EP3199257B1 - Verfahren zur herstellung eines heisspressgeformten teils und heisspressgeformtes teil - Google Patents

Verfahren zur herstellung eines heisspressgeformten teils und heisspressgeformtes teil Download PDF

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Publication number
EP3199257B1
EP3199257B1 EP15843885.3A EP15843885A EP3199257B1 EP 3199257 B1 EP3199257 B1 EP 3199257B1 EP 15843885 A EP15843885 A EP 15843885A EP 3199257 B1 EP3199257 B1 EP 3199257B1
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Prior art keywords
steel sheet
cooling
press
less
press forming
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EP15843885.3A
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English (en)
French (fr)
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EP3199257A1 (de
EP3199257A4 (de
Inventor
Tatsuya Nakagaito
Yuichi Tokita
Toru Minote
Yoshikiyo Tamai
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JFE Steel Corp
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JFE Steel Corp
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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 method of manufacturing a hot press-formed part according to claim 1 and particularly, to a method of manufacturing a hot press-formed part from a coated steel sheet that enables press forming of the coated steel sheet which is heated beforehand, whereby the coated steel sheet can be quenched to attain a predetermined strength (tensile strength: 1180 MPa or higher) while being formed into a predetermined shape.
  • a predetermined strength tensile strength: 1180 MPa or higher
  • some conventional techniques propose performing hot press forming of a blank sheet heated to high temperature to have a desired shape using a tool of press forming, while quenching the blank sheet in the tool of press forming by utilizing heat extraction, to achieve high-strengthening of the hot press-formed part.
  • GB1490535A proposes a technique in which, when manufacturing a part of a predetermined shape by hot press forming a blank sheet (steel sheet) heated to an austenite single phase region at around 900 °C, the blank sheet is quenched in a tool of press forming simultaneously with the hot press forming, thus providing high-strengthening of the part.
  • the technique proposed in PTL 1 has a problem in that if the steel sheet is heated to a temperature as high as around 900 °C before subjection to the press forming, oxided scale (ion oxide) forms on the surface of the steel sheet, and the oxided scale peels during the hot press forming and damages the tool of press forming or the surface of the press formed part. Besides, the oxided scale remaining on the surface of the part causes poor appearance and degraded coating adhesion properties. Accordingly, the oxided scale on the surface of the part is typically removed by a process such as pickling or shot blasting. Such a process, however, causes lower productivity.
  • JP3663145B proposes a technique in which a steel sheet coated with Zn or a zinc-based alloy is heated to 700 °C to 1200 °C and then hot press formed to obtain a hot press-formed part having a Zn-Fe-based compound or a Zn-Fe-Al-based compound on its surface.
  • PTL 2 describes that the use of the steel sheet coated with Zn or a zinc-based alloy can suppress the oxidation of the surface of the steel sheet during heating before hot press forming, and provide a hot press-formed part having excellent corrosion resistance.
  • the generation of oxided scale on the surface of the hot press-formed part is suppressed to some extent.
  • Zn in the plating layer may induce liquid metal embrittlement cracking, causing cracks of about 100 ⁇ m in depth in the surface layer part of the hot press-formed part.
  • Such cracks pose various problems, such as a decrease in the fatigue resistance of the hot press-formed part.
  • JP201391099A proposes a method that includes heating a coated steel sheet having a Zn-Fe-based plating layer formed on the steel sheet surface to a temperature from the Ac 1 transformation temperature of the steel sheet to 950 °C, and cooling the coated steel sheet to a temperature at or below the freezing point of the plating layer before starting press forming.
  • PTL 3 describes that liquid metal embrittlement cracking can be suppressed by starting the press forming after the coated steel sheet is cooled to a temperature at or below the freezing point of the plating layer.
  • PTL 4 relates to a method for producing a hardened steel component with regions of different hardness and/or ductility; a blank is stamped out and either heated in some regions to a temperature ⁇ Ac3, and then transferred to a forming die, is formed, and is cooled at a speed that is greater than the critical hardening speed and thus hardened or is cold formed into the finished shape and the formed blank is heated in some regions to a temperature >Ac3 and then transferred to a hardening die and is hardened at a speed greater than the critical hardening speed; the steel material is adjusted in a transformation-delaying fashion so that a quench hardening through transformation of austenite into martensite takes place at a forming temperature that lies in the range from 450° C to 700° C; after the heating and before the forming, an active cooling takes place at >15 K/s.
  • the technique proposed in PTL 3 can suppress liquid metal embrittlement cracking, i.e., cracks in the surface of the hot press-formed part, which are about 100 ⁇ m in depth from the interface between the plating layer and the steel sheet (steel) toward the inside of the steel sheet, and in which Zn is detected at its interface (such cracks referred to hereinafter as "macro-cracks").
