a box type annealing furnace to obtain a cold-rolled steel sheet,
      wherein the rust inhibiting oil is applied to the cold-rolled steel sheet.
    9. (9) The method for producing a steel sheet for hot stamping according to any one of (5) to (8) described above,
      wherein an amount of S in the rust inhibiting oil that is applied to the steel sheet is 5% or less in mass%.
    10. (10) The method for producing a steel sheet for hot stamping according to any one of (5) to (9),
      wherein a composition of the slab contains, in mass%,
      one kind or two or more kinds selected from a group consisting of
      • 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%.
    11. (11) The method for producing a steel sheet for hot stamping according to any one of (5) to (10) described above,
      wherein a composition of the slab contains, in mass %,
      a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
    12. (12) A hot stamp formed body, including a composition containing,
      • in mass%,
      • C: 0.100% to 0.600%,
      • Si: 0.50% to 3.00%,
      • Mn: 1.20% to 4.00%,
      • Ti: 0.005% to 0.100%,
      • B: 0.0005% to 0.0100%,
      • P: 0.100% or less,
      • S: 0.0001% to 0.0100%,
      • Al: 0.005% to 1.000%,
      • N: 0.0100% or less,
      • Ni: 0% to 2.00%,
      • Cu: 0% to 2.00%,
      • Cr: 0% to 2.00%,
      • Mo: 0% to 2.00%,
      • Nb: 0% to 0.100%,
      • V: 0% to 0.100%,
      • W: 0% to 0.100%, and
      • a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
      • with a balance being Fe and impurities,
      • wherein three or more irregularities in a range of 0.2 µm to 8.0 µm in depth are present per 100 µm in an interface between scale and a base iron, and tensile strength is 1180 MPa or more.
    13. (13) The hot stamp formed body according to (12) described above,
      wherein an Si oxide, FeO, Fe3O4 and Fe2O3 are included in a surface of the hot stamp formed body, and a thickness of the scale is 10 µm or less.
    14. (14) The hot stamp formed body according to (12) or (13) described above,
      wherein the composition of the hot stamp formed body contains, in mass%,
      one kind or two or more kinds selected from a group consisting of
      • 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%.
    15. (15) The hot stamp formed body according to any one of (12) to (14) described above,
      wherein the composition of the hot stamp formed body contains, in mass %,
      a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
    ADVANTAGEOUS EFFECTS OF INVENTION
  • According to the present invention, the steel sheet for hot stamping excellent in scale adhesion at the time of hot stamping, in which adhesion of a molten metal to the die does not occur, the method for producing the steel sheet for hot stamping and the hot stamp formed body can be provided.
    • BRIEF DESCRIPTION OF DRAWINGS
    • [Fig. 1] Fig. 1 is a diagram illustrating a relationship between a coating oil amount on a steel sheet and surface roughness Rz of the steel sheet.
    • [Fig. 2] Fig. 2 is a diagram for explaining that when an S concentration in coating oil increases, scale easily detaches.
    • [Fig. 3] Fig. 3 is a diagram illustrating a relationship between a pickling time period and the surface roughness Rz of the steel sheet.
    • [Fig. 4A] Fig. 4A is a photograph showing a microstructure of a surface layer of a hot-rolled steel sheet before pickling.
    • [Fig. 4B] Fig. 4B is a photograph showing the surface layer microstructure after pickling.
    • [Fig. 5] Fig. 5 is a diagram illustrating a relationship between an coating oil amount and a thickness of scale.
    • [Fig. 6A] Fig. 6A is a photograph showing a section of a hot stamp formed body surface of an example of the present invention.
    • [Fig. 6B] Fig. 6B is a photograph showing a section of a hot stamp formed body surface of a comparative example.
    • [Fig. 7] Fig. 7 is a diagram for explaining that when the surface roughness Rz before hot stamp thermal treatment is less than 2.5, a number density of irregularities after hot stamp thermal treatment is less than 3.
    DESCRIPTION OF EMBODIMENTS
  • A steel sheet for hot stamping of the present invention contains from 0.5 mass% to 3.0 mass% of Si in the steel sheet, an amount of rust inhibiting oil applied to the steel sheet is in a range of 50 mg/m2 to 1500 mg/m2, and surface roughness of the steel sheet is Rz>2.5 µm. It is preferable that an S content contained in the rust inhibiting oil be 5 mass% or less.
  • First of all, the reason why the present inventors paid attention to the coating oil will be described.
  • With an objective of improving scale adhesion of the steel sheets to which no plating is applied (cold-rolled steel sheets or hot-rolled steel sheets), the present inventors have investigated the surface properties of the steel sheets, and influences of various kinds of treatment. As a result, the present inventors have found that although the steel sheets after degreasing show excellent scale adhesion, scale adhesion significantly deteriorates after rust inhibiting oil is applied. When the present inventors investigated the relationship between scale adhesion and rust inhibiting oil in more detail, it has been found that when an amount of S contained as impurities in the rust inhibiting oil increases, scale tends to detach easily. It is conceivable that S in the rust inhibiting oil has an influence on scale adhesion, although the detailed reason is unclear.
  • On the other hand, it is necessary to apply rust inhibiting oil such as mineral oil to a pickled hot-rolled steel sheet for hot stamping, and a cold-rolled steel sheet for hot stamping after cold rolling or annealing in order to restrain rust from occurring in the period from production to use. In particular, a steel sheet after pickling has been generally coated with oil of more than 1500 mg/m2, assuming that the period from delivery to a customer to use is long. When the present inventors investigated the influence of the coating oil amount for the purpose of making scale adhesion and rust inhibition properties compatible, the present inventors have found that as illustrated in Fig. 1, scale adhesion is enhanced by strictly controlling the range of the coating oil amount and the surface roughness of a steel sheet. The effect is exhibited by setting the coating oil amount at 50 mg/m2 to 1500 mg/m2. A lower limit of the coating oil amount is set at 50 mg/m2, because it is difficult to ensure excellent rust inhibition properties with the coating oil amount less than the coating oil amount of 50 mg/m2. The lower limit of the coating oil amount is preferably 100 mg/m2 or more, and more preferably 200 mg/m2 or more. An upper limit is set at 1500 mg/m2 to obtain an effect of excellent scale adhesion. The upper limit of the coating oil amount is set at 1500 mg/m2 because when the coating oil amount exceeds 1500 mg/m2, scale adhesion deteriorates. The upper limit is preferably 1000 mg/m2, is more preferably 900 mg/m2, and far more preferably is 800 mg/m2. Further, coated oil on the steel sheet surface burns at the time of heating, and therefore becomes the cause of generating soot. From this, a smaller coating oil amount is more preferable.
  • Scale adhesion illustrated in Fig. 1 was evaluated by a hot shallow drawing test in a cylindrical die of φ70 mm and a depth of 20 mm. After a steel sheet was heated to a temperature range of 800°C to 1100°C at 50°C/s in an electrical heater, and was retained for 0 seconds to 120 seconds, energization was stopped, the steel sheet was cooled to 650°C by standing to cool, and hot shallow drawing was performed in the above described die. Specimens after forming were visually observed, and specimens in which an area where scale was detached accounted for 5% or less were determined as having good (circle) scale adhesion, specimens in which the area where scale was detached accounted for 5 to 15% were determined as poor (triangle), and specimens in which the area where scale was detached accounted for more than 15% were determined as very poor (X). The specimens in which the area where scale was detached accounted for 5% or less were determined as within the range of the present invention.
  • It is possible to evaluate scale adhesion without particularly limiting the heating method. For example, conditions of any of a heating furnace, far-infrared rays, near-infrared rays and electrical heating may be adopted. Further, when a steel sheet is heated in a heating furnace, more excellent scale adhesion can be obtained by thinning scale by controlling the atmosphere in the heating furnace and restraining oxidation of the steel sheet.
  • Note that a shallow drawing test temperature may be in any temperature region as long as a steel sheet can be processed, but in general, a steel sheet for hot stamping has high strength and excellent shape fixability by processing in an austenite region and subsequent die hardening. From this, characteristics evaluation was carried out by hot shallow drawing at 650°C exceeding Ar3.
