WO2016047058A1 - 熱間プレス成形品の製造方法および熱間プレス成形品 - Google Patents

熱間プレス成形品の製造方法および熱間プレス成形品 Download PDF

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WO2016047058A1
WO2016047058A1 PCT/JP2015/004533 JP2015004533W WO2016047058A1 WO 2016047058 A1 WO2016047058 A1 WO 2016047058A1 JP 2015004533 W JP2015004533 W JP 2015004533W WO 2016047058 A1 WO2016047058 A1 WO 2016047058A1
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Prior art keywords
steel sheet
press
cooling
treated steel
hot press
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PCT/JP2015/004533
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English (en)
French (fr)
Japanese (ja)
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WO2016047058A8 (ja
Inventor
達也 中垣内
裕一 時田
簑手　徹
玉井　良清
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to US15/502,614 priority Critical patent/US20170225215A1/en
Priority to EP15843885.3A priority patent/EP3199257B1/de
Priority to KR1020177005467A priority patent/KR20170036086A/ko
Priority to CN201580049874.9A priority patent/CN106714996B/zh
Priority to MX2017003875A priority patent/MX2017003875A/es
Publication of WO2016047058A1 publication Critical patent/WO2016047058A1/ja
Publication of WO2016047058A8 publication Critical patent/WO2016047058A8/ja

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    • 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
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing 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
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/201—Work-pieces; preparation of the work-pieces, e.g. lubricating, coating
    • 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
    • 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
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • 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
    • C22C38/02—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • 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
    • C23F17/00—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
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/56—Electroplating: Baths therefor from solutions of alloys
    • C25D3/565—Electroplating: Baths therefor from solutions of alloys containing more than 50% by weight of zinc
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces

Definitions

  • the present invention relates to a hot press-formed product and a method for producing the same, and in particular, when press-forming a pre-heated surface-treated steel sheet, it is possible to obtain a predetermined strength (tensile strength: 1180 MPa class or more) by quenching simultaneously with shape formation.
  • the present invention relates to a method for producing a hot press-formed product.
  • the present invention also relates to a hot press-formed product manufactured according to the above-described method for manufacturing a hot press-formed product.
  • Patent Document 1 discloses that when a blank plate (steel plate) heated to an austenite single phase region around 900 ° C. is subjected to hot press forming to produce a member having a predetermined shape, There has been proposed a technique for increasing the strength of a member by quenching.
  • Patent Document 1 Although excellent corrosion resistance is required for the undercarriage member and the vehicle body structural member of an automobile, the technology proposed in Patent Document 1 does not provide a rust preventive film such as a plating layer on the material steel plate. For this reason, the hot press-formed member obtained according to this technique has insufficient corrosion resistance.
  • a hot press molding technique that can suppress the formation of oxide scale during heating before hot press molding and can improve the corrosion resistance of members after hot press molding.
  • a surface-treated steel sheet provided with a coating such as a plating layer on the surface and a hot press forming method using the surface-treated steel sheet have been proposed.
  • a steel sheet coated with Zn or a Zn base alloy is heated to 700 to 1200 ° C. and then hot pressed to form a Zn—Fe base compound or a Zn—Fe—Al base on the surface.
  • a technique for forming a hot press-formed member provided with a compound has been proposed.
  • Patent Document 2 by using a steel sheet coated with Zn or a Zn base alloy, it becomes possible to suppress the oxidation of the steel sheet surface, which becomes a problem during heating before hot press forming, and has excellent corrosion resistance. Further, it is described that a hot press-formed member is obtained.
  • Patent Document 3 a surface-treated steel sheet in which a Zn-Fe-based plating layer is formed on the surface of the base steel sheet, the surface-treated steel sheet is brought to a temperature not lower than the Ac 1 transformation point of the base steel sheet and not higher than 950 ° C.
  • a method of starting press forming after heating and cooling the surface-treated steel sheet to a temperature below the freezing point of the plating layer has been proposed.
  • Patent Document 3 describes that liquid metal embrittlement cracking can be suppressed by starting press forming after cooling the surface-treated steel sheet to a temperature below the freezing point of the plating layer.