  • macro-cracks we studied the use of Zn-Ni alloy coating obtained by blending Zn with about 9 % to 25 % of Ni as a plating layer with high melting point. To ensure the corrosion resistance of a Zn-Ni alloy, the Zn-Ni alloy needs to be ⁇ -phase.
  • the ⁇ -phase in the phase equilibrium diagram of Zn-Ni alloy has a melting point of 860 °C or higher, which is very high as compared to that of a normal Zn or Zn alloy plating layer, making it possible to suppress macro-cracks under normal press conditions.
  • microfissures which are about 30 ⁇ m or less in depth from the interface between the plating layer and the steel sheet toward the inside of the steel sheet, and in which Zn is not detected at its interface, may also occur in the surface of the hot press formed-part.
  • micro-cracks Such microfissures are called "micro-cracks", which pass through the interface between the plating layer and the steel sheet and reach the inside of the steel sheet, adversely affecting the characteristics (fatigue resistance, etc.) of the hot press-formed part. Macro-cracks also occur in, for example, a round portion of the die shoulder on the punch-contacting side which is subjected to only tensile strain while press forming of a hat-shaped section part. On the other hand, micro-cracks do not occur in such area, but on the die-contacting side of wall portions, which are subjected to compression (due to bending) followed by tensile strain (due to bend restoration). It is thus estimated that macro-cracks and micro-cracks are produced by different mechanisms.
  • PTL 3 may suppress the occurrence of macro-cracks in a coated steel sheet having a Zn-Fe-based plating layer formed thereon, but is not necessarily effective for suppressing the occurrence of micro-cracks, because it does not consider potential micro-cracks occurring in a coated steel sheet having a Zn-Ni plating layer formed thereon.
  • the coated steel sheet is press formed in a state where the entire coated steel sheet has been cooled to a temperature at or below the freezing point of the plating layer, without specifying the lowest temperature at which the press forming can be started.
  • micro-cracks microfissures
  • press forming of a steel sheet coated with Zn or a zinc-based alloy at high temperature at or below the freezing point of the plating layer may cause microfissures in the surface of the steel sheet.
  • Similar microfissures also occur in a Zn-Ni coated steel sheet during press forming.
  • Such microfissures are about 30 ⁇ m in depth from the interface between the plating layer and the steel sheet, and pass through the interface between the plating layer and the steel sheet and reach the inside of the steel sheet.
  • micro-cracks are not caused by compressive deformation or bending deformation alone, but are caused at those portions that are subjected to deformation resulting from bending and subsequent bend restoration.
  • forming as described above may limited to a particular range, but in some cases the portions of the steel sheet subjected to forming that would cause micro-cracks may be extensive depending on the shape of the formed part.
  • the temperature of the steel sheet would become lower at the time of press forming and shape accuracy would degrade.
  • the steel sheet was cooled to a temperature of 550 °C or lower and 410 °C or higher at a cooling rate of 100 °C/s or higher, and when press forming of the steel sheet was started within 5 seconds after the cooling while the temperature of the steel sheet was 550 °C or lower and 400 °C or higher, there was almost no loss of shape accuracy.
  • the steel sheet when the heated steel sheet is quenched with the press tool for cooling and subjected to press forming while the steel sheet temperature is 550 °C or lower and 400 °C or higher, the steel sheet has a microstructure of austenite during the press forming, and austenite transforms to martensite after the press forming, thereby relieving the stress accumulating during the press forming.
  • the present invention provides a method of manufacturing a hot press-formed part according to claims 1 and 2 as well as a hot press-formed part manufactured by said method.
  • the present invention it becomes possible to provide hot press-formed parts, using coated steel sheets as steel sheets, that are free from micro-cracks throughout both front and back surfaces and that have sufficient hardness and satisfactory shape fixability without a significant increase in press forming load, and thus to manufacture automotive parts and the like in a variety of product shapes using coated steel sheets with high strength.
  • a method of manufacturing a hot press-formed part by hot pressing a coated steel sheet 1 formed with a Zn-Ni plating layer on a surface of a steel sheet as illustrated in FIG. 1 comprises: heating (not shown) the coated steel sheet 1 to a temperature range of Ac 3 transformation temperature to 1000 °C; cooling (S1) the heated coated steel sheet I to a temperature of 550 °C or lower and 410 °C or higher, at a cooling rate of 100 °C/s or higher, by squeezing the coated steel sheet 1 with a press tool for cooling 3 having flat surfaces configured to contact the coated steel sheet 1; starting (S2) press forming of the coated steel sheet 1 with a tool of press forming 11 within 5 seconds after the cooling while the temperature of the coated steel sheet 1 is 550 °C or lower and 400 °C or higher, to obtain a formed body 1'; and quenching (S3) the formed body 1', while squeezing the formed body with the tool of press forming 11 and
  • a coated steel sheet formed with a Zn-Ni plating layer on a surface of a steel sheet is used as the material of a hot press-formed part.