  • As an oil coating method, electrostatic oil coating, spray, a roll coater and the like are generally used, but the oil coating method is not limited as long as the coating oil amount can be ensured.
  • Although the kind of oil is not specified, NOX-RUST530F (made by PARKER INDUSTRIES, INC.) or the like is generally used if the oil is mineral oil, for example, and if the coating oil amount satisfies the range of the present invention, the kind of oil is not limited.
  • Although the coating oil amount may be measured by any method as long as the coating oil amount can be measured, the present inventors measured the coating oil amount by the following method. The steel sheet coated with rust inhibiting oil was cut into 150 mm square first, and thereafter, a tape was applied so that a 100 mm by 100 mm region is exposed. Subsequently, the weights of the coating oil and the steel sheet to which seal was carried out (including the weight of the tape) were measured in advance. Subsequently, degreasing was performed by wiping off the rust inhibiting oil on the steel sheet surface with cloth containing acetone, the weight of the degreased steel sheet was measured, the weights before and after degreasing were compared, and thereby the coating oil amount per unit area was calculated. Measurement was carried out at three spots in each of the steel sheets, and an average value of the attached amounts was determined as a coating oil attaching amount of each of the steel sheets.
  • It is preferable to restrict the S content contained in the rust inhibiting oil to 5 mass% or less. When the present inventors investigated the relationship between the S content in the coating oil and a scale detached area ratio as illustrated in Fig. 2, the present inventors have found that as the S content in the coating oil becomes smaller, the scale adhesion increases, and especially when the S content in the coating oil is 5 mass% or less, the scale detached area becomes substantially 0%. It is conceivable that while the oil contained in the rust inhibiting oil is burned and eliminated during heating, S contained as an impurity remains on the steel sheet surface to concentrate into scale, and thereby deteriorates scale adhesion, although detailed mechanism is unclear. Hence, it is preferable to reduce the content of S contained in the rust inhibiting oil. The S content is preferably 4 mass% or less, and is more preferably 3 mass% or less. Although analysis of S in the rust inhibiting oil may be performed by any method as long as S can be analyzed, the present inventors extracted 5 mL of the rust inhibiting oil which is applied to the steel sheet, and carried out analysis by fluorescence X-rays (C-ray Fluorescence Sulfur-in-Oil Analyzer SLFA-2800/HORIBA). In measurement, measurement was carried out with n=3, and an average value thereof was defined as the S content.
  • The surface roughness of the steel sheet will be described next. In order to ensure scale adhesion, the surface roughness of the steel sheet needs to satisfy Rz>2.5 µm. A result obtained by investigating a relationship between the surface roughness Rz of the steel sheet and scale adhesion is as illustrated in Fig. 1 described above. By providing irregularities on an interface between scale that is generated at the time of hot stamping thermal treatment and a base iron, the irregularities are formed on the interface between the base iron and scale, and further increase in adhesion is brought about. The effect is generally referred to as an anchor effect. In particular, scale that is generated at the time of heating in the present steel sheet is thin. As a result, in the present steel sheet in which the thickness of the scale is thin, scale having irregularities is formed by receiving an influence of the base iron surface state. Hence, the surface roughness of the steel sheet before hot stamping needs to satisfy Rz>2.5 µm. When Rz≤2.5 µm, the surface roughness of the steel sheet is small, and the anchor effect is insufficient, and thus excellent scale adhesion at the time of hot stamping cannot be ensured. Although the effect of the excellent scale adhesion of the present invention can be obtained without particularly providing the upper limit, if scale adhesion is excessively increased, it becomes difficult to remove scale in a downstream process such as shot blast, for example. Thus, it is preferable to set Rz<8.0 µm. It is more preferable to set Rz<7.0 µm. However, even if Rz≥8.0 µm is set, it is possible to ensure excellent scale adhesion that is the effect of the present invention. Note that in the steel sheet in which an Si content is less than 0.50 mass%, even if the surface roughness of Rz>2.5 µm is set, thick Fe scale is formed at the time of heating, and thus even when the irregularities are on the steel sheet surface, the interface between the base iron and the scale becomes flat by excessive oxidation. As a result, the irregularities in the interface between the scale and the base iron are eliminated, and the effect of the excellent scale adhesion that is the effect of the present invention is not exhibited.
  • Although measurement of the surface roughness Rz may be performed by any method, the present inventors measured the region of a length of 10 mm with n=3, with use of a contact surface roughness measuring instrument (SURFCOM2000DX/SD3 made by TOKYO SEIMITSU CO., LTD) with a probe point angle of 60°, and a point R of 2 µm, and determined the average value as the surface roughness Rz of each of the steel sheets.
  • Next, a scale structure of the hot stamp formed body will be described. The steel sheet for hot stamping of the present invention ensures scale adhesion by control of the irregularities in the interface between the scale and the base iron. Hence, the scale can be scale mainly composed of an Si oxide, Fe3O4, Fe2O3 and FeO. An Si oxide exists in the interface between base iron and iron scale (FeO, Fe2O3, Fe2O3), and thereby controls a thickness of the iron scale. Hence, the scale needs to contain an Si oxide. Since the main object is to control the thickness of the iron oxide, even if the Si oxide is very thin, it is sufficient if the Si oxide exists, and even with 1 nm, the Si oxide exhibits the effect.
  • Composition analysis of the scale of the formed body was carried out by X-ray diffraction by cutting out the sheet from a bottom of the cylindrical portion of a shallow drawn specimen piece. From a peak intensity ratio of the respective oxides, volume ratios of the respective Fe oxides were measured. The Si oxide existed very thinly, and the volume ratio was less than 1%, and thus quantitative evaluation in X-ray diffraction was difficult. However, it is possible to confirm that an Si oxide exists in the interface between the scale and the base iron by line analysis of EPMA (Electron Probe Micro Analyzer).
  • The thickness of the scale is preferably 10 µm or less. When the thickness of the scale is 10 µm or less, scale adhesion is enhanced more. When the thickness of the scale exceeds 10 µm, the scale tends to detach easily due to a thermal stress that works at the time of cooling at the time of hot stamping. Thereafter, in a scale removing process such as shot blast or wet blast, fractures occur among Fe scales, and a scale existing on an outer side detaches. As a result, the scale also has a problem of being inferior in scale removability. Hence, the thickness of the scale is preferably 10 µm or less. The thickness of the scale is more preferably 7 µm or less, and is more preferably 5 µm or less. The thickness of the scale is achieved by controlling the coating oil amount within the predetermined range simultaneously with controlling the Si content of the steel sheet within a predetermined range. Fig. 5 illustrates a relationship between the coating oil amount and the scale thickness.
  • In the interface between the base iron and the scale in the hot stamp formed body of the present invention, three or more irregularities of 0.2 µm to 8.0 µm are present per 100 µm. Fig. 6A shows a photograph of an interface between a base iron and scale of a formed body excellent in scale adhesion, and Fig. 6B shows a photograph of an interface between a base iron and scale inferior in scale adhesion. Since the irregularities contribute to enhancement in scale adhesion at the time of hot stamping, and thus excellent scale adhesion can be ensured by controlling the irregularities within the above described range. Irregularities of less than 0.2 µm provide an insufficient anchor effect, and provide inferior scale adhesion. With irregularities of 8.0 µm or more, scale adhesion is so strong that scale is difficult to remove in the subsequent scale removal process, for example, by shot blast or wet blast, and therefore it is preferable to make the irregularities in the interface between scale and the base iron 8.0 µm or less. The irregularities are more preferably 6.0 µm or less, and more preferably 4.0 µm or less. Note that even if the irregularities exceed 8.0 µm, excellent scale adhesiveness that is the effect of the present invention can be ensured.
  • When the number of irregularities of 0.2 µm to 8.0 µm per 100 µm is less than three, an improvement effect of scale adhesion is not sufficient, and thus the number of irregularities per 100 µm is set at three or more. It is possible to ensure excellent scale adhesion which is the effect of the present invention without particularly setting an upper limit of the number of irregularities per 100 µm. Note that the irregularities of the formed body are correlated with the surface roughness Rz of the steel sheet as illustrated in Fig. 7, and are controllable by setting the steel sheet surface roughness as Rz>2.5 µm.