  • liquid metal embrittlement cracking occurs, that is, occurs on the surface of a hot press-formed member, and the depth from the plating layer-base steel plate (base metal) interface to the inside of the base steel plate is 100 ⁇ m. It is considered that cracks in which Zn is detected at the interface of the cracked portion (hereinafter referred to as “macro crack”) can be suppressed.
  • macro crack cracks in which Zn is detected at the interface of the cracked portion
  • the present inventors examined the use of Zn—Ni alloy plating containing about 9 to 25% Ni in Zn as a high melting point plating layer. In order to ensure the corrosion resistance of Zn-Ni alloy plating, it is necessary to use Zn-Ni alloy as the ⁇ phase.
  • the ⁇ phase present in the equilibrium diagram of the Zn-Ni alloy has a melting point of 860 ° C or higher and becomes a normal Zn-based plating layer. It is very high compared to the above, and the occurrence of macro cracks can be suppressed even under normal pressing conditions.
  • the depth from the plating layer-base steel plate interface to the base steel plate inside is not more than about 30 ⁇ m instead of the macro cracks described above, and Zn is present at the crack interface. It is known that microcracks that are not detected occur.
  • This microcrack is called a microcrack, penetrates the plating layer-base steel plate interface and reaches the inside of the base steel plate, and adversely affects various properties (such as fatigue resistance) of the hot press-formed member.
  • macro cracks also occur in a portion where only tensile strain occurs, such as the punch contact side of the die shoulder R portion.
  • microcracks do not occur in such portions, but occur in places where tensile strain is applied after (bending) compression (bending back) as in the die contact side of the vertical wall. For this reason, it is guessed that the generation mechanism differs between a macro crack and a micro crack.
  • the present invention has been made to solve such a problem.
  • a hot-pressed product is manufactured by hot-pressing a surface-treated steel sheet on which a Zn-Ni-based plating layer has been formed, It aims at providing the manufacturing method of the hot press-molded article which suppresses generation
  • an object of the present invention is to provide a hot press-formed product manufactured according to the above-described method for manufacturing a hot press-formed product.
  • microcracks which are problematic when hot-pressing a Zn-based plated steel sheet.
  • the generation mechanism of microcracks is not clear, but microcracks are generated on the surface of plated steel sheets by press-forming Zn-based plated steel sheets at a high temperature below the freezing point of plating.
  • similar microcracking occurs when a Zn-Ni plated steel sheet is press-formed.
  • the micro crack is a micro crack having a depth of about 30 ⁇ m from the plating layer-base steel plate interface and penetrates through the plating layer-base steel plate interface to the inside of the base steel plate.
  • micro-cracks do not occur only by simple tension, compression deformation and bending deformation, but micro-cracks occur in the portion subjected to bending-bending unbending deformation, where the once bent portion is stretched again.
  • the processing as described above may be limited to a specific portion, but depending on the shape of the molded product, the portion subjected to processing that generates microcracks may be widely spread on the steel sheet.
  • the surface-treated steel sheet is 550 ° C. or lower and 410 ° C. or higher at a cooling rate of 100 ° C./s or higher.
  • the reason why the shape accuracy defect is suppressed by cooling with the cooling mold is considered as follows. That is, as a typical defective shape accuracy of the hat-shaped member, the angle change between the two surfaces sandwiching the bending ridge line is larger than the mold angle, and the surface of the vertical wall portion has a curvature. Wall warping that becomes. These are all caused by the difference in stress distribution in the thickness direction, and the higher the flow stress of the steel sheet during processing, the greater the difference in stress distribution and the lower the shape accuracy. That is, in hot press forming, the lower the press forming temperature, the higher the flow stress during press forming of the steel sheet and the lower the shape accuracy.
  • the temperature of the steel sheet at the time of press forming is lowered by cooling and the shape accuracy is lowered, it is cooled to a temperature of 550 ° C or lower and 410 ° C or higher at a cooling rate of 100 ° C / s or higher, within 5 seconds after cooling, and
  • a cooling rate 100 ° C / s or higher
  • press forming was started within the range where the steel plate temperature was 550 ° C. or lower and 400 ° C. or higher, almost no decrease in shape accuracy was observed.