  • the provision of a Zn-Ni plating layer on a surface of the steel sheet ensures the corrosion resistance of the part after subjection to hot press forming.
  • the method of forming a Zn-Ni plating layer on a surface of the steel sheet is not particularly limited, and any methods such as hot-dip galvanizing and electrogalvanizing may be used.
  • the coating weight per side is preferably 10 g/m 2 or more and 90 g/m 2 or less.
  • the Ni content in the plating layer is preferably 9 mass% or more and 25 mass% or less.
  • a ⁇ phase having any of the crystal structures of Ni 2 Zn 11 , NiZn 3 , or Ni 5 Zn 21 is formed when the Ni content in the plating layer is 9 mass% or more and 25 mass% or less.
  • the ⁇ phase has a high melting point, and thus is advantageous in preventing the plating layer from evaporating when heating the coated steel sheet before subjection to hot press forming.
  • the ⁇ phase is also advantageous in suppressing liquid metal embrittlement cracking during high-temperature hot press forming.
  • the coated steel sheet 1 is heated to a temperature range of Ac 3 transformation temperature to 1000 °C. If the heating temperature of the coated steel sheet I is below Ac 3 transformation temperature, a sufficient amount of austenite cannot be obtained during heating, leading to the presence of ferrite during press forming. As a result, it becomes difficult to obtain sufficient strength or good shape fixability through hot press forming.
  • the heating temperature of the coated steel sheet 1 exceeds 1000 °C, on the other hand, the plating layer evaporates or excessive oxide generation occurs in the surface layer part, as a result of which the oxidation resistance or the corrosion resistance of the hot press-formed part decreases. Therefore, the heating temperature is from Ac 3 transformation temperature to 1000 °C.
  • the heating temperature is from Ac 3 transformation temperature + 30 °C to 950 °C.
  • the method of heating the coated steel sheet 1 is not particularly limited, and any methods may be used, such as heating in an electric furnace, induction heating furnace, or direct current furnace.
  • the coated steel sheet 1 thus heated 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, by being squeezed with the press tool for cooling 3.
  • the press tool for cooling 3 comprises an upper cooling tool 5 and a lower cooling tool 7, each having a flat surface configured to contact the coated steel sheet 1.
  • An extendable lifter pin 9 is provided on the lower cooling tool 7. The heated coated steel sheet 1 is placed on the lifter pin 9, and cooled by being squeezed between the upper cooling tool 5 and the lower cooling tool 7.
  • both front and back surfaces of the coated steel sheet 1 may be squeezed entirely with the press tool for cooling 3 as illustrated in FIG. 1 .
  • the coated steel sheet 1 may be placed with some portions, such as portions to be trimmed afterwards before finishing operations to form a final product, extending beyond the edges of the press tool for cooling 3.
  • portions subjected to forming that would cause micro-cracks, i.e., bending-bend restoration deformation cover a large area of the coated steel sheet 1 as the working material, it is possible to suppress the occurrence of micro-cracks throughout both front and back surfaces of the resulting press formed part.
  • the temperature at start of squeezing the heated coated steel sheet I with the press tool for cooling 3 is preferably 800 °C or lower from the perspective of preventing the risk of the Zn-Ni plating layer being adhered to the press tool for cooling, and preferably 670 °C or higher from the perspective of guaranteeing the strength after hot press forming.
  • the coated steel sheet 1 may be cooled with one surface pressed against the press tool for cooling 3.
  • the cooling rate is set to be 100 °C/s or higher because this cooling rate enables the press formed part to have a martensite single phase structure, and thus allows for strengthening, without increasing cost. In the following, this will be described in detail.
  • FIG, 2 schematically illustrates the relationship between a typical metallographic structure, temperature, and cooling time when a steel sheet is subjected to hot press forming using a tool of press forming.
  • FIG. 2A shows a case where the press forming start temperature is high and, after the start of press forming, the coated steel sheet is rapidly cooled by heat extraction to the tool of press forming, so as to have a martensite single phase structure.
  • a martensite single phase structure can be obtained while lowing the forming start temperature, as indicated by a dashed curve in FIG. 3 .
  • the upper limit of the cooling rate is normally around 500 °C/s.
  • the cooling stop temperature is set to be 550 °C or lower because, above 550 °C, cooling becomes insufficient, causing micro-cracks after the hot press forming.