  • Next, chemical compositions of the steel sheet and the hot stamp formed body of the present invention will be described. Note that hereunder % means mass%.
    • C: 0.100% to 0.600%
  • C represents an element that is contained to enhance the strength of the steel sheet. If a C content is less than 0.100%, tensile strength of 1180 MPa or more cannot be ensured, and a formed body with high strength which is the object of hot stamp cannot be ensured. When the C content exceeds 0.600%, weldability and processibility become insufficient, and thus the C content is set at 0.100% to 0.600%. The C content is preferably 0.100% to 0.550%, and is more preferably 0.150% to 0.500%. However, if the strength of the formed 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 enhances scale adhesion by controlling the scale composition at the time of hot stamping, and therefore Si is an essential element. If the Si content is less than 0.50%, the thickness of Fe scale cannot be controlled, and excellent scale adhesion cannot be ensured. Consequently, it is necessary to set the Si content at 0.50% or more. Further, when application to a member which is difficult to form at the time of hot stamping is considered, it is preferable to increase the Si content. Accordingly, the Si content is preferably 0.70% or more, and is more preferably 0.90% or more. Meanwhile, Si increases an Ae3 point, and the heating temperature necessary to make martensite a main phase, and thus if the Si is excessively contained, productivity and economic efficiency are reduced. Hence, an upper limit of the Si content is set as 3.00%. The upper limit of the Si content is preferably 2.5%, and the upper limit is more preferably 2.0%. However, it is possible to ensure excellent scale adhesion excepting productivity and economic efficiency.
    • Mn: 1.20% to 4.00%
  • Mn delays ferrite transformation in a cooling process at the time of hot stamping, and makes a hot stamp formed body into a structure having a martensite main phase, and thus it is necessary to contain 1.20% or more of Mn. If the Mn content is less than 1.20%, martensite cannot be made a main phase, and it is difficult to ensure high strength which is an object of the hot stamp formed body, and thus a lower limit of the Mn content is set as 1.20%. However, if the strength of the formed body is not required, excellent scale adhesion can be ensured even if the Mn content is less than 1.20%. When the Mn content exceeds 4.00%, the effect is saturated, embrittlement is caused, and a fracture is caused at the time of casting, cold rolling or hot rolling, and thus an upper limit of the Mn content is set as 4.00%. The Mn content is preferably within a range of 1.50% to 3.50%, and is more preferably within a range of 2.00% to 3.00%.
    • Ti: 0.005% to 0.100%
  • Ti is an element that combines with N to form TiN, and thereby restrains B from being a nitride to enhance hardenability. The effect becomes remarkable when a Ti content is 0.005% or more, and thus the Ti content is set as 0.005% or more. However, when the Ti content exceeds 0.100%, a Ti carbide is formed, an amount of C that contributes to strengthening martensite is reduced, and reduction in strength is caused, and thus an upper limit of the Ti content is set as 0.100%. The C content is preferably within a range of 0.005% to 0.080%, and is more preferably within a range of 0.005% to 0.060%.
    • B: 0.0005% to 0.0100%
  • B enhances hardenability at the time of hot stamping, and contributes to making a main phase of martensite. The effect is remarkable when a B content is 0.0005% or more, and thus it is necessary to set the B content at 0.0005% or more. When the B content exceeds 0.0100%, the effect is saturated, an iron boride is precipitated, and the effect of hardenability of B is lost, and thus an upper limit of the B content is set at 0.0100%. The B content is preferably within a range of 0.0005% to 0.0080%, and is more preferably within a range of 0.0005% to 0.0050%.
    • P: 0.100% or less
  • P is an element that segregates in a central portion of a sheet thickness of the steel sheet, and is an element that embrittles a welded portion. Accordingly, an upper limit of a P content is set at 0.100%. A more preferable upper limit is 0.050%. The lower the P content, the more preferable, and although the effect of the present invention is exhibited without particularly setting the lower limit, but it is economically disadvantageous to reduce P to less than 0.001% from the viewpoint of productivity and cost of dephosphorization, and thus the lower limit is preferably set at 0.001%.
    • S: 0.0001% to 0.0100%
  • S exerts a large influence on scale adhesion, and thus it is necessary to restrict a content in the steel sheet. Accordingly, an upper limit of an S content is set at 0.0100%. A lower limit of the S content is set at 0.0001% because it is economically disadvantageous from the viewpoint of productivity and cost of dephosphorization. The S content is preferably within a range of 0.0001% to 0.0070%, and is more preferably within a range of 0.0003% to 0.0050%.
    • Al: 0.005% to 1.000%
  • Al acts as a deoxidizer, and thus an Al content is set as 0.005% or more. When the Al content is less than 0.005%, a sufficient deoxidization effect cannot be obtained, and a large amount of enclosure (oxide) exist in the steel sheet. These enclosures become starting points of destruction at the time of hot stamping, and the causes of breakage, and therefore are not preferable. The effect becomes remarkable when the Al content reaches 0.005% or more, and thus it is necessary to set the Al content at 0.005% or more. When the Al content exceeds 1.000%, the Ac3 point is increased and a heating temperature at the time of hot stamping is increased. That is, hot stamp is a technique of obtaining a formed body with high strength having a complicated shape by heating a steel sheet to an austenite single phase region, and subjecting the steel sheet to hot die press excellent in formability, and rapidly cooling by using a die. As a result, when a large amount of Al is contained, the Ac3 point is significantly increased, increase in the heating temperature required for austenite single phase region heating is caused, and productivity is reduced. Consequently, it is necessary to set an upper limit of the Al content at 1.000%. The Al content is preferably within a range of 0.005% to 0.500%, and is more preferably within a range of 0.005% to 0.300%.
    • N: 0.0100% or less
  • N is an element that forms coarse nitrides and deteriorates bendability and hole-expandability. When an N content exceeds 0.0100%, bendability and hole-expandability are significantly deteriorated, and thus an upper limit of the N content is set at 0.0100%. Note that N becomes a cause of generating a blowhole at the time of welding, and thus the smaller the N content is, the more preferable. Accordingly, the N content is preferably 0.0070 or less, and is more preferably 0.0050% or less. Although it is not necessary to particularly set a lower limit of the N content, manufacturing cost increases significantly when the N content is reduced to less than 0.0001%, and thus a practical lower limit is 0.0001%. From the viewpoint of manufacturing cost, the N content is more preferably 0.0005% or more.
  • Note that other unavoidable elements may be contained in extremely small amounts. For example, O forms an oxide and exists as an enclosure.
  • The steel sheet of the present invention further contains the following elements in accordance with necessity.
    • Ni: 0.01% to 2.00%
    • Cu: 0.01% to 2.00%
    • Cr: 0.01% to 2.00%
    • Mo: 0.01% to 2.00%
  • Ni, Cu, Cr and Mo are elements that contribute to increase in strength by enhancing hardenability at the time of hot stamping, and making a main phase of martensite. The effect becomes remarkable by containing 0.01% or more of each one kind or two or more kinds selected from a group consisting of Ni, Cu, Cr and Mo, and thus contents of the elements are preferably 0.01% respectively. When the content of each of the elements exceeds a predetermined amount, weldability, hot workability and the like are deteriorated, or the strength of the steel sheet for hot stamping is so high as to be likely to cause a manufacturing trouble, and thus upper limits of the contents of these elements are preferably set at 2.00%.
    • Nb: 0.005 to 0.100%
    • V: 0.005 to 0.100%
    • W: 0.005 to 0.100%
  • Nb, V and W are elements that strengthen fine grains by inhibiting growth of austenite at the time of hot stamping, and contribute to increase in strength and enhancement in tenacity. Hence, one kind or two or more kinds selected from a group consisting of these elements may be contained. The effect becomes more remarkable when 0.005% or more of each of the elements are contained, and thus it is preferable that 0.005% or more of each of the elements be contained. Note that when more than 0.100% of each of these elements is contained, it is not preferable because Nb, V and W carbides are formed, an amount of C that contributes to strengthening martensite is reduced, and reduction in strength is caused. Each of the elements is preferably in a range of 0.005% to 0.090%.