  • the reason for this is that when the heated steel sheet is quenched with a cooling die and the steel sheet temperature is press-formed within a range of 550 ° C. or lower and 400 ° C. or higher, the steel sheet structure at the time of press forming is austenite.
  • a method for producing a hot press-formed product in which a hot-pressed product is produced by subjecting a surface-treated steel sheet having a Zn-Ni plating layer formed on the surface of a base steel plate to hot press, Heating the surface-treated steel sheet to a temperature range of 1000 ° C. or less above the Ac 3 transformation point;
  • the surface-treated steel sheet is 550 ° C. or lower and 410 ° C. or higher at a cooling rate of 100 ° C./s or higher. Cooling to temperature, Within 5 seconds after the cooling, and the temperature of the surface-treated steel sheet is within a range of 550 ° C.
  • press molding of the surface-treated steel sheet is started using a press molding die to obtain a molded body Process
  • a method of manufacturing a hot press-molded product comprising: holding the molded body at a bottom dead center while being sandwiched between the press-molding dies, and quenching the molded body to obtain a hot press-molded product.
  • microcracks do not occur on the entire front and back surfaces, the hardness of the molded product is sufficient, there is no significant increase in molding load, and there is no problem with shape freezing properties. Since a hot press-formed product can be obtained, it becomes possible to manufacture automobile parts and the like having various product shapes using a high-strength surface-treated steel sheet.
  • the method for producing a hot press-formed product according to an embodiment of the present invention is performed by hot-pressing a surface-treated steel sheet 1 having a Zn-Ni plating layer formed on the surface of a base steel sheet as shown in FIG.
  • a method for producing a hot press-formed product for producing an intermediate press-formed product comprising a heating step (not shown) for heating the surface-treated steel sheet 1 to a temperature range not lower than the Ac 3 transformation point and not higher than 1000 ° C.
  • the cooling process (S1) for cooling to the surface, and the press of the surface-treated steel sheet 1 using the press mold 11 within 5 seconds after the cooling and the temperature of the surface-treated steel sheet 1 is in the range of 550 ° C. or lower and 400 ° C. or higher.
  • the material of the hot press-formed product, the heating step, the cooling step (S1), the press forming step (S2), and the quenching step (S3) will be described in detail.
  • a surface-treated steel sheet in which a Zn—Ni plating layer is provided on the surface of the base steel sheet is used.
  • the method for forming the Zn—Ni plating layer on the surface of the base steel plate is not particularly limited, and any method such as hot dipping or electroplating may be used.
  • the amount of plating is preferably 10 g / m 2 or more and 90 g / m 2 or less per side.
  • the Ni content in the plating layer is preferably 9% by mass or more and 25% by mass or less.
  • the surface-treated steel sheet 1 is heated to a temperature range from the Ac 3 transformation point to 1000 ° C.
  • the heating temperature of the surface-treated steel sheet 1 is lower than the Ac 3 transformation point, an adequate amount of austenite cannot be obtained during heating, and sufficient strength is obtained after hot press forming due to the presence of ferrite during press forming. It is difficult to ensure good shape freezing property.
  • the heating temperature of the surface-treated steel sheet 1 exceeds 1000 ° C., the oxidation resistance and the corrosion resistance of the hot press-formed product are deteriorated due to evaporation of the plating layer and excessive generation of oxide at the surface layer portion. Therefore, the heating temperature is set to the Ac 3 transformation point or higher and 1000 ° C. or lower.
  • the heating method of the surface-treated steel sheet 1 is not particularly limited, and any method such as heating with an electric furnace, an induction heating furnace, or a direct current heating furnace may be used.
  • the cooling step (S1) is a step in which the heated surface-treated steel sheet 1 is sandwiched between cooling dies 3 and cooled to a temperature of 550 ° C. or lower and 410 ° C. or higher at a cooling rate of 100 ° C./s or higher.
  • the cooling mold 3 includes an upper mold 5 and a lower mold 7 whose contact surfaces with the surface-treated steel sheet 1 are flat, and the lower mold 7 is extended and contracted.