  • the cooling stop temperature is preferably 500 °C or lower.
  • the lower limit of the cooling stop temperature is 410 °C because, below 410 °C, the coated steel sheet 1 is excessively cooled before subjection to the press forming, leading to deterioration in shape fixability after subjection to the press forming.
  • the cooling stop temperature is preferably 430 °C or higher.
  • the cooling rate and the cooling stop temperature may be controlled by, for example, varying the time to hold the coated steel sheet 1 with the press tool for cooling 3 (see FIG. 1 ).
  • Changes in the temperature of the coated steel sheet 1 when squeezed with the press tool for cooling 3 may be determined by measuring the temperature of the coated steel sheet 1 using a sheath type thermocouple 19 of 0.5 mm ⁇ inserted into the steel sheet in a manner as illustrated in FIG. 4 .
  • FIG. 5 is a graph showing some of the results, where the vertical axis is temperature (°C) and the horizontal axis is time (s).
  • FIG. 6 is a graph representing a partial enlarged view of FIG.
  • press formed parts were formed at different conditions by varying the holding time during which the press formed part was being held in the press tool for cooling (in particular, the cooling stop temperature set for the press tool for cooling), and the press forming start temperature, which will be described below, and evaluation was made of the following parameters.
  • FIG. 7 shows SEM (Scanning Electron Microscope) images of cross sections of surface layers, on the side contacting a die 13, of wall portions of press formed parts that were formed at different conditions by varying the time to cool the press formed part in the press tool for cooling (the cooling stop temperature set for the press tool for cooling) and the press forming start temperature. It can be seen from FIGS. 7A-7C that no micro-cracks were observed in the steel sheets with a cooling time in the press tool for cooling of 0.9 s or more (and a press forming start temperature of 550 °C or lower). Under all conditions, Hv > 450, proving that quench hardenability does not deteriorate.
  • FIG. 8 shows the relationship between press forming start temperature and press forming load, where the vertical axis is the press forming load (kN) and the horizontal axis is the press forming start temperature (°C). It can be seen from FIG. 8 that a reduction in the press forming start temperature caused by the process of cooling in the press tool for cooling prior to press forming caused an increased press forming load, which was, however, equivalent to that on mild steel (270D, cold deep forming) at temperatures around 550 °C at which micro-cracks do not occur, and thus posed no problem.
  • mild steel 270D, cold deep forming
  • FIG. 9 shows the relationship between press forming start temperature and amount of mouth opening deformation, where the vertical axis is the amount of mouth opening deformation (mm) of a formed part and the horizontal axis is the press forming start temperature (°C).
  • the amount of mouth opening deformation increases due to a decrease in the forming start temperature caused by the process of cooling in the press tool for cooling prior to the press forming process, which shows a tendency such that shape fixability deteriorates accordingly.
  • the press forming start temperature is 400 °C or higher, almost no deterioration of shape fixability is observed.
  • the coated steel sheet 1 is press formed into the shape of a product.
  • the press forming is performed with the tool of press forming 11 after the cooling.
  • the tool of press forming 11 comprises a die 13 and a punch 17 as illustrated in FIG. 1 .
  • the coated steel sheet 1 is press formed by being squeezed between the die 13 and the punch 17, to obtain a formed body 1'.
  • the press forming is started within 5 seconds after the cooling because, if press forming is started after expiry of the time limit of 5 seconds after the cooling, for example, ferrite and bainite are formed before the start of press forming, preventing formation of a martensite single phase structure. As a result, the press formed part has insufficient hardness. Press forming is preferably started within 3 seconds after the cooling. No lower limit is particularly placed on the time limit, yet a preferred time limit is normally 1 second or more.
  • the present disclosure is not limited to a particular press forming method.
  • available methods include, for example, draw forming whereby the coated steel sheet 1 is subjected to forming while being squeezed between the die 13 and the blank holder 15 as illustrated in FIG. 10A , and crash forming whereby the coated steel sheet 1 is subjected to forming while lowering the blank holder 15, or alternatively, without using the blank holder 15, as illustrated in FIG. 10B .
  • crash forming is preferred because of less excessive forming of wall portions of the press formed part.
  • the formed body 1' is quenched while being squeezed and held in the tool of press forming 11, to obtain a hot press-formed part.
  • the press slide of the formed body 1' is stopped at its press bottom dead center after subjection to the press forming.
  • the sliding stop time is preferably 3 seconds or more, although it varies with the amount of heat released by the tool of press forming. No upper limit is particularly placed on the sliding stop time, yet it is preferably 20 seconds or less from the perspective of productivity.