  • A total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0.0003% to 0.0300%
  • In the present invention, 0.0003% to 0.0300% of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg may be further contained in total.
  • REM, Ca, Ce and Mg are elements that enhance strength and contribute to improvement of the material. When the total of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg is less than 0.0003%, a sufficient effect cannot be obtained, and thus it is preferable to set a lower limit of the total at 0.0003%. When the total of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg exceeds 0.0300%, castability and hot workability are likely to be deteriorated, and thus it is preferable to set an upper limit of the total at 0.0300%. Note that REM is an abbreviation of Rare Earth Metal, and refers to an element belonging to a lanthanoid system. In the present invention, REM is often added in misch metal, and besides Ce, elements of a lanthanoid system are sometimes contained in combination.
  • In the present invention, the effect of the present invention becomes apparent even when elements of a lanthanoid system other than La and Ce are contained as unavoidable impurities, and the effect of the present invention becomes apparent even when the other elements such as metals are contained as impurities.
  • Next, features of microstructures of the steel sheet for hot stamping and hot stamp formed body of the present invention will be described.
  • Provided that the chemical composition, the surface roughness of the steel sheet, and the coating oil amount satisfy the ranges of the present invention, the effect of the present invention can be exhibited by any of a pickled hot-rolled steel sheet, a cold-rolled steel sheet obtained by cold-rolling a hot-rolled steel sheet, or a cold-rolled steel sheet to which annealing is applied after cold rolling.
  • These steel sheets are heated to an austenite region exceeding 800°C at the time of hot stamping, and therefore exhibit performance as steel sheets for hot stamping having excellent scale adhesion that is the effect of the present invention without particularly limiting the microstructure. However, when mechanical cutting of the steel sheets and cold punching are carried out prior to hot stamping, the strength of the steel sheets is preferably as low as possible in order to reduce wear and tear of dies, cutting edges of cutters, or punching dies. Consequently, the microstructure of the steel sheet for hot stamping is preferably ferrite and pearlite structures, or a bainite structure and a structure obtained by tempering martensite. However, if wear and tear of a punch and dies at the time of mechanical cutting and cold punching do not become a problem, it is possible to ensure excellent scale adhesion which is the effect of the present invention, even if one kind or two or more kinds of retained austenite, martensite in a hardened state, and bainite are contained. Further, in order to reduce the strength of the steel sheet, thermal treatment in a box type annealing furnace or a continuous annealing facility may be carried out. Alternatively, even when cold rolling is carried out after the above softening treatment, and the sheet thickness is controlled to a predetermined sheet thickness, excellent scale adhesion which is the effect of the present invention is ensured.
  • When formed body strength after hot stamping is enhanced, and high component strength is obtained, the microstructure of the formed body preferably has a martensite main phase. In particular, in order to ensure tensile strength of 1180 MPa or more, a volume ratio of martensite that is a main phase is preferably made 60% or more. Martensite may be subjected to tempering after hot stamping, and made tempered martensite. As the structure other than martensite, bainite, ferrite, pearlite, cementite and retained austenite may be contained. Further, even if the martensite volume rate is less than 60%, it is possible to ensure the excellent scale adhesion of the present invention.
  • The following methods are used in identification of the microstructures (tempered martensite, martensite, bainite, ferrite, pearlite, retained austenite and a remaining structure) composing the steel sheet structure, confirmation of existence positions, and measurement of area ratios. For example, it is possible to corrode a section in a steel sheet rolling direction or a section in a direction perpendicular to the rolling direction with a nital reagent and the reagent disclosed in Japanese Laid-open Patent Publication No. 59-219473 , and observe the structure with a 1000 to 100000-power scanning electron microscope (SEM: Scanning Electron Microscope) and transmission electron microscope (TEM: Transmission Electron Microscope). The present inventors determined the sheet thickness section parallel with the rolling direction of the steel sheet as an observation surface, extracted a specimen, polished the observation surface, performed nital etching, observed a range of thickness of 1/8 to 3/8 with 1/4 of the sheet thickness as a center with a field emission scanning electron microscope (FE-SEM: Field Emission Scanning Electron Microscope), measured an area fraction, and the area fraction was taken as a volume fraction. As for the volume fraction of the retained austenite, the volume fraction was measured by performing X-ray diffraction with the surface which was parallel with the sheet surface of the parent steel sheet and had a 1/4 of thickness, used as the observation surface.
  • Next, a method for producing the steel sheet for hot stamping of the present invention will be described.
  • Although the other operation conditions are based on a usual method, the following conditions are preferable in terms of productivity.
  • In order to produce the steel sheet in the present invention, a slab having the same component composition as the component composition of the aforementioned steel sheet is cast first. As the slab provided for hot rolling, a continuously cast slab, the slab produced by a thin slab caster or the like can be used. The method for manufacturing the steel sheet of the present invention is adapted to a process like continuous casting-direct rolling (CC-DR) that performs hot rolling immediately after casting.
    • Slab heating temperature: 1100°C or higher
    • Hot-rolling completion temperature: Ar3 transformation point or higher
    • Coiling temperature: 700°C or lower
    • Cold rolling ratio: 30 to 70%
  • The slab heating temperature is preferably set at 1100°C or higher. The slab heating temperature in a temperature region of lower than 1100°C causes reduction in the finishing rolling temperature, and thus strength at the time of finishing rolling tends to be high. As a result, there is the possibility that rolling becomes difficult, a poor shape of the steel sheet after rolling is caused, and thus the slab heating temperature is preferably set at 1100°C or higher.
  • The finishing rolling temperature is preferably set at the Ar3 transformation point or higher. When the finishing rolling temperature becomes lower than the Ar3 transformation point, a rolling load becomes high, and there is the possibility that rolling becomes difficult, and a poor shape of the steel sheet after rolling is caused, and thus a lower limit of the finishing rolling temperature is preferably set at the Ar3 transformation point. An upper limit of the finishing rolling temperature does not have to be particularly set, but if the finishing rolling temperature is set to be excessively high, the slab heating temperature has to be made excessively high in order to ensure the temperature, and thus the upper limit of the finishing rolling temperature is preferably 1100°C.
  • The coiling temperature is preferably set at 700°C or lower. When the coiling temperature exceeds 700°C, the thickness of the oxides formed on the steel sheet surface is excessively increased, and the pickling property is deteriorated, and thus the coiling temperature higher than 700°C is not preferable. When cold rolling is performed thereafter, a lower limit of the coiling temperature is preferably set at 400°C. When the coiling temperature is lower than 400°C, the strength of the hot-rolled steel sheet extremely increases, and a sheet fracture and a poor shape at the time of cold rolling are easily caused, and thus the lower limit of the coiling temperature is preferably set at 400°C. However, if the hot-rolled steel sheet which is coiled is intended to be softened by heating the coiled hot-rolled steel sheet in the box type annealing furnace or the continuous annealing facility, the steel sheet may be coiled at a low temperature of lower than 400°C. Note that at the time of hot-rolling, rough-rolled sheets may be bonded to one another and finishing rolling may be continuously performed. Further, the rough-rolled sheet may be coiled temporarily.
  • Next, pickling is applied to the hot-rolled steel sheet which is produced in this way for 30 seconds or more in an aqueous solution with an temperature of 80°C to 100°C in which a concentration of acid is 3 mass% to 20 mass% and an inhibitor is included. In the present invention, pickling under the present conditions is extremely important, and in order to control the surface roughness Rz of the steel sheet to more than 2.5 µm, pickling under the above described conditions is necessary. Note that an aqueous solution of a hydrochloric acid, a sulfuric acid or the like as an acid is generally used, and an aqua regia or the like may be used.
  • The temperature of the aqueous solution is set at 80°C to lower than 100°C, because with a temperature lower than 80°C, a reaction rate is low, and it takes a long time to bring the surface roughness of the hot-rolled steel sheet into a proper range. Meanwhile, heating at a temperature of 100°C or higher is dangerous and is not preferable because the solution boils and splashes although the reaction of pickling has no problem.