  • a lifter pin 9 of the type is installed. The heated surface-treated steel sheet 1 is placed on the lifter pin 9 and then cooled by being sandwiched between the upper mold 5 and the lower mold 7.
  • the heated surface-treated steel sheet 1 is sandwiched between the cooling molds 3, basically, the entire surface of the surface-treated steel sheet 1 is sandwiched between the cooling molds 3 as shown in FIG. However, the portion that is trimmed before the final product may be protruded from the cooling mold 3. Thereby, even if the part that undergoes processing that generates microcracks, that is, the part that undergoes bending-bending unreformation extends widely to the surface-treated steel sheet 1 that is the workpiece, the final press forming is obtained. It is possible to suppress the occurrence of microcracks over the entire front and back surfaces of the product.
  • the timing for sandwiching the heated surface-treated steel sheet 1 with the cooling mold 3 is preferably set to 800 ° C.
  • the temperature it is preferable to set the temperature to 670 ° C. or higher. Further, the cooling mold 3 may be pressed against one side surface of the surface-treated steel sheet 1 to be cooled.
  • FIG. 2 is a schematic diagram showing the relationship between a general metal structure, temperature, and cooling time when hot pressing a steel sheet using a press mold.
  • FIG. 2A shows a case where the press molding start temperature is high. In this case, after the press molding is started, the mold is rapidly cooled by heat removal from the mold to form a martensite single phase structure.
  • FIG. 2B when the press molding start temperature is low, ferrite and bainite are generated before the press molding starts, and the strength of the press molded product after press molding is lowered.
  • the reason why the cooling stop temperature in this cooling step is set to 550 ° C. or less is that if it exceeds 550 ° C., cooling becomes insufficient and micro cracks are generated after hot press forming. Preferably it is 500 degrees C or less.
  • the lower limit of the cooling stop temperature is set to 410 ° C., if the temperature is lower than 410 ° C., the surface-treated steel sheet 1 is excessively cooled before press forming, and the shape freezing property after press forming is lowered. Preferably it is 430 ° C or more.
  • the cooling rate and cooling stop temperature in this cooling step can be controlled by, for example, the time that the surface-treated steel sheet 1 is held by the cooling mold 3 (see FIG. 1).
  • the temperature change of the surface-treated steel sheet 1 by sandwiching the surface-treated steel sheet 1 with the cooling mold 3 is measured by inserting a 0.5 mm ⁇ sheath thermocouple 19 into the steel sheet shown in FIG. Can be obtained.
  • FIG. 5 is a graph showing an example of the result.
  • the vertical axis represents temperature (° C.) and the horizontal axis represents time (s).
  • FIG. 6 is a graph showing an enlarged horizontal axis of a portion surrounded by a broken line in FIG. As shown in FIG. 6, the temperature change during cooling by the cooling mold is about 160 ° C./s, and it can be seen that rapid cooling is possible.
  • a press-molded product was manufactured by changing the holding time in the cooling mold (particularly the cooling stop temperature by the cooling mold) and the press-molding start temperature described later in various ways.
  • evaluation items observe the cross section of the vertical wall of the press-molded product to confirm the presence or absence of microcracks, confirm the hardness of the molded product, confirm the press-molding load, and open the hat of the molded product.
  • the shape freezing property is confirmed by confirming the opening amount of the part (the difference between the width dimension of the opening part released after molding and the width of the molded product in the mold shape).
  • FIG. 7 shows the side of the vertical wall portion of the press-molded product in contact with the die 13 when the cooling time in the cooling die (cooling stop temperature by the cooling die) and the press molding start temperature are variously changed. It is a SEM image of a section of a surface layer. From FIG. 7, it can be seen that when the cooling time in the cooling mold is 0.9 s or more (press forming start temperature 550 ° C. or less), microcracks are not recognized in the base steel sheet. Moreover, it was confirmed that Hv> 450 under all conditions and there was no deterioration in hardenability.
  • FIG. 8 is a diagram showing the relationship between the press molding start temperature and the press molding load, where the vertical axis represents the press molding load (kN) and the horizontal axis represents the press molding start temperature (° C.).
  • the press molding load increases as the press molding start temperature decreases due to cooling in the cooling mold before press molding, but mild steel (at a temperature of about 550 ° C. at which generation of microcracks is eliminated. 270D, cold draw forming), which is equivalent to the press forming load.
