CN106714996A - Method of manufacturing hot press-formed part, and hot press-formed part - Google Patents
Method of manufacturing hot press-formed part, and hot press-formed part Download PDFInfo
- Publication number
- CN106714996A CN106714996A CN201580049874.9A CN201580049874A CN106714996A CN 106714996 A CN106714996 A CN 106714996A CN 201580049874 A CN201580049874 A CN 201580049874A CN 106714996 A CN106714996 A CN 106714996A
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- Prior art keywords
- steel plate
- hot
- temperature
- treated steel
- cooling
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 51
- 239000010959 steel Substances 0.000 claims abstract description 195
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 194
- 238000001816 cooling Methods 0.000 claims abstract description 88
- 229910007567 Zn-Ni Inorganic materials 0.000 claims abstract description 31
- 229910007614 Zn—Ni Inorganic materials 0.000 claims abstract description 31
- 230000009466 transformation Effects 0.000 claims abstract description 10
- 238000007731 hot pressing Methods 0.000 claims abstract description 6
- 239000011248 coating agent Substances 0.000 claims description 63
- 238000000576 coating method Methods 0.000 claims description 63
- 238000000034 method Methods 0.000 claims description 56
- 239000011159 matrix material Substances 0.000 claims description 45
- 238000007747 plating Methods 0.000 claims description 11
- 238000007493 shaping process Methods 0.000 claims description 10
- 238000004381 surface treatment Methods 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 abstract description 15
- 238000010791 quenching Methods 0.000 abstract description 14
- 230000000171 quenching effect Effects 0.000 abstract description 13
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 230000006866 deterioration Effects 0.000 abstract 1
- 239000011701 zinc Substances 0.000 description 28
- 230000000694 effects Effects 0.000 description 17
- 238000007710 freezing Methods 0.000 description 17
- 230000008014 freezing Effects 0.000 description 17
- 230000000052 comparative effect Effects 0.000 description 16
- 230000007423 decrease Effects 0.000 description 16
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 14
- 208000037656 Respiratory Sounds Diseases 0.000 description 13
- 238000005516 engineering process Methods 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 230000009467 reduction Effects 0.000 description 12
- 238000010586 diagram Methods 0.000 description 11
- 230000033228 biological regulation Effects 0.000 description 10
- 229910052725 zinc Inorganic materials 0.000 description 10
- 230000008859 change Effects 0.000 description 9
- 239000010960 cold rolled steel Substances 0.000 description 9
- 238000012545 processing Methods 0.000 description 9
- 239000002994 raw material Substances 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 238000005336 cracking Methods 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 238000005452 bending Methods 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 238000005554 pickling Methods 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 229910001338 liquidmetal Inorganic materials 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 238000004080 punching Methods 0.000 description 4
- 230000003014 reinforcing effect Effects 0.000 description 4
- 230000001629 suppression Effects 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 238000000137 annealing Methods 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000005238 degreasing Methods 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000003780 insertion Methods 0.000 description 3
- 230000037431 insertion Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000009713 electroplating Methods 0.000 description 2
- 230000008020 evaporation Effects 0.000 description 2
- 238000001704 evaporation Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005246 galvanizing Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 229940116202 nickel sulfate hexahydrate Drugs 0.000 description 2
- -1 nickel sulfate hexahydrate compound Chemical class 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000003672 processing method Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 235000019628 coolness Nutrition 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000000284 extract Substances 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000010813 municipal solid waste Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 238000005480 shot peening Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
Classifications
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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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Electrochemistry (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
- Heat Treatment Of Articles (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Mounting, Exchange, And Manufacturing Of Dies (AREA)
Abstract
A method of manufacturing a hot press-formed part, in which the hot press-formed part is manufactured by hot pressing a surface-treated steel sheet (1) comprising a Zn-Ni plated layer formed on the surface of a base steel sheet, is provided with the following steps in order to suppress the generation of micro-cracks while suppressing deterioration in the shape-fixability during hot press-forming, namely: a step of heating the surface-treated steel sheet to a temperature in a range at least equal to the Ac3 transformation point and at most equal to 1000 DEG C; a step of cooling the surface-treated steel sheet at a cooling rate of at least 100 DEG C/s to a temperature at most equal to 550 DEG C and at least equal to 410 DEG C, by sandwiching the heated surface-treated steel sheet in a cooling die (3) of which the surface that is in contact with the surface-treated steel sheet is planar; a step of obtaining a formed body by starting to press-form the surface-treated steel sheet using a press-forming die (11) within 5 seconds after cooling, and while the temperature of the surface-treated steel sheet is in a range at most equal to 550 DEG C and at least equal to 400 DEG C; and a step of maintaining the formed body at bottom dead center of forming while the formed body is still sandwiched in the press-forming die, and quenching the formed body to yield the hot press-formed part.