  • Further, the reason why the concentration of the acid is set at 3 mass% to 20 mass% is to control the surface roughness Rz of the hot-rolled steel sheet within the proper range. When the concentration of the acid is less than 3 mass%, it takes a long time to control the irregularities on the surface by pickling. When the concentration of the acid exceeds 20 mass%, a pickling tank is damaged significantly and facility management becomes difficult, and thus it is not preferable. A preferable range of the concentration of the acid is a range of 5 mass% to 15 mass%.
  • Further, the reason why the pickling time period is set at 30 seconds or more is to stably give predetermined irregularities (irregularities of Rz>2.5 µm) to the steel sheet surface by pickling. When the pickling tank is divided into a plurality of tanks, if a pickling time period of some of the pickling tanks or a total pickling time period satisfies the above described conditions, the surface roughness Rz of the hot-rolled steel sheet can be brought into the range of the present invention, even if concentrations or temperatures of the individual pickling tanks differ from one another. Further, pickling may be carried out by being divided into a plurality of times. Note that in the experiment by the present inventors, a hydrochloric acid including an inhibitor was used, but the effect of the present invention can be obtained by using another acid such as hydrochloric acid using no inhibitor, a sulfuric acid, and a nitric acid, or a composite of these acids, as long as the surface roughness Rz can be controlled by pickling.
  • Further, the irregularities formed by pickling of the hot-rolled steel sheet also remain even after temper rolling, cold rolling or annealing is carried out, and thus it is extremely important to control the pickling conditions, and give irregularities to the sheet surface after pickling. Consequently, temper rolling may be carried out to the hot-rolled steel sheet after pickling.
  • Further, even with a cold-rolled steel sheet to which only cold rolling is performed, or a cold-rolled steel sheet thermally treated in a continuous annealing facility or a box type annealing furnace after cold rolling, irregularities are formed on the surface by performing pickling before cold rolling, and the predetermined effect can be obtained. Note that cold rolling is preferably performed with roll roughness Rz for cold rolling within a range of 1.0 µm to 20.0 µm, and the cold rolling roll also includes temper rolling roll.
  • Cold rolling is applied to the hot-rolled steel sheet pickled under the conditions as above at a draft of 30% to 80%, and the steel sheet may be passed through a continuous annealing facility. When the draft is less than 30%, it becomes difficult to keep the shape of the steel sheet flat, and ductility of the finished product deteriorates, and thus a lower limit of the draft is preferably set at 30%. When the draft exceeds 80%, a rolling load becomes excessively large, and cold rolling becomes difficult, and thus an upper limit of the draft is preferably set at 80%. The draft is more preferably 40% to 70%. The effect of the present invention becomes apparent even without particularly specifying the number of times of rolling pass and the draft of each pass, and thus it is not necessary to specify the number of times of rolling pass, and the draft at each pass.
  • Thereafter, the cold-rolled steel sheet may be passed through the continuous annealing line. An object of the treatment is to soften the steel sheet which is highly strengthened by cold-rolling, and thus any conditions may be adopted as long as the condition is such that the steel sheet is softened. For example, when the annealing temperature is in a range of 550°C to 750°C, dislocation introduced at the time of cold rolling is released by recovery, recrystalization, or phase transformation, and thus annealing is preferably performed in this temperature region.
  • By performing annealing by a box type furnace for the similar purpose, the steel sheet for hot stamping excellent in scale adhesion of the present invention can be obtained.
  • Thereafter, oil coating is carried out. As an oil coating method, electrostatic oiling, spray, a roll coater and the like are generally used, and as long as a coating oil amount in a range of 50 mg/m2 to 1500 mg/m2 can be ensured, the method is not limited. In the present invention, coating of a predetermined amount of oil was carried out by an electrostatic oiling machine. Further, as long as the coating oil amount in the range of 50 mg/m2 to 1500 mg/m2 can be ensured, a rust inhibitor in an amount equal to or larger than the coating oil amount may be applied, and degreasing may be performed.
  • The excellent scale adhesion that is the effect of the present invention and a rust inhibition property can be made compatible without particularly limiting the hot stamping conditions. For example, by producing by the production method shown as follows, compatibility of excellent performance of the tensile strength of 1180 MPa or more and productivity is achieved. At the time of performing hot stamping, heating is preferably performed to a temperature region of 800°C to 1100°C at a heating rate of 2°C/second or more. By heating at a rate of 2°C/second or more, scale generation at the time of heating can be restrained, and the effect of improvement in scale adhesion is provided. The heating rate is preferably 5°C/second or more, and is more preferably 10°C/second or more. Further, increase of the heating rate is also effective for the purpose of enhancing productivity.
  • The annealing temperature at the time of performing hot stamping is preferably within the range of 800°C to 1100°C. By performing annealing in this temperature region, it is possible to make the structure into an austenite single phase structure, and the structure can be made into a structure having martensite as a main phase by cooling that is performed subsequently. When the annealing temperature at this time is lower than 800°C, the structure at the time of annealing is made into a ferrite and austenite structures, the ferrite grows in the cooling process, the ferrite volume ratio exceeds 10%, and the tensile strength of the hot stamp formed body becomes lower than 1180 MPa. Consequently, a lower limit of the annealing temperature is preferably set at 800°C. When the annealing temperature exceeds 1100°C, not only the effect is saturated, but also the scale thickness is significantly increased, and there arises the fear that scale adhesion is reduced. Consequently, it is preferable to perform annealing at 1100°C or lower. The annealing temperature is more preferably in a range of 830°C to 1050°C.
  • After heating, retention may be performed in the temperature region of 800°C to 1100°C. When retention is carried out at a high temperature, melting of carbides included in the steel sheet is possible, and contribution is made to increase in the strength of the steel sheet and enhancement in hardenability. Retention includes residence, heating removal and cooling removal in the present temperature region. Since the object is to melt the carbides, the object is achieved as long as the residence time period in the present temperature region is ensured. Although the limitation on the retention time period is not particularly provided, 1000 seconds is preferably set as an upper limit, because when the retention time period is 1000 seconds or more, the scale thickness becomes excessively large, and scale adhesion is deteriorated.
  • Thereafter, a temperature of 800°C to 700°C is preferably reduced at an average cooling rate of 5°C/second or more. Here, 700°C is a die cooling start temperature, and the reason why the temperature of 800°C to 700°C is reduced at 5°C/second or more is to avoid ferrite transformation, bainite transformation and pearlite transformation, and make the structure into a martensite main phase. When the cooling rate is less than 5°C/second, these soft structures are formed, and it is difficult to ensure the tensile strength of 1180 MPa or more. Meanwhile, the effect of the present invention is exhibited without particularly setting the upper limit of the cooling rate. The reason why the temperature range which is reduced at 5°C/second or more is set from 800°C to 700°C is that in this temperature range, the structure of ferrite or the like that causes reduction in strength is likely to be formed. Cooling at this time is not limited to continuous cooling, and even when retention and heating in the temperature region are performed, the effect of the present invention is exhibited as long as the average cooling rate is 5°C/second or more. The effect of the present invention can be exhibited without particularly limiting the cooling method. That is, the effect of the present invention can be exhibited by either one of cooling using a die or die cooling using water cooling in combination.
    • EXAMPLES
  • Next, examples of the present invention will be described, and conditions in the examples are only one example of the conditions adopted to confirm implementability and the effect of the present invention, and the present invention is not limited to the one condition example. The present invention can adopt various conditions as long as the conditions achieve the object of the present invention without departing from the gist of the present invention.
  • First, slabs of the component compositions of A to S and a to n shown in Table 1 were cast, and after the slabs were temporarily cooled to a room temperature, heating was carried out for 220 minutes in a heating furnace with a furnace temperature = 1230°C, hot rolling was carried out with the finishing rolling temperature = 920°C to 960°C, and coiling was carried out under the temperature conditions shown in Table 2.