  • a hot-rolled or cold-rolled steel sheet having a chemical composition containing (consisting of), for example, in mass%, C: 0.15 % or more and 0.50 % or less, Si: 0.05 % or more and 2.00 % or less, Mn: 0.50 % or more and 3.00 % or less, P: 0.10 % or less, S: 0.050 % or less, Al: 0.10 % or less, and N: 0.010 % or less, and the balance consisting of Fe and unavoidable impurities.
  • the following provides a description of the chemical composition. When the composition is expressed in "%”, this refers to "mass%" unless otherwise specified.
  • the C content is an element that improves the strength of steel.
  • the C content is preferably 0.15 % or more.
  • the C content exceeds 0.50 %, on the other hand, the weldability of the hot press-formed part and the fine blanking workability of the material (steel sheet) decrease significantly. Accordingly, 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.
  • the Si is an element that improves the strength of steel, as with C.
  • the Si content is preferably 0.05 % or more.
  • the Si content exceeds 2.00 %, on the other hand, a surface defect, called red scale, increases significantly during hot rolling for manufacturing a steel sheet. Accordingly, 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 quench hardenability of steel, and is effective in suppressing the ferrite transformation of the steel sheet and improving quench hardenability in the cooling process after the hot press forming. Mn also has a function of lowering the Ac 3 transformation temperature, and thus is an element effective in lowering the heating temperature of the coated steel sheet 1 before subjection to hot press forming. To achieve these effects, the Mn content is preferably 0.50 % or more. When the Mn content exceeds 3.00 %, on the other hand, Mn segregation occurs, reducing the uniformity of characteristics of the steel sheet and of the hot press-formed part. Accordingly, 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 exceeds 0.10 %, P segregates to grain boundaries, reducing the low-temperature toughness of the steel sheet and of the hot press-formed part. Accordingly, the P content is preferably 0.10 % or less, and more preferably 0.01 % or less. Excessively reducing the P content, however, leads to increased cost in the steelmaking process. Therefore, the P content is preferably 0.003 % or more.
  • S is an element that forms a coarse sulfide by combining with Mn and causes a decrease in ductility of steel.
  • the S content is preferably reduced as much as possible, though up to 0.050 % is allowable. Accordingly, the S content is preferably 0.050 % or less, and more preferably 0,010 % or less. Excessively reducing the S content, however, leads to increased cost of desulfurization in the steelmaking process. Therefore, the S content is preferably 0.0005 % or more.
  • the Al content exceeds 0.10 %, oxide inclusions in steel increase, and the ductility of steel decreases. Accordingly, the Al content is preferably 0.10 % or less, and more preferably 0.07 % or less. Al functions as a deoxidation material, however, and from the perspective of improving the cleanliness factor of steel, the Al content is preferably 0.01 % or more.
  • the N content exceeds 0.010 %, nitrides such as AIN form in the steel sheet, which causes lower formability during hot press forming. Accordingly, the N content is preferably 0.010 % or less, and more preferably 0.005 % or less. Excessively reducing the N content, however, leads to increased cost in the steelmaking process. Therefore, the N content is preferably 0.001 % or more.
  • the steel sheet may further contain one or more of the following elements as necessary:
  • Cr, V, Mo, and Ni are each an element effective in enhancing the quench hardenability of steel. This effect is achieved when the content of any of these elements contained is 0.01 % or more. However, adding any of Cr, V, Mo, or Ni beyond 0.50 % fails to further increase this effect, but instead increases cost. Accordingly, in the case where one or more of Cr, V, Mo, and Ni is included, the content is preferably 0.01 % or more and 0.50 % or less, and more preferably 0,10 % or more and 0.40 % or less.
  • Ti is effective for strengthening steel.
  • the strengthening effect of Ti is achieved when the content is 0.01 % or more.
  • Ti can be used to strengthen steel without any problem as long as the content is within the range specified herein.
  • adding Ti beyond 0.20 % fails to increase this effect, but instead increases cost.
  • the content 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 strengthening effect of Nb is achieved when the content is 0.01 % or more.
  • Nb can be used to strengthen steel without any problem as long as the content is within the range specified herein.
  • adding Nb beyond 0.10 % fails to increase this effect, but instead increases cost.
  • the content is preferably 0.01 % or more and 0.10 % or less, and more preferably 0.01 % or more and 0.05 % or less.
  • B is an element that enhances the quench hardenability of steel, and is effective in suppressing the generation of ferrite from austenite grain boundaries and obtaining a quenched microstructure when cooling the steel sheet after subjection to the hot press forming.
  • This effect is achieved when the B content is 0.0002 % or more.
  • adding B beyond 0.0050 % fails to increase this effect, but instead increases cost.