Description
Technical field
The present invention relates to hot-forming product and its manufacture method, the manufacture method of more particularly to following hot-forming product, institute
When to state manufacture method be by pre-heated surface treated steel plate stamping and forming, quenched while shape is assigned, from
And can obtain prescribed strength (tensile strength：More than 1180MPa grades) hot-forming product manufacture method.
Additionally, the present invention relates to the hot-forming product manufactured according to the manufacture method of above-mentioned hot-forming product.
Background technology
In recent years, high intensity, the thin-walled property of requirement automobile component are started.Therefore, advancing and use in automobile component
Steel plate high intensity, however as high intensity, punch process declines, it is difficult to which steel plate is processed into desired part shape
Shape.
As the technology for solving the above problems, it is known to following technology：The raw material steel of high temperature is will warm up using mould
Plate hot forming is desired shape, while radiating quenching is carried out in mould, so that the component obtained after hot forming is high
Intensity.
Following technology is for example proposed in patent document 1：In the base to being heated to 900 DEG C or so of austenite one phase area
When plate (steel plate) implements hot forming and manufactures the component of regulation shape, quenched in mould while hot forming, by
This realizes the high intensity of component.
However, in patent document 1 propose technology there are the following problems：Preceding steel plate is heated to 900 DEG C stamping
During the high temperature of left and right, oxide skin (oxided scale) (ferriferous oxide) is generated in surface of steel plate, the oxide layer is in hot forming
When it is peeling-off and make mould damage or damage the component surface after hot forming.Additionally, in the oxygen of component surface residual
Change layer and also result in bad order, the decline of application adhesiveness.Therefore, generally carry out the treatment such as pickling, shot-peening and come removing member surface
Oxide layer, but comprehend at these and cause the reduction of productivity ratio.In addition, the suspension member of automobile, body structure component etc. are also needed
Excellent corrosion resistance is wanted, but for the technology proposed in patent document 1, coating etc. is not provided with sheet stock
Antirust envelope.Therefore, the corrosion resistance according to hot forming component obtained from the technology is insufficient.
Due to it is above-mentioned the reasons why, expect following hot forming technologies：Oxidation can be suppressed in the heating before hot forming
Layer generation, while can improve the corrosion resistance of the component after hot forming.For above-mentioned expectation, it is proposed that set on surface
The surface treated steel plate for having the envelopes such as coating or the hot press forming method for having used surface treated steel plate.
For example, proposing following technology in patent document 2：To be heated to by the steel plate of Zn (zinc) or Zn based alloy plating
700~1200 DEG C, hot forming is then carried out, be thus formed in surface and possess Zn-Fe based compounds or Zn-Fe-Al base chemical combination
The hot forming component of thing.Additionally, being recorded in patent document 2：By using by the steel plate of Zn or Zn based alloy plating, energy
It is enough to suppress the oxidation of the surface of steel plate as problem in the heating before hot forming, and excellent corrosion resistance can be obtained
Hot forming component.
Using the technology proposed in patent document 2, the generation of the oxide skin of hot forming component surface is to a certain extent
It is suppressed.But, cause sometimes because of Liquid Metal Embrittlement crackle caused by the Zn in coating, sometimes in hot forming component
Skin section produce 100 μm or so of depth crackle.If producing such crackle, the endurance of hot forming component can be caused
The various problems such as characteristic decline.