  • FIG. 9 is a diagram showing the relationship between the press molding start temperature and the opening amount, where the vertical axis represents the opening amount (mm) of the molded product, and the horizontal axis represents the press molding start temperature (° C.).
  • the amount of opening increases as the press molding start temperature decreases due to cooling in the cooling mold before press molding, and the shape freezeability tends to decrease. There is almost no decrease in shape freezing property until the molding start temperature is 400 ° C.
  • the surface-treated steel sheet is cooled to a temperature of 550 ° C. or lower and 410 ° C. or higher at a cooling rate of 100 ° C./s or higher.
  • the press forming step (S2) is a step of press forming the surface-treated steel sheet 1 into a product shape.
  • the press molding process is performed by the press molding die 11 after the cooling process.
  • the press molding die 11 includes a die 13 and a punch 17 as shown in FIG. Then, press-molding is performed by sandwiching the surface-treated steel sheet 1 between the die 13 and the punch 17 to obtain a molded body 1 ′.
  • the surface-treated steel sheet 1 is cooled to a temperature of 550 ° C. or lower and 410 ° C. or higher using the cooling die 3 at a cooling rate of 100 ° C./s or higher.
  • press forming with sufficient hardness and shape freezing property without increasing micro-cracking without increasing the press forming load.
  • the product can be manufactured.
  • the press molding process starts within 5 seconds after the cooling process. If the time until the press molding starts after cooling exceeds 5 seconds, ferrite, bainite, etc. are generated before the press molding starts.
  • the time until the start of press molding after cooling is preferably within 3 seconds.
  • the lower limit is not particularly limited, but it is usually preferably 1 second or longer.
  • the press molding method is not particularly limited. As shown in FIG. 10 (a), draw forming is performed with the die 13 and the blank holder 15 sandwiching the surface-treated steel sheet 1, or is the blank holder 15 lowered as shown in FIG. 10 (b)? Alternatively, it is possible to perform foam molding that performs molding without using the blank holder 15. From the viewpoint of suppressing microcracks, foam molding is preferable because the degree of processing of the vertical wall portion of the press-molded product is small.
  • the quenching step (S3) is a step of obtaining a hot press-molded product by holding the molded body 1 'while being sandwiched between the press-molding dies 11 and then quenching the molded body 1'.
  • the slide is stopped at the bottom dead center of the molding after the press molding.
  • the stop time varies depending on the amount of heat removed by the mold, but is preferably 3 seconds or more.
  • the upper limit of the stop time is not particularly limited, but is preferably 20 seconds or less from the viewpoint of productivity.
  • the hot-rolled steel sheet or the cold-rolled steel having a composition composed of Fe and inevitable impurities as the balance A steel plate can be used.
  • this component composition is demonstrated.
  • “%” indicating the content of a component means “% by mass” unless otherwise specified.
  • ⁇ C 0.15% to 0.50% ⁇ C is an element for improving the strength of the steel, and the amount is preferably 0.15% or more in order to increase the strength of the hot press-formed product.
  • the C content is preferably 0.15% or more and 0.50% or less, and more preferably 0.20% or more and 0.40% or less.
  • Si 0.05% or more and 2.00% or less
  • Si is an element that improves the strength of steel, and the amount is preferably 0.05% or more in order to increase the strength of a hot press-formed product.
  • the Si content is preferably 0.05% or more and 2.00% or less, and more preferably 0.10% or more and 1.50% or less.
  • Mn is an element that enhances the hardenability of steel, and is an effective element for improving the hardenability by suppressing the ferrite transformation of the base steel sheet during the cooling process after hot press forming. Further, Mn is an element effective for lowering the heating temperature of the surface-treated steel sheet 1 before hot press forming because it has an action of lowering the Ac 3 transformation point. In order to exhibit such an effect, the Mn content is preferably 0.50% or more. On the other hand, when the amount of Mn exceeds 3.00%, Mn is segregated and the uniformity of the properties of the base steel sheet and the hot press-formed member decreases. Therefore, the Mn content is preferably 0.50% or more and 3.00% or less, and more preferably 0.75% or more and 2.50% or less.