    • [Table 1]
  • Table.1 Chemical component(mass%)
    C Si Mn P S Ti B N Al Others
    A 0211 1.04 2.29 0.011 0.0009 0.025 0.0028 0.0023 0.023 -
    B 0207 0.67 2.09 0.009 0.0012 0.023 0.0014 0.0027 0.019 -
    C 0.189 1.83 2.55 0.007 0.0016 0.028 0.0029 0.0026 0.035 -
    D 0207 121 1.44 0.012 0.0018 0.035 0.0009 0.0031 0.056 Cr=0.68
    E 0208 1.19 1.82 0.013 0.0022 0.045 0.0022 0.0024 0.045 Mo=0.13
    F 0.100 1.11 1.74 0.008 0.0019 0.029 0.0023 0.0022 0.024 Ni=0.44, Cu=0.12
    G 0203 1.05 227 0.009 0.0017 0.024 0.0020 0.0026 0.029 Nb=0.068
    H 0219 0.98 2.35 0.010 0.0033 0.021 0.0024 0.0037 0.018 V=0.054
    I 0228 124 2.19 0.011 0.0027 0.022 0.0021 0.0024 0.033 W=0.033
    J 0218 124 2.31 0.015 0.0045 0.026 0.0034 0.0034 0.027 REM=0.0046
    K 0234 1.05 2.37 0.016 0.0039 0.024 0.0025 0.0021 0.025 Ca=0.0033
    L 0219 1.03 2.19 0.009 0.0048 0.025 0.0021 0.0038 0.011 Ce=0.0029
    M 0246 1.11 2.27 0.013 0.0052 0.019 0.0021 0.0029 0.007 Mg=0.0019
    N 0309 1.09 2.19 0.008 0.0024 0.016 0.0026 0.0019 0.022 -
    O 0314 0.78 2.11 0.013 0.0028 0.025 0.0018 0.0024 0.030 -
    P 0311 1.32 1.87 0.011 0.0030 0.028 0.0020 0.0023 0.035 Cr=0.18
    Q 0356 1.24 2.09 0.015 0.0034 0.022 0.0034 0.0025 0.029 -
    R 0.349 1.06 1.43 0.016 0.0019 0.021 0.0032 0.0022 0.027 Cr=0.46
    S 0.412 0.99 222 0.007 0.0014 0.028 0.0023 0.0020 0.024 -
    a 0.097 098 2.03 0.022 0.0022 0.033 0.0028 0.0023 0.021 -
    b 0.698 1.49 1.68 0.007 0.0006 0.024 0.0026 0.0029 0.089 -
    c 0203 034 2.11 0.015 0.0027 0.029 0.0026 0.0029 0.019 -
    d 0.194 325 2.09 0.009 0.0018 0.021 0.0031 0.0025 0.023 -
    e 0211 1.03 1.12 0.014 0.0016 0.026 0.0018 0.0021 0.026 -
    f 0.199 123 7.39 0.024 0.0039 0.025 0.0049 0.0042 0.038 -
    g 0205 0.78 231 0.009 0.0148 0.021 0.0012 0.0031 0.022 -
    h 0209 1.16 2.31 0.007 0.0013. - 0.0018 0.0034 0.031 -
    l 0.184 1.08 1.42 0.006 0.0037 0.139 0.0034 0.0037 0.022 -
    j 0210 1.05 1.89 0.016 0.0035 0.022 - 0.0028 0.027 -
    k 0201 0.98 1.45 0.011 0.0055 0.027 0.1180 0.0033 0.024 -
    l 0.198 121 1.52 0.008 0.0042 0.033 0.0027 0.0191 0.046 -
    m 0205 0.87 2.42 0.011 0.0057 0.021 0.0016 0.0082 0.001 -
    n 0213 0.94 1.98 0.012 0.0019 0.023 0.0024 0.0024 1.285 -
    The underlined part means being outside the range of the present invention.
    "-"= means that each element is not added.
    • [Table 2]
  • Table.2
    Steel number Steel grade*1 Colling temperature (°C) Acid concentration (%) Acid temperature (°C) Pickling time period (s) Kind of coating oll Coating oil amount (mg/m2) S content (mass%) Remarks
    A1 FH 580 8 83 160 NOX503F - 0 Comparative steel
    A2 FH 600 6 87 200 NOX503F 60 0 Present invention steel
    A3 FH 590 8 85 160 NOX503F 140 1 Present invention steel
    A4 FH 680 7 90 680 NOX503F 270 1 Present invention steel
    A5 FH 590 9 89 160 NOX503F 480 1 Present invention steel
    A6 FH 600 9 86 160 NOX503F 780 1 Present invention steel
    A7 FH 580 8 84 240 NOX503F 1020 1 Present invention steel
    A8 FH 550 8 86 40 NOX503F 1480 5 Present invention steel
    A9 FH 510 6 82 18 NOX503F 1000 2 Comparative steel
    A10 FH 520 7 85 24 NOX503F 970 1 Comparative steel
    A11 FH 510 6 85 28 NOX503F B20 1 Comparative steel
    A12 FH 620 10 94 180 NOX503F 1790 6 Comparative steel
    A13 FH 560 8 89 65 NOX503F 2050 6 Comparative steel
    A14 FH 600 9 85 200 NOX503F Comparative steel
    A15 FH 570 8 87 240 NOX504F 4880 9 Comparative steel
    B1 HR 580 12 85 230 NOX503F 490 1 Present invention steel
    C1 OR 590 8 86 160 NOX503F 420 1 Present invention steel
    D1 FH 560 8 85 100 NOX503F 550 1 Present invention steel
    E1 FH 560 7 83 100 NOX503F 1030 2 Present invention steel
    F1 FH 570 6 88 140 NOX503F 1200 3 Present invention steel
    G1 FH 610 B 83 200 NOX503F 820 1 Present invention steel
    H1 FH 600 10 89 130 NOX503F 670 1 Present invention steel
    I1 FH 580 8 86 240 NOX503F 980 0 Present invention steel
    J1 FH 550 9 90 80 NOX503F 1180 2 Present invention steel
    K1 FH 570 8 84 160 NOX503F 630 1 Present invention steel
    L1 FH 590 9 88 220 NOX503F 940 0 Present invention steel
    M1 FH 600 6 90 200 NOX503F 430 1 Present invention steel
    N1 FH 590 8 83 200 NOX503F 570 1 Present invention steel
    N2 FH 560 8 89 80 NOX503F 690 1 Present invention steel
    N3 FH 550 11 92 70 NOX503F 700 1 Present invention steel
    N4 FH 000 10 94 120 NOX503F 800 1 Present invention steel
    N5 FH 520 7 82 18 NOX503F 760 1 Comparative steel
    N6 FH 530 7 83 26 NOX503F 80 1 Comparative steel
    N7 FH 590 8 86 210 NOX503F - 0 Comparative steel
    N8 FH 570 9 87 190 NOX504F 3560 6 Comparative steel
    N9 FH 600 9 92 200 NOX503F 4320 Comparative steel
    N10 FH 590 8 88 240 NOX503F 7 Comparative steel
    O1 HR 590 8 94 240 NOX503F 1220 2 Present invention steel
    P1 OR 580 7 86 200 NOX503F 890 1 Present invention steel
    Q1 FH 580 9 86 180 NOX503F 800 1 Present invention steel
    R1 HR 590 8 83 200 NOX503F 1370 3 Present invention steel
    S1 FH 560 9 89 200 NOX503F 680 1 Present invention steel
    a1 FH 590 8 85 240 NOX503F 590 1 Comparative steel
    b1 -*2 -*2 -*2 -*2 -*2 -*2 -*2 -*2 Comparative steel
    c1 FH 560 8 84 240 NOX503F 1260 2 Comparative steel
    d1 FH 480 7 86 18 NOX503F 2450 2 Comparative steel
    e1 FH 570 9 90 270 NOX503F 990 1 Comparative steel
    f1 -*2 -*2 -*2 -*2 -*2 -*2 -*2 -*2 Comparative steel
    g1 FH 580 0.013 8 88 210 NOX503F 1210 1 Comparative steel
    h1 FH 560 8 92 180 NOX503F 1040 0 Comparative steel
    i1 FH 590 7 89 220 NOX503F 1300 1 Comparative steel
    j1 FH 570 8 88 200 NOX503F 1230 2 Comparative steel
    k1 FH 640 8 85 190 NOX503F 840 1 Comparative steel
    n FH 610 9 82 80 NOX503F 900 2 Comparative steel
    m1 FH 560 9 93 280 NOX503F 1000 1 Comparative steel
    n1 FH 560 9 86 180 NOX503F 570 1 Comparative steel
    * 1 means that FH: left as cold rolled, HR: hot-rolled steel sheet, and CR: cold-rolled steel sheet annealed after cold rolling.