  • the content is preferably 0.0002 % or more and 0.0050 % or less, and more preferably 0.0005 % or more and 0.0030 % or less.
  • the Sb has the effect of suppressing generation of a decarburized layer in the surface layer part of the steel sheet during the period from when a steel sheet is heated before subjection to hot press forming to when the steel sheet is cooled through 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.
  • the components (balance) other than the above are Fe and unavoidable impurities.
  • the manufacturing conditions of the coated steel sheet 1 used as the material of the hot press-formed part are not particularly limited.
  • the steel sheet may be a hot-rolled steel sheet (pickled steel sheet) having a predetermined chemical composition or a cold-rolled steel sheet obtained by subjecting the hot-rolled steel sheet to cold rolling.
  • the formation of a Zn-Ni plating layer on a surface of the steel sheet for obtaining the coated steel sheet 1 is not limited to particular conditions.
  • the coated steel sheet 1 may be obtained by subjecting the hot-rolled steel sheet (pickled steel sheet) to Zn-Ni coating treatment.
  • the coated steel sheet 1 may be obtained by subjecting the cold-rolled steel sheet to Zn-Ni coating treatment either directly after subjection to the cold rolling, or after subjection to annealing treatment following the cold rolling.
  • the Zn-Ni plating layer may be formed by degreasing and pickling the steel sheet, and then subjecting the steel sheet to electrogalvanizing treatment with a current density of 10 A/dm 2 or more and 150 A/dm 2 or less, in a plating bath which has a pH of 1.0 or more and 3.0 or less and a bath temperature of 30 °C or higher and 70 °C or lower, and which contains 100 g/L or more and 400 g/L or less nickel sulfate hexahydrate and 10 g/L or more and 400 g/L or less zinc sulfate heptahydrate.
  • the cold-rolled steel sheet may be subjected to annealing treatment before subjection to the degreasing and pickling.
  • the Ni content in the plating layer may be set within the desired range (for example, 9 mass% to 25 mass%) by appropriately adjusting the concentration of zinc sulfate heptahydrate or the current density within the above-mentioned range.
  • the coating weight of the Zn-Ni plating layer may be set within the desired range (for example, 10 g/m 2 to 90 g/m 2 per side) by adjusting the energizing time.
  • the hot-rolled steel sheet was then pickled and cold rolled with a reduction of 50 %, to obtain a cold-rolled steel sheet with a thickness of 1.6 mm.
  • the Ac 3 transformation temperature in Table 1 was calculated by Formula (1) below (see William C. Leslie, "The Physical Metallurgy of Steels", translation supervised by Nariyasu Kouda, translated by Hiroshi Kumai and Tatsuhiko Noda, Maruzen Co., Ltd., 1985, p. 273 ).
  • a cold-rolled steel sheet was passed through a continuous hot-dip galvanizing line, heated to a temperature range of 800 °C to 900 °C at a heating rate of 10 °C/s, and held in this temperature range for 10 s or more and 120 s or less. Subsequently, the cold-rolled steel sheet was cooled to a temperature range of 460 °C to 500 °C at a cooling rate of 15 °C/s, and dipped into a galvanizing bath at 450 °C to form a Zn plating layer. The coating weight of the Zn plating layer was adjusted to a predetermined coating weight using a gas wiping method.
  • a cold-rolled steel sheet was passed through a continuous hot-dip galvanizing line, heated to a temperature range of 800 °C to 900 °C at a heating rate of 10 °C/s, and held in this temperature range for 10 s or more and 120 s or less. Subsequently, the cold-rolled steel sheet was cooled to a temperature range of 460 °C to 500 °C at a cooling rate of 15 °C/s, and dipped into a galvanizing bath at 450 °C to form a Zn plating layer. The coating weight of the Zn plating layer was adjusted to a predetermined coating weight using a gas wiping method.
  • the cold rolled steel sheet was heated to a temperature range of 500 °C to 550 °C and held for 5 s to 60 s in an alloying furnace, thereby forming a Zn-Fe plating layer.
  • the Fe content in the plating layer was set to a predetermined content by changing the heating temperature in the alloying furnace and the holding time at the heating temperature within the above-mentioned ranges.
  • the cold-rolled steel sheet was passed through a continuous annealing line, heated to a temperature range of 800 °C to 900 °C at a heating rate of 10 °C/s, and held in this temperature range for 10 s or more and 120 s or less. Subsequently, the cold-rolled steel sheet was cooled to a temperature range of 500 °C or lower at a cooling rate of 15 °C/s.