  • the P content is preferably 0.10% or less, and more preferably 0.01% or less.
  • P is preferably 0.003% or more.
  • S is an element that combines with Mn to form coarse sulfides and causes a reduction in the ductility of the steel. Therefore, it is preferable to reduce the S content as much as possible, but it is acceptable up to 0.050%. Therefore, the S content is preferably 0.050% or less, and more preferably 0.010% or less. However, excessive S reduction leads to an increase in desulfurization cost in the steel making process. Therefore, S is preferably 0.0005% or more.
  • the Al content is preferably 0.10% or less, and more preferably 0.07% or less.
  • Al has an action as a deoxidizing material, and from the viewpoint of improving the cleanliness of steel, the content is preferably 0.01% or more.
  • N 0.010% or less>
  • a nitride such as AlN is formed in the base steel sheet, resulting in a decrease in formability during hot press forming. Therefore, the N content is preferably 0.010% or less, and more preferably 0.005% or less.
  • N is preferably 0.001% or more.
  • this base steel plate may contain the following elements further as needed.
  • Cr 0.01% or more and 0.50% or less
  • V 0.01% or more and 0.50% or less
  • Mo 0.01% or more and 0.50% or less
  • Ni 0.01 or more and 0.50% or less
  • Cr, V, Mo and Ni are all It is an effective element for improving the hardenability of steel. This effect can be obtained by setting the content to 0.01% or more for any element. However, if the Cr, V, Mo, and Ni content exceeds 0.50%, the above effect is saturated, which increases the cost. Accordingly, when containing one or more of Cr, V, Mo, Ni, the content is preferably 0.01% or more and 0.50% or less, more preferably 0.10% or more and 0.40% or less. .
  • Ti 0.01% or more and 0.20% or less Ti is effective for strengthening steel.
  • the strength increasing effect by Ti can be obtained by setting its content to 0.01% or more, and if it is within the range specified here, it can be used for strengthening steel. However, when the Ti content exceeds 0.20%, the effect is saturated, resulting in a cost increase. Accordingly, when Ti is contained, it is preferably 0.01% or more and 0.20% or less, and more preferably 0.01% or more and 0.05% or less.
  • Nb 0.01% or more and 0.10% or less Nb is also effective for strengthening steel.
  • the effect of increasing the strength by Nb can be obtained by setting its content to 0.01% or more. If it is within the range specified here, it can be used for strengthening steel. However, if the Nb content exceeds 0.10%, the effect is saturated, resulting in a cost increase. Therefore, when Nb is contained, it is preferably 0.01% or more and 0.10% or less, and more preferably 0.01% or more and 0.05% or less.
  • B 0.0002% or more and 0.0050% or less
  • B is an element that enhances the hardenability of steel.
  • the base steel sheet is cooled after hot press forming, it suppresses the formation of ferrite from the austenite grain boundaries and obtains a hardened structure. Is an effective element.
  • the effect can be obtained when the B content is 0.0002% or more. However, if the B content exceeds 0.0050%, the effect is saturated, resulting in a cost increase. Therefore, when B is contained, the content is preferably 0.0002% or more and 0.0050% or less. More preferably, it is 0.0005% or more and 0.0030% or less.
  • Sb 0.003% or more and 0.030% or less Sb suppresses the decarburization layer generated in the surface layer of the base steel sheet from the time the steel sheet is heated before hot press forming until the steel sheet is cooled by a series of hot press forming processes.
  • the Sb content is preferably 0.003% or more.
  • the content is preferably 0.003% or more and 0.030% or less, and more preferably 0.005% or more and 0.010% or less.
  • components (remainder) other than the above components are Fe and inevitable impurities.
  • the surface-treated steel sheet 1 used as a raw material of the hot press-formed member is not particularly limited in its production conditions.
  • the production conditions of the base steel sheet are not particularly limited.
  • a hot-rolled steel sheet (pickled steel sheet) having a predetermined composition and a cold-rolled steel sheet obtained by cold rolling a hot-rolled steel sheet may be used as the base steel sheet.