    *2 means that Mn is excessively high many fractures occur in casting and hot rolling time, and no hot-rolled steel sheet was able to be produced.
  • The finished sheet thickness of the hot-rolled steel sheet provided for hot stamping as the hot-rolled steel sheet was made 1.6 mm. The sheet thickness of the hot-rolled steel sheet provided for cold rolling was made 3.2 mm. When pickling was carried out under the conditions in Table 2 thereafter, and cold rolling was performed, the sheet thickness was made 50% (3.2 mm → 1.6 mm). Thereafter, annealing was performed for some of the steel sheets in a continuous annealing facility, and the steel sheets were made into cold-rolled steel sheets. Thereafter, by using NOX-RUST503F (made by PARKER INDUSTRIES, INC.), NOX503F (made by PARKER INDUSTRIES, INC.) was applied to the hot-rolled steel sheets and the cold-rolled steel sheets by an electrostatic oiling machine, in a range of no coating oil to 6090 mg/m2.
  • Thereafter, the steel sheets were cut into a predetermined size, after which, electrical heating was performed to 900°C at 50°C/second, retention for 10 seconds at 900°C was carried out, thereafter, standing to cool for 10 seconds was performed, and hardening was performed in the above described hot shallow drawing dies at a temperature of 650°C or higher. Visual observation of the obtained hot stamp formed bodies was performed, and the steel sheets without detachment of scale were determined as the steel sheets excellent in scale adhesion.
  • Concerting the rust inhibition property, retention for 30 days was carried out at a room temperature, and the steel sheets with no rust generated on the steel sheet surfaces were defined as the steel sheets excellent in rust inhibition property. In combination, with use of flat sheet test pieces, hot stamping was performed under the aforementioned conditions, and tensile characteristics were evaluated. The evaluation result is shown in Table 3.
    • [Table 3]
  • Table.3
    Steel number Steel grade*1 Rz (µm) Scale thickness (µm) Irregularities in scale/base iron interface Scale detached area (%) Scale adhesion Presence or absence of rust generation TS of formed body(MPa) Remarks
    A1 FH 3.7 4 6 0 ○ Presence 1555 Comparative steel
    A2 FH 3.6 5 5 0 ○ Absence 1562 Present invention steel
    A3 FH 4.0 4 8 0 ○ Absence 1560 Present invention steel
    A4 FH 4.4 5 8 0 ○ Absence 1559 Present invention steel
    A5 FH 4.2 4 6 0 ○ Absence 1555 Present invention steel
    A6 FH 4.5 6 8 0 ○ Absence 1550 Present invention steel
    A7 FH 3.8 6 7 0 ○ Absence 1557 Present invention steel
    A8 FH 2.6 5 4 3 ○ Absence 1562 Present invention steel
    A9 FH 2.2 2 0 11 Δ Absence 1562 Comparative steel
    A10 FH 1.9 3 1 16 × Absence 1554 Comparative steel
    A11 FH 2.4 2 2 8 Δ Absence 1564 Comparative steel
    A12 FH 4.8 12 7 14 Δ Absence 1549 Comparative steel
    A13 FH 2.6 14 4 26 × Absence 1556 Comparative steel
    A14 FH 3.9 15 8 44 × Absence 1560 Comparative steel
    A15 FH 3.6 18 7 68 × Absence 1567 Comparative steel
    B1 HR 5.8 4 13 0 ○ Absence 1549 Present invention steel
    C1 CR 4.1 4 6 0 ○ Absence 1483 Present invention steel
    D1 FH 3.7 3 5 0 ○ Absence 1529 Present invention steel
    E1 FH 3.8 3 8 0 ○ Absence 1550 Present invention steel
    F1 FH 3.7 7 7 0 ○ Absence 1625 Present invention steel
    G1 FH 4.5 4 8 0 ○ Absence 1572 Present invention steel
    H1 FH 4.6 4 6 0 ○ Absence 1645 Present invention steel
    n FH 4.4 5 6 0 ○ Absence 1687 Present invention steel
    J1 FH 3.8 5 8 0 ○ Absence 1639 Present invention steel
    K1 FH 4.0 3 7 0 ○ Absence 1752 Present invention steel
    L1 FH 4.5 4 8 0 ○ Absence 1624 Present invention steel
    M1 FH 4.3 4 7 0 ○ Absence 1715 Present invention steel
    N1 FH 4.4 4 7 0 ○ Absence 1834 Present invention steel
    N2 FH 3.9 3 6 0 ○ Absence 1828 Present invention steel
    N3 FH 32 3 5 0 ○ Absence 1833 Present invention steel
    N4 FH 4.5 4 10 0 ○ Absence 1829 Present invention steel
    N5 FH 2.3 2 0 9 Δ Absence 1830 Comparative steel
    N6 FH 1.8 3 1 13 Δ Absence 1826 Comparative steel
    N7 FH 3.9 4 8 0 ○ Presence 1834 Comparative steel
    N8 FH 4.6 13 8 39 × Absence 1823 Comparative steel
    N9 FH 4.3 13 7 47 × Absence 1835 Comparative steel
    N10 FH 4.5 21 8 45 × Absence 1830 Comparative steel
    O1 HR 5.3 4 13 0 ○ Absence 1854 Present invention steel
    P1 OR 4.4 4 8 0 ○ Absence 1847 Present invention steel
    Q1 FH 4.7 4 9 0 ○ Absence 2108 Present invention steel
    R1 HR 6.0 4 12 0 ○ Absence 2138 Present invention steel
    S1 FH 3.9 3 7 0 ○ Absence 2505 Present invention steel
    a1 FH 4.3 4 8 0 ○ Absence 1064 Comparative steel
    b1 FH -*2 -*2 -*2 -*2 -*2 -*2 ->1<2 Comparative steel
    c1 FH 2.4 16 0 89 X Absence 1483 Comparative steel
    d1 FH 1.8 1 0 84 X Absence 1598 Comparative steel
    e1 FH 3.8 4 9 0 ○ Absence 987 Comparative steel
    f1 FH -*2 -*2 -*2 -*2 -*2 -*2 -*2 1604 Comparative steel
    g1 FH 4.3 5 9 92 × Absence 1604 Comparative steel
    h1 FH 4.1 4 9 0 ○ Absence 1156 Comparative steel
    i1 FH 4.0 5 7 0 ○ Absence 1095 Comparative steel
    j1 FH 4.6 4 7 0 ○ Absence 1023 Comparative steel
    k1 FH 4.4 7 11 0 ○ Absence 1154 Comparative steel
    l1 FH 4.1 5 9 0 ○ Absence 1072 Comparative steel
    m1 FH 3.9 4 5 0 ○ Absence -*3 Comparative steel
    n1 FH 45 4 7 0 ○ Absence 1008 Comparative steel
    *1 means that FH: left as cold rolled, HR: hot-rolled steel sheet, and CR: cold-rolled steel sheet annealed after cold rolling.
    *2 means that Mn was excessively high, many fractures occurred in casting and hot rolling time, and no hot-rolled steel sheet was able to be produced.
    *3 means that at the time of hot stemping, a feature with the enclosure as the starting point occurred, and the tenslie test was not be able to be carried out with the formed
  • As for the tensile characteristics, the tensile test pieces which were in conformity with JIS Z 2201 were extracted, the tensile test was performed in conformity with JIS Z 2241, and the maximum tensile strength was measured. The formed bodies having the maximum tensile strength of 1180 MPa or more were determined as the formed bodies of the present invention.