  • the cold-rolled steel sheet was subjected to degreasing and pickling, followed by electrogalvanizing treatment whereby the cold-rolled steel sheet was energized for 10 s to 100 s with a current density of 30 A/dm 2 to 100 A/dm 2 , in a plating bath containing 200 g/L nickel sulfate hexahydrate and 10 g/L to 300 g/L zinc sulfate heptahydrate and having a pH of 1.3 and a bath temperature 50 °C, thereby forming a Zn-Ni plating layer.
  • the Ni content in the plating layer was set to a predetermined content by appropriately adjusting the concentration of zinc sulfate heptahydrate and the current density within the above-mentioned ranges.
  • the coating weight of the Zn-Ni plating layer was set to a predetermined coating weight by appropriately adjusting the energizing time within the above-mentioned range.
  • a blank sheet of 200 mm ⁇ 400 mm was blanked from each coated steel sheet thus obtained, and heated in an electric furnace in air atmosphere.
  • the blank sheet was then placed and cooled in a press tool for cooling (material: SKD61), and subjected to press forming and quenching using a tool of press forming under the conditions presented in Table 2.
  • the blank sheet was released from the tool of press forming to manufacture a press formed part with a hat-shaped section as illustrated in FIG. 11 .
  • the round portion of punch shoulder was 6 mm and the round portion of die shoulder was 6 mm.
  • the press forming was performed with a punch-die clearance of 1.6 mm. Cooling prior to press forming was performed by bringing the blank sheet into contact with the press tool for cooling. Press forming was performed either by draw forming under a blank holder force of 98 kN, or crash forming without using a blank holder.
  • Table 2 shows the blank sheet heating temperature, type of steel sheet, type of plating layer, heating conditions, cooling conditions, and press forming conditions.
  • micro-crack depth refers to, as illustrated in FIG.
  • each press formed part was evaluated based on the amount of mouth opening deformation, which was determined by the difference (W - W 0 ) between the width (W) of each press formed part with a hat-shaped section after die release and the width (W 0 ) of the corresponding formed part when conformed to the shape of the tool of press forming illustrated in FIG. 13 .
  • a sample for hardness measurement was collected from a wall portion of each press formed part with a hat-shaped section.
  • the hardness of the cross section of each sample was measured using a micro-Vickers hardness meter.
  • a test was conducted with a test load of 9.8 N, and hardness measurement was made at five central positions in the thickness direction for each sample, and the average was used as the hardness of the sample. In this case, the targeted hardness was 400 Hv or more.
  • a JIS No. 13 B tensile test piece was collected from a wall portion of each press formed part with a hat-shaped section.
  • the type of plating layer Zn-Ni plating layer
  • cooling process cooling in the press tool for cooling
  • cooling time 0.6 s to 1.7 s
  • cooling rate (appropriate range: 100 °C/s or higher)
  • cooling stop temperature (appropriate range: 410 °C to 550 °C)
  • time limit to start press forming after cooling (appropriate range: within 5 seconds)
  • press forming start temperature (appropriate range: 400 °C to 550 °C) are all within the appropriate ranges specified in this disclosure.
  • the pressed samples according to our examples were free from micro-cracks, and the amount of mouth opening deformation was determined to be 0 mm for these samples. From these results, it can be seen that, with the press forming process disclosed herein, it is possible to suppress the occurrence of micro-cracks while ensuring good shape fixability.
  • Comparative Example 1 was subjected to a forming process without being cooled with the press tool for cooling.
  • Comparative Examples 2 to 4 were outside the appropriate range (410 °C to 550 °C) in terms of cooling stop temperature. Specifically, the cooling stop temperature was 600 °C in Comparative Example 2, 340 °C in Comparative Example 3, and 290 °C in Comparative Example 4.
  • the cooling process was gas cooling, in which the cooling rate was outside the appropriate range (100 °C/s or higher), and thus rapid cooling could not be performed. Accordingly, in Comparative Examples 5 and 6, the cooling stop temperature and the press forming start temperature of the steel sheets were outside the appropriate ranges (cooling stop temperature: 410 °C to 550 °C, press forming start temperature: 400 °C to 550 °C), and micro-cracks occurred. Further, in Comparative Example 7, the cooling stop temperature was 510 °C, which is within the appropriate range. However, the amount of mouth opening deformation was 3 mm, which shows a reduction in the shape fixability.
  • Comparative Examples 8 and 9 press forming was started in 10 seconds and 8 seconds respectively after the cooling, exceeding the appropriate time limit of 5 seconds. Accordingly, in Comparative Examples 8 and 9, the amount of mouth opening deformation was 2 mm, and the steel sheets showed a reduction in the hardness and tensile strength after subjection to the press forming.