  • the conditions at the time of forming the Zn-Ni plating layer on the surface of the base steel sheet to form the surface-treated steel sheet 1 are not particularly limited.
  • the surface-treated steel plate 1 can be obtained by subjecting the hot-rolled steel plate (pickled steel plate) to a Zn—Ni plating treatment.
  • the surface-treated steel sheet 1 can be obtained by performing a Zn-Ni plating process as it is after cold rolling or after annealing.
  • a Zn—Ni plating layer can be formed.
  • the Ni content in the plating layer can be adjusted to the desired Ni content (for example, 9% by mass to 25% by mass) by appropriately adjusting the concentration and current density of zinc sulfate heptahydrate within the above ranges. can do.
  • the coating weight of Zn-Ni plated layer, by adjusting the energization time can be desired adhesion amount (e.g., 10 g / m 2 or more per side 90 g / m 2 or less).
  • ⁇ Pure Zn plating layer> The cold-rolled steel sheet is passed through a continuous hot-dip galvanizing line, heated to a temperature range of 800 ° C. or higher and 900 ° C. or lower at a temperature increase rate of 10 ° C./s.
  • the Zn plating layer was formed by cooling to a temperature range of 460 ° C. or more and 500 ° C. or less at a cooling rate of ° C./s and dipping in a 450 ° C. zinc plating bath.
  • the adhesion amount of the Zn plating layer was adjusted to a predetermined adhesion amount by a gas wiping method.
  • ⁇ Zn-Fe plating layer> The cold-rolled steel sheet is passed through a continuous hot-dip galvanizing line, heated to a temperature range of 800 ° C. or higher and 900 ° C. or lower at a temperature increase rate of 10 ° C./s.
  • the Zn plating layer was formed by cooling to a temperature range of 460 ° C. or more and 500 ° C. or less at a cooling rate of ° C./s and dipping in a 450 ° C. zinc plating bath.
  • the adhesion amount of the Zn plating layer was adjusted to a predetermined adhesion amount by a gas wiping method.
  • a Zn—Fe plating layer was formed by immediately heating to 500 to 550 ° C. in an alloying furnace and holding for 5 to 60 seconds.
  • the Fe content in the plating layer was set to a predetermined content by changing the heating temperature in the alloying furnace and the residence time at the heating temperature within the above range.
  • ⁇ Zn-Ni plating layer> The cold-rolled steel sheet is passed through a continuous annealing line, heated to a temperature range of 800 ° C to 900 ° C at a rate of 10 ° C / s, and retained in the temperature range for 10s to 120s, then 15 ° C / s It cooled to the temperature range below 500 degreeC with the cooling rate of s.
  • a Zn—Ni plating layer was formed by performing an electroplating process in which a current of 10 to 100 s was applied at a current density of 100 A / dm 2 .
  • the Ni content in the plating layer was set to a predetermined content by appropriately adjusting the concentration and current density of zinc sulfate heptahydrate within the above ranges.
  • the adhesion amount of the Zn—Ni plating layer was set to a predetermined adhesion amount by appropriately adjusting the energization time within the above range.
  • a 200mm x 400mm blank plate is punched from the surface-treated steel plate obtained as described above, and the blank plate is heated by an electric furnace in an atmospheric atmosphere, and then the blank plate is placed in a cooling mold (material: SKD61). Then, under the conditions shown in Table 2, cooling with a mold, press molding, and quenching were performed. And after quenching in a metal mold
  • the molds were punch punch R: 6 mm and die shoulder R: 6 mm, and the punch-die clearance was 1.6 mm.
  • the surface-treated steel sheet before press forming was cooled by contact with a cooling mold.
  • the press molding was performed by a draw molding in which a 98 kN wrinkle pressing force was applied and a foam molding in which no wrinkle pressing was performed.
  • Table 2 shows the heating temperature of the blank plate, the type of the base steel plate, the type of the plating layer, the heating condition, the cooling condition, and the press molding condition.
  • a sample was taken from the vertical wall portion of the press-formed product with the obtained hat cross-sectional shape, and the cross section of the surface was observed with 10 fields of view for each sample at a magnification of 1000 using a scanning electron microscope (SEM).