For such problem, following methods are proposed in patent document 3：By above-mentioned surface treated steel plate (in matrix
Surface of steel plate is formed with the surface treated steel plate of Zn-Fe systems coating) it is heated to the Ac of matrix steel plate1It is more than transformation temperature 950 DEG C with
Under temperature, after the temperature that surface treated steel plate is cooled to below the freezing point of coating, start it is stamping.Also, patent
Recorded in document 3：Start stamping after the temperature that surface treated steel plate is cooled to below the freezing point of coating, thus may be used
Suppress Liquid Metal Embrittlement crackle.
Prior art literature
Patent document
Patent document 1：No. 1490535 publications of British Patent No.
Patent document 2：Japanese Patent No. 3663145
Patent document 3：Japanese Unexamined Patent Publication 2013-91099 publications
The content of the invention
The invention problem to be solved
If thinking, using the technology proposed in patent document 3, Liquid Metal Embrittlement crackle can be suppressed, you can suppress to produce
In the surface of hot forming component, from coating-matrix steel plate (base steel) interface to the depth in matrix steel intralamellar part direction be 100 μm
Left and right, can detect the crackle (hereinafter referred to as " macroscopic cracking (macro-cracks) ") of Zn at the interface in crackle portion.
For the suppression of such macroscopic cracking, present inventor contains 9~25% or so in have studied use Zn
The Zn-Ni alloy coating of Ni is used as dystectic coating.For the corrosion resistance of Zn-Ni alloy coating ensures, it is necessary to make
Zn-Ni alloy is γ phases, γ phases fusing point present in the equilibrium state diagram of Zn-Ni alloy compared with common Zn systems coating very
It is high, be more than 860 DEG C, even so that common punching press condition can also suppress the generation of macroscopic cracking.
It is well known, however, that on the surface of hot forming component, generation is not above-mentioned macroscopic cracking, but from coating-base
Body steel plate interface is for about less than 30 μm to the depth in matrix steel intralamellar part direction, can not detect the small of Zn at the interface in crackle portion
Crackle.The fine crack is referred to as micro-crack (micro-cracks), its insertion coating-matrix steel board interface and to reaching matrix steel
The inside of plate, all characteristics (fatigue-resistance characteristics etc.) to hot forming component have undesirable effect.
Only produced as the punch. contact side of punch die shoulder arc sections when for example that hat section component is stamping
The part of stretcher strain can also produce macroscopic cracking.And on the other hand, micro-crack is not produced in such part, in longitudinal wall part
Punch die contact side as after (bending) compression (bending recover) be stretched the place generation of deformation.Thus it is speculated that for
For macroscopic cracking and micro-crack, the mechanism that it is produced is different.
From the aspect of from this, for the technology of patent document 3, for being formed with the surface of Zn-Fe systems coating
Reason steel plate, can suppress the generation of macroscopic cracking, but be directed to the micro-crack being formed with the surface treated steel plate of Zn-Ni coating also
There is no any consideration, it cannot be said that micro-crack is produced and suppresses certain effective.
Additionally, in the technology proposed in patent document 3, proposing that surface treated steel plate is integrally cooled to the solidification of coating
The state of the following temperature of point carries out stamping, but does not show that the lower limit of the temperature for starting stamping.Accordingly, it is possible to
The intensity of steel plate when causing stamping because of the reduction of stamping temperature rises, and there is shape freezing (shape
Fixability) (resilience etc. is small, can maintain the property of the shape for shaping lower dead center) declines, so as to easily cause resilience
The problem of (spring back).
The present invention is completed to solve described problem, the manufacture its object is to provide following hot-forming product
Method：When surface treated steel plate to being formed with Zn-Ni systems coating implements hot pressing and manufactures hot-forming product, suppress hot forming
When shape freezing decline, while suppress micro-crack generation.Additionally, present invention aim at offer according to above-mentioned heat
The manufacture method of molded product and the hot-forming product that manufacture.
Means for solving the problems
The micro-crack as problem is (small to split when present inventor is first to suppressing Zn systems plated steel sheet hot forming
Line) method studied.
The generting machanism of micro-crack is also indefinite, but by with the high temperature below coating freezing point by the plated steel sheet of Zn systems
It is stamping, fine crack can be produced on the surface of plated steel sheet.Additionally, immediately Zn-Ni plated steel sheets is stamping
In the case of, also produce same fine crack.Also, it from the depth of coating-matrix steel board interface is 30 μm that the fine crack is
The small crackle of left and right, its insertion coating-matrix steel board interface reaches matrix steel intralamellar part.