  • Comparative Examples 10 and 11 were different from the examples and other comparative examples in the type of plating layer. Specifically, Comparative Example 10 used a pure Zn plating layer and Comparative Example 11 used a Zn-Fe plating layer. The press forming start temperature at which micro-cracks will not occur in the pure Zn plating layer or in the Zn-Fe plating layer is even lower than the press forming start temperature at which micro-cracks will not occur in a Zn-Ni plating layer. Thus, micro-cracks occurred in Comparative Examples 10 and 11.

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Claims (2)

  1. Verfahren zum Herstellen eines warmgepressgeformten Teils durch Warmpressen eines beschichteten Stahlblechs (1), das mit einer Zn-Ni-Plattierungsschicht (23) an einer Oberfläche eines Stahlblechs (25) versehen ist, wobei das Stahlblech (25) eine chemische Zusammensetzung aufweist, die in Masse-% aus
    0,15 % oder mehr und 0,50 % oder weniger C,
    0,05 % oder mehr und 2,00 % oder weniger Si,
    0,50 % oder mehr und 3,00 % oder weniger Mn,
    0,10 % oder weniger P, 0,050 % oder weniger S,
    0,10 % oder weniger Al, sowie
    0,010 % oder weniger N,
    wahlweise einem oder mehreren der folgenden Bestandteile:
    0,01 % oder mehr und 0,50 % oder weniger Cr,
    0,01 % oder mehr und 0,50 % oder weniger V,
    0,01 % oder mehr und 0,50 % oder weniger Mo,
    0,01 % oder mehr und 0,50 % oder weniger Ni,
    0,01 % oder mehr und 0,20 % oder weniger Ti,
    0,01 % oder mehr und 0,10 % oder weniger Nb,
    0,0002 % oder mehr und 0,0050 % oder weniger B,
    sowie 0,003 % oder mehr und 0,030 % oder weniger Sb
    besteht, wobei der Rest aus Fe und unvermeidbaren Verunreinigungen besteht, und das Verfahren umfasst:
    Erhitzen des beschichteten Stahlblechs (1) auf einen Temperaturbereich von Ac3-Umwandlungstemperatur bis 1000 °C;
    Abkühlen des erhitzten beschichteten Stahlblechs auf eine Temperatur von 550 °C oder darunter und 410 °C oder darüber mit einer Abkühlgeschwindigkeit von 100 °C/s oder höher, durch Pressen des beschichteten Stahlblechs (1) mit einem Abkühl-Presswerkzeug (3), wobei das Abkühl-Presswerkzeug (3) ein oberes Abkühl-Werkzeug (5) und ein unteres Abkühl-Werkzeug (7) umfasst, die jeweils eine plane Oberfläche haben, die so ausgeführt ist, dass sie mit dem beschichteten Stahlblech (1) in Kontakt kommt, und wobei sowohl die Vorder- als auch die Rückseite des beschichteten Stahlblechs (1) vollständig mit dem Abkühl-Presswerkzeug (3) gepresst werden;
    Pressformen des beschichteten Stahlblechs (1) durch Pressen des Stahlblechs (1) zwischen einer Matrize (13) und einem Stempel (17) eines Pressform-Werkzeugs (11), um einen geformten Körper (1') zu erhalten, wobei das Pressformen innerhalb von 5 Sekunden nach dem Abkühlen eingeleitet wird, wenn die Temperatur des beschichteten Stahlblechs (1) 550 °C oder weniger und 400 °C oder mehr beträgt; und
    Abschrecken des geformten Körpers (1'), während der geformte Körper (1') mit dem Pressform-Werkzeug (11) gepresst wird und an seinem unteren Pressen-Totpunkt gehalten wird, um ein warmpressgeformtes Teil zu erhalten.
  2. Verfahren zum Herstellen eines warmpressgeformten Teils nach Anspruch 1, dadurch gekennzeichnet, dass die Zn-Ni-Plattierungsschicht (23) des beschichteten Stahlblechs (1) 9 Masse-% oder mehr und 25 Masse-% oder weniger Ni enthält.
EP15843885.3A 2014-09-25 2015-09-07 Verfahren zur herstellung eines heisspressgeformten teils und heisspressgeformtes teil Active EP3199257B1 (de)

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JP2016064440A (ja) 2016-04-28
EP3199257A1 (de) 2017-08-02
MX2017003875A (es) 2017-06-08
US20170225215A1 (en) 2017-08-10
WO2016047058A8 (ja) 2017-01-19
CN106714996A (zh) 2017-05-24
CN106714996B (zh) 2019-07-05
WO2016047058A1 (ja) 2016-03-31
KR20170036086A (ko) 2017-03-31
EP3199257A4 (de) 2017-12-06

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