  • SEM scanning electron microscope
  • microcrack depth refers to the length of the crack in the center direction of the thickness of the microcrack 21 measured from the interface between the plating layer 23 and the base steel plate 25 (see FIG. 12). 12, the length of h). When the number of observed microcracks was less than 20, the average depth of all the observed microcracks was taken. Further, regarding the shape accuracy of the obtained press-molded member, the difference (W ⁇ W 0) between the molded product width W after mold release of the press-molded product having the hat cross-sectional shape shown in FIG. 13 and the molded product width W 0 in the mold shape. ) was evaluated as the amount of opening. These results are also shown in Table 2.
  • a sample for hardness measurement was taken from the vertical wall portion of the press-formed product having the hat cross-sectional shape.
  • the hardness of the cross section of this sample was determined with a micro Vickers hardness tester. The test was conducted at a test load of 9.8 N, the central portion in the thickness direction was measured at five points, and the average value was taken as the hardness of the sample.
  • the target hardness is 400 Hv or more.
  • a JIS 13 B tensile test piece was collected from the vertical wall portion of the obtained press-formed product having a hat cross-sectional shape.
  • the type of plating layer Zn—Ni plating layer
  • cooling method mold cooling
  • cooling time 0.6 s to 1.7 s
  • cooling rate appropriate range: 100 ° C./s or more
  • the cooling stop temperature proper range: 410 ° C to 550 ° C
  • the time to start press forming after cooling proper range: within 5 seconds
  • the press molding start temperature proper range 400 ° C to 550 ° C
  • Comparative Example 1 was formed without cooling with a cooling mold.
  • the cooling stop temperature is outside the proper range (410 ° C. to 550 ° C.). Specifically, the cooling stop temperature of Comparative Example 2 is 600 ° C., and the cooling stop temperatures of Comparative Examples 3 and 4 are 340 ° C. and 290 ° C.
  • the opening amount is 0 mm, but microcracks are generated.
  • the forming start temperature of a steel plate is higher than 550 degreeC, it turns out that a micro crack generate
  • the opening amount is 8 mm to 9 mm.
  • the press forming start temperature is also less than 400 ° C, the strength of the steel sheet is increased, and the shape freezing property may be lowered. Recognize.
  • Comparative Examples 5 to 7 since the cooling method is gas cooling, the cooling rate is out of the appropriate range (100 ° C./s or more), and rapid cooling cannot be performed. Therefore, in Comparative Examples 5 and 6, the cooling stop temperature and press forming start temperature of the steel plate are also outside the appropriate ranges (cooling stop temperature: 410 ° C. to 550 ° C., press forming start temperature: 400 ° C. to 550 ° C.), and microcracks occur. appear. In Comparative Example 7, although the cooling stop temperature is 510 ° C. and falls within the proper range, the amount of opening of the mouth is 3 mm and the shape freezing property is reduced.
  • Comparative Examples 8 and 9 the time until the start of press forming is 10 seconds and 8 seconds, respectively, which is longer than the appropriate range within 5 seconds. Therefore, in Comparative Examples 8 and 9, the opening amount is 2 mm, and the hardness and tensile strength after press molding are also reduced.
  • Comparative Examples 10 and 11 have different types of plating layers, that is, Comparative Example 10 is a Zn-only plating layer, and Comparative Example 11 is a Zn-Fe plating layer.
  • the press molding start temperature at which microcracks are not generated in the Zn-only plating layer and the Zn-Fe plating layer is lower than the press molding start temperature at which microcracks are not generated in the Zn-Ni plating layer. Therefore, in Comparative Examples 10 and 11, microcracks are generated.

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WO2015163016A1 (ja) * 2014-04-23 2015-10-29 Ｊｆｅスチール株式会社 熱間プレス成形品の製造方法および熱間プレス成形品

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MX2017003875A (es) 2017-06-08
WO2016047058A8 (ja) 2017-01-19
EP3199257A1 (de) 2017-08-02
JP2016064440A (ja) 2016-04-28
KR20170036086A (ko) 2017-03-31
EP3199257A4 (de) 2017-12-06
US20170225215A1 (en) 2017-08-10
EP3199257B1 (de) 2021-02-24

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