For above-mentioned problem, the result that present inventor has carried out various researchs finds：By reducing hot forming
When steel billet temperature can suppress micro-crack.In addition, following effects are also obtained：By it is as described above stamping when steel plate
The reduction of temperature, has been greatly reduced the coating adhesion amount to mould as problem in existing hot pressing plated steel sheet.
If however, steel billet temperature when reducing stamping, because the intensity of steel plate rises, therefore causes shape freezing
The decline of property, it is impossible to play advantage during hot forming.
Therefore, present inventor whether expect can be with：When stamping, will only be subjected to produce the processing of micro-crack
Part cooled down, then hot forming.Also, what kind of processing the processing to producing above-mentioned micro-crack is, bears to add
The part of work is what kind of is partly studied.
First, when studying the processing for producing micro-crack, generation band of the processing deformation to micro-crack is have studied repeatedly
The influence for coming.Its result finds：Only stretching, compression, flexural deformation when do not produce micro-crack, once the part quilt for having bent
Stretch again, just produce micro-crack in the part for being recovered deformation by bending-bending.
It is from the aspect of from this, as described above to be machined with the situation for being defined to privileged site, also with good grounds products formed
Shape, bear produce micro-crack processing position extensively throughout steel plate situation.
Therefore, the method that the generation of micro-crack can be just suppressed to the privileged site not limited as the steel plate of processed component
Studied.Its result finds：Added by being clamped with the cooling mould that the contact surface with surface treated steel plate is plane
Heat surface treated steel plate, with the cooling velocity of 100 DEG C/more than s by surface treated steel plate be cooled to less than 550 DEG C 410 DEG C with
On temperature, in addition after the cooling period within 5 seconds and surface treated steel plate temperature in the range of less than 550 DEG C more than 400 DEG C,
Using press forming die, start the stamping of surface treated steel plate, thus in the table of the manufacturing press-molded products for finally giving
Face entire surface scope suppresses the generation of micro-crack, while it is bad also to suppress form accuracy.
Think on can by cooling suppressed with the cooling of mould form accuracy it is bad the reasons why it is as described below.
That is, the representational form accuracy as shape for hat component is bad, can enumerate clamping bending crestal line 2 faces institute into
Angle become the plane of big angle change and longitudinal wall part relative to die angle and become the wall in the face with curvature and stick up
It is bent.These are produced by the stress distribution difference in thickness of slab direction, and the flow stress of steel plate during processing is higher, and stress distribution is poor
More expand, form accuracy declines.That is, in hot forming, stamping temperature is lower, steel plate it is stamping when flow stress
Higher, form accuracy declines.Although it is contemplated that under temperature reduction, the form accuracy of steel plate when stamping caused by cooling
Drop, but less than 550 DEG C more than 410 DEG C of temperature is cooled to by the cooling velocity with 100 DEG C/more than s, after the cooling period 5 seconds with
Interior and steel billet temperature is stamping to start in the range of less than 550 DEG C more than 400 DEG C, then almost do not find form accuracy
Decline.
Think that its reason is as described below：Using cooling mould by the steel plate chilling after heating, and it is 550 in steel billet temperature
When carrying out stamping in the range of more than 400 DEG C below DEG C, steel plate when stamping is organized as austenite, it is stamping after
Austenite phase becomes martensite, so that the stress applied when stamping is alleviated.
On the other hand, it is believed that：If the steel plate after heating is not made into stamping started temperature reduction with carrying out chilling, by
In generation ferrite, bainite before stamping beginning, therefore above-mentioned angle change is produced while intensity decreases.
Additionally it is believed that：When steel billet temperature during stamping beginning is less than 400 DEG C, due to before stamping beginning
Start martensitic traoformation, the stress applied along with the increase of armor plate strength, therefore when stamping causes to produce above-mentioned wall
Face warpage.
The present invention is completed based on opinion as described above, specifically possesses following composition.