  • Composition analyses of the scales of the formed bodies were carried out by X-ray diffraction by cutting out sheets from the bottoms of the cylindrical portions of the shallow drawing test pieces. From the peak strength ratios of the respective oxides, the volume ratios of the respective Fe oxides were measured. The Si oxides were present very thinly and the volume ratio was less than 1%, and thus quantitative evaluation by X-ray diffraction was difficult. However, it could be confirmed that the Si oxides were present in the interface between the scale and the base iron by the line analysis of EPMA.
  • As for evaluation of the irregularities in the interfaces of the scales and the base irons formed in the formed bodies, embedded polishing was carried out for the steel sheets cut out from the above described position, and thereafter, SEM observation was performed by power of 3000 from the section perpendicular to the rolling direction. Five visual fields were observed in each of the test pieces, and the number density of the irregularities in the range of 0.2 µm to 1.0 µm per length of 100 µm was measured.
  • The formed bodies satisfying the conditions of the present invention were able to make excellent rust inhibition properties and excellent scale adhesion compatible. The formed bodies that do not satisfy the conditions of the invention were inferior in scale adhesion, or inferior in corrosion resistance.
    • INDUSTRIAL APPLICABILITY
  • According to the present invention, the steel sheet excellent in scale adhesion at the time of hot stamping can be provided, the problems of wear and tear of the die at the time of hot stamping, plating adhesion to the die, and indentation flaws accompanying it can be solved, and thus the present invention can bring about significant enhancement in productivity, and has an industrially large value.

Claims (15)

  1. A steel sheet for hot stamping, comprising a composition containing:
    in mass%,
    C: 0.100% to 0.600%;
    Si: 0.50% to 3.00%;
    Mn: 1.20% to 4.00%;
    Ti: 0.005% to 0.100%;
    B: 0.0005% to 0.0100%;
    P: 0.100% or less;
    S: 0.0001% to 0.0100%;
    Al: 0.005% to 1.000%;
    N: 0.0100% or less;
    Ni: 0% to 2.00%;
    Cu: 0% to 2.00%;
    Cr: 0% to 2.00%;
    Mo: 0% to 2.00%;
    Nb: 0% to 0.100%;
    V: 0% to 0.100%;
    W: 0% to 0.100%, and
    a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
    with a balance being Fe and impurities,
    wherein surface roughness of the steel sheet satisfies Rz>2.5 µm, and coating oil in an amount of 50 mg/m2 to 1500 mg/m2 is applied onto a surface.
  2. The steel sheet for hot stamping according to claim 1,
    wherein an amount of S contained in the coating oil which is applied onto the steel sheet is 5% or less in mass%.
  3. The steel sheet for hot stamping according to claim 1 or 2,
    wherein the composition of the steel sheet contains, in mass%,
    one kind or two or more kinds selected from a group consisting of
    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%.
  4. The steel sheet for hot stamping according to any one of claims 1 to 3,
    wherein the composition of the steel sheet contains, in mass %,
    a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
  5. A method for producing a steel sheet for hot stamping, comprising:
    a step of casting a slab containing,
    in mass%,
    C: 0.100% to 0.600%;
    Si: 0.50% to 3.00%;
    Mn: 1.20% to 4.00%;
    Ti: 0.005% to 0.100%;
    B: 0.0005% to 0.0100%;
    P: 0.100% or less;
    S: 0.0001% to 0.0100%;
    Al: 0.005% to 1.000%;
    N: 0.0100% or less;
    Ni: 0% to 2.00%;
    Cu: 0% to 2.00%;
    Cr: 0% to 2.00%;
    Mo: 0% to 2.00%;
    Nb: 0% to 0.100%;
    V: 0% to 0.100%;
    W: 0% to 0.100%, and
    a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
    with a balance being Fe and impurities, and hot rolling the slab directly or by allowing the slab to cool and heating the slab to obtain a hot-rolled steel sheet;
    a step of pickling the hot-rolled steel sheet for 30 seconds or more in an aqueous solution having a temperature of 80°C to lower than 100°C and including an inhibitor with a concentration of an acid being 3 mass% to 20 mass%; and
    a step of applying a rust inhibiting oil to the steel sheet after carrying out the pickling,
    wherein a rust inhibiting oil remaining amount on a steel sheet surface is limited to 50 mg/m2 to 1500 mg/m2.
  6. The method for producing a steel sheet for hot stamping according to claim 5,
    wherein the rust inhibiting oil is applied to the hot-rolled steel sheet which has been pickled.
  7. The method for producing a steel sheet for hot stamping according to claim 5, further comprising:
    a step of cold rolling the hot-rolled steel sheet which has been pickled to obtain a cold-rolled steel sheet,
    wherein the rust inhibiting oil is applied to the cold-rolled steel sheet.
  8. The method for producing a steel sheet for hot stamping according to claim 5, further comprising:
    a step of cold rolling the hot-rolled steel sheet which has been pickled, and further performing thermal treatment in a continuous annealing facility or a box type annealing furnace to obtain a cold-rolled steel sheet,
    wherein the rust inhibiting oil is applied to the cold-rolled steel sheet.
  9. The method for producing a steel sheet for hot stamping according to any one of claims 5 to 8,
    wherein an amount of S in the rust inhibiting oil that is applied to the steel sheet is 5% or less in mass%.
  10. The method for producing a steel sheet for hot stamping according to any one of claims 5 to 9,
    wherein a composition of the slab contains, in mass%,
    one kind or two or more kinds selected from a group consisting of
    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%.
  11. The method for producing a steel sheet for hot stamping according to any one of claims 5 to 10,
    wherein a composition of the slab contains, in mass %,
    a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
  12. A hot stamp formed body, comprising a composition containing:
    in mass%,
    C: 0.100% to 0.600%;
    Si: 0.50% to 3.00%;
    Mn: 1.20% to 4.00%;
    Ti: 0.005% to 0.100%;
    B: 0.0005% to 0.0100%;
    P: 0.100% or less;
    S: 0.0001% to 0.0100%;
    Al: 0.005% to 1.000%;
    N: 0.0100% or less;
    Ni: 0% to 2.00%;
    Cu: 0% to 2.00%;
    Cr: 0% to 2.00%;
    Mo: 0% to 2.00%;
    Nb: 0% to 0.100%;
    V: 0% to 0.100%;
    W: 0% to 0.100%, and
    a total of one kind or two or more kinds selected from a group consisting of REM, Ca, Ce and Mg: 0% to 0.0300%,
    with a balance being Fe and impurities,
    wherein three or more irregularities in a range of 0.2 µm to 8.0 µm in depth are present per 100 µm in an interface between scale and a base iron, and tensile strength is 1180 MPa or more.
  13. The hot stamp formed body according to claim 12,
    wherein an Si oxide, FeO, Fe3O4 and Fe2O3 are included in a surface of the hot stamp formed body, and a thickness of the scale is 10 µm or less.
  14. The hot stamp formed body according to claim 12 or 13,
    wherein the composition of the hot stamp formed body contains, in mass%,
    one kind or two or more kinds selected from a group consisting of
    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%.
  15. The hot stamp formed body according to any one of claims 12 to 14,
    wherein the composition of the hot stamp formed body contains, in mass %,
    a total of 0.0003% to 0.0300% of one kind or two or more kinds selected from the group consisting of REM, Ca, Ce and Mg.
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RU2683397C1 (en) 2019-03-28
JPWO2016158961A1 (en) 2018-01-18
TW201702403A (en) 2017-01-16
CA2979978A1 (en) 2016-10-06
KR102000863B1 (en) 2019-07-16
CN107427889A (en) 2017-12-01
EP3278895B1 (en) 2020-03-11
EP3278895A4 (en) 2018-09-05
BR112017020165A2 (en) 2018-06-05
KR20170122823A (en) 2017-11-06
JP6515356B2 (en) 2019-05-22
US20180044754A1 (en) 2018-02-15
ES2781465T3 (en) 2020-09-02
WO2016158961A1 (en) 2016-10-06

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