(1) manufacture method of hot-forming product, the manufacture method is to being formed with Zn-Ni platings on the surface of matrix steel plate
The surface treated steel plate of layer implements hot pressing to manufacture the manufacture method of the hot-forming product of hot-forming product, the manufacture method bag
Include following operation：
Above-mentioned surface treated steel plate is heated to Ac3It is more than transformation temperature, less than 1000 DEG C of temperature range；
Using the contact surface with above-mentioned surface treated steel plate for the cooling mould of plane clamps the above-mentioned surface heated
Treatment steel plate, thus with the cooling velocity of 100 DEG C/more than s by above-mentioned surface treated steel plate be cooled to less than 550 DEG C 410 DEG C with
On temperature；
After above-mentioned cooling within 5 seconds, and the temperature of above-mentioned surface treated steel plate is less than 550 DEG C more than 400 DEG C of model
In enclosing, the stamping of above-mentioned surface treated steel plate is started using press forming die, obtain formed body；
Above-mentioned formed body is hold using above-mentioned press forming die and it is directly maintained at shaping lower dead center, to above-mentioned
Formed body is quenched, and obtains hot-forming product.
(2) manufacture method of the hot-forming product described in above-mentioned 1, wherein, the Zn-Ni coating in above-mentioned surface treated steel plate
In Ni contents be below the mass % of more than 9 mass % 25.
(3) hot-forming product, the hot-forming product are using the method manufacture described in above-mentioned 1 or 2.
The effect of invention
Due to according to the present invention, using surface treated steel plate as raw material, can obtain the entire surface inside table do not produce it is micro-
Crackle, products formed hardness also sufficiently, without significantly shaping load it is increased, also no shape freezing ask
The hot-forming product of topic, therefore can be used the surface treated steel plate of high intensity to create the automobile component of various article shapes
Deng.
Brief description of the drawings
The explanatory diagram of the manufacture method of the hot-forming product that [Fig. 1] is related to for one embodiment of the present invention.
[Fig. 2] is to show metal structure and temperature, the schematic diagram (one) of the relation of cool time.
[Fig. 3] be show metal structure and temperature, the relation of cool time schematic diagram (secondly).
[Fig. 4] is the explanatory diagram of the test film for testing in one embodiment of the present invention.
[Fig. 5] is the explanatory diagram of the experimental result in one embodiment of the present invention, to show the temperature change of test film
Curve map.
[Fig. 6] is the figure that a part for the transverse axis of Fig. 5 is amplified display.
[Fig. 7] is the figure for showing the experimental result in an implementation method, is the SEM image of the longitudinal wall part of manufacturing press-molded products.
[Fig. 8] is the figure for showing the experimental result in an implementation method, to show stamping started temperature and striking out
The figure of the relation of shape load.
[Fig. 9] is the figure for showing the experimental result in an implementation method, to show stamping started temperature and amount of opening
Relation figure.
[Figure 10] is the explanatory diagram of the manufacturing process in one embodiment of the present invention.
[Figure 11] is the explanatory diagram of manufacturing press-molded products stamping in embodiment.
[Figure 12] is the explanatory diagram of micro-crack verified in embodiment.
[Figure 13] is the explanatory diagram of amount of opening verified in embodiment.
Specific embodiment
As shown in figure 1, the manufacture method of hot-forming product that one embodiment of the present invention is related to is in matrix steel plate
Surface be formed with the surface treated steel plate 1 of Zn-Ni coating and implement hot pressing to manufacture the system of the hot-forming product of hot-forming product
Method is made, it possesses following operations：Heating process, surface treated steel plate 1 is heated to Ac by it3It is more than transformation temperature, 1000 DEG C with
Under temperature range (not shown)；Refrigerating work procedure (S1), it is using the contact surface with surface treated steel plate 1 for the cooling of plane is used
Mould 3 clamps the surface treated steel plate 1 for having heated, and is thus cooled down surface treated steel plate 1 with the cooling velocity of 100 DEG C/more than s
To less than 550 DEG C more than 410 DEG C of temperature；Stamping operation (S2), it is after the cooling period within 5 seconds, and in surface treated steel
The temperature of plate 1 is in the range of less than 550 DEG C more than 400 DEG C, rushing for surface treated steel plate 1 to be started using press forming die 11
Pressing formation, obtains formed body 1 '；Quenching process (S3), it holds formed body 1 ' and its is direct using press forming die 11
Shaping lower dead center is maintained at, formed body 1 ' is quenched, obtain hot-forming product.
Hereinafter, for hot-forming product raw material, heating process, refrigerating work procedure (S1), stamping operation (S2), quench
Firer's sequence (S3) is described in detail.
The raw material ＞ of the hot-forming product of ＜
As the raw material of hot-forming product, the surface treatment for being provided with the surface of matrix steel plate Zn-Ni coating is used
Steel plate.Zn-Ni coating is set by matrix surface of steel plate, it can be ensured that the corrosion resistance of the component after hot forming.
The method for forming Zn-Ni coating in matrix surface of steel plate is not particularly limited, and can be any hot-dip, plating etc.
Method.The adhesion amount of coating is preferably set to every one side 10g/m2Above 90g/m2Below.
Furthermore it is preferred that the Ni contents in making coating are set as more than 9 mass % below 25 mass %.Will using galvanoplastic
It is below the mass % of more than 9 mass % 25 by making the Ni contents in coating when Zn-Ni coating is formed at matrix surface of steel plate,
Can be formed with Ni2Zn11、NiZn3、Ni5Zn21In the crystalline texture of any one γ phases.Because the γ phase fusing points are high, therefore
It is favourable in terms of the evaporation of the worried coating of suppression when surface treated steel plate before hot forming is heated.Additionally, to
The suppression of the Liquid Metal Embrittlement crackle as problem is also advantageous during the hot forming of high temperature.
＜ heating processes ＞
Surface treated steel plate 1 is heated to Ac3It is more than transformation temperature, less than 1000 DEG C of temperature range.If surface treated steel
The heating-up temperature of plate 1 is less than Ac3Transformation temperature, then can not obtain the austenite of appropriate amount, and deposited when stamping when due to heating
It is difficult to obtain sufficient intensity after ferrite, therefore hot forming, is difficult to ensure that good shape freezing.On the other hand,
It is excessive due to the oxide in the evaporation of coating or skin section if the heating-up temperature of surface treated steel plate 1 is more than 1000 DEG C
Generation, and cause the corrosion resistance of oxidative resistance or hot-forming product to decline.Therefore, heating-up temperature is Ac3It is more than transformation temperature
Less than 1000 DEG C.More preferably (Ac3+ 30 DEG C of transformation temperature) more than less than 950 DEG C.The heating means of surface treated steel plate 1 do not have
It is particularly limited to, can is using the arbitrary method such as electric furnace or induction heater, the heating of direct-electrifying heating furnace.
＜ refrigerating work procedures ＞
Refrigerating work procedure (S1) is to clamp the surface treated steel plate 1 for having heated using cooling mould 3, with 100 DEG C/more than s
Cooling velocity be cooled to less than 550 DEG C more than 410 DEG C temperature operation.
As shown in figure 1, cooling mould 3 have with the contact surface of surface treated steel plate 1 be plane mold 5 and under
Mould 7, is provided with telescopic lifter pin (lifter pin) 9 in lower mould 7.Surface treated steel plate 1 after heating is loaded
In on lifter pin 9, thereafter by mold 5 and the clamping of lower mould 7 so as to cooled.
Additionally, as shown in figure 1, when clamping the surface treated steel plate 1 for having heated with cooling mould 3, substantially using cooling
The table the inside entire surface of steel plate 1 is processed with the clamping surface of mould 3, but for the portion being trimmed before end article is made
Point, or the mode that the part is exposed from cooling mould 3.Thus, even if bearing to produce the portion of the such processing of micro-crack
Point, bear bending-bending recover deformation part it is extensive in the case of the surface treated steel plate 1 as processed material,
Also can inside the table of the manufacturing press-molded products for finally giving entire surface scope suppress micro-crack generation.
It should be noted that as the opportunity that the surface treated steel plate 1 after heating is clamped with cooling mould 3, preferably
It is that no Zn-Ni coating is attached to below dangerous 800 DEG C of mould, it is excellent that the intensity from after hot forming ensures that viewpoint considers
Elect more than 670 DEG C as.Additionally, cooling can be connected to a side of surface treated steel plate 1 with mould 3 to be cooled down.
Here, cooling velocity is set as 100 DEG C/s above is in order to martensite single phase just can be turned into without cost increase
Tissue is so as to realize high intensity.
This point is illustrated in further detail.
Fig. 2 is the general metal structure and temperature, cooling when being shown with press forming die by steel plate hot forming
The schematic diagram of the relation of time.Fig. 2 (a) shows stamping started temperature situation high, in this case, stamping beginning
Afterwards, the chilling by the radiating to mould, becomes martensite single phase structure.
On the other hand, shown in such as Fig. 2 (b), when stamping started temperature is low, stamping beginning previous existence into ferrite,
Bainite, it is stamping after manufacturing press-molded products intensity decreases.
So, if individually only reducing stamping started temperature, the mode of Fig. 2 (b) is become.
On the other hand, as shown in the curve of the dotted line of Fig. 3, in the present invention, can be anxious before stamping beginning by using
Cold refrigerating work procedure, although reduce shaping started temperature, but martensite single phase structure can be formed.
It should be noted that the upper limit of cooling velocity is usually 500 DEG C/s or so.
Additionally, by the refrigerating work procedure cooling stop temperature being set as 550 DEG C the following is due to：If more than 550 DEG C,
Cooling is insufficient, and micro-crack is generated after hot forming.Preferably less than 500 DEG C.On the other hand, cooling is stopped at temperature
Limit value be set as 410 DEG C be due to：If being less than 410 DEG C, the stamping sub-cooled of preceding surface treated steel plate 1 is stamping
Shape freezing afterwards declines.Preferably more than 430 DEG C.
Cooling velocity and cooling in the refrigerating work procedure stop temperature can be for example, by being kept using cooling with mould 3
The time of surface treated steel plate 1 controls (reference picture 1).Additionally, being caused using the clamping surface of cooling mould 3 treatment steel plate 1
The temperature change of surface treated steel plate 1 can be obtained by following manner：Inserted in the steel plate shown in Fig. 4's
Armoured thermocouple (sheath type thermocouple) 19, determines the temperature of surface treated steel plate 1, thus obtains at surface
Manage the temperature change of steel plate 1.Fig. 5 is a curve map for example for showing the result, and the longitudinal axis represents temperature (DEG C), and transverse axis is represented
Time (s).Additionally, Fig. 6 is the curve map that the transverse axis of the part of the dotted line in Fig. 5 is amplified display.As shown in fig. 6, cold
But it is for about 160 DEG C/s with temperature change when cooling down caused by mould, it is known that it can chilling.
Additionally, as the experiment in an implementation method, to retention time (the especially cooling mould in cooling mould
The cooling of generation stops temperature) and stamping started temperature hereinafter described carry out various change, making manufacturing press-molded products, and
Carry out following evaluations.As assessment item, to have observe a section of the longitudinal wall part of manufacturing press-molded products and confirm micro-crack
The presence or absence of, confirm products formed hardness, confirm stamping load, confirm products formed hat opening portion amount of opening (into
After shape, the difference of the width dimensions of the opening portion after the demoulding and the products formed width of mold shape) confirm shape freezing.
Fig. 7 is and stamping to the cool time (cooling that cooling mould is produced stops temperature) in cooling mould
When started temperature carries out various change, the SEM in the section on the top layer that side is contacted with punch die 13 of the longitudinal wall part of manufacturing press-molded products
Image.As shown in Figure 7, when the cool time in cooling mould is more than 0.9s (below 550 DEG C of stamping started temperature),
Micro-crack is not observed in matrix steel plate.In addition, it is thus identified that at all conditions, equal Hv ＞ 450, the decline without hardenability.
Fig. 8 is the figure for showing stamping started temperature and the relation of stamping load, and the longitudinal axis is stamping load
(kN), transverse axis is stamping started temperature (DEG C).As shown in Figure 8, it is known that：With in stamping preceding cooling mould
The reduction of stamping started temperature caused by cooling, stamping load increases, but on 550 DEG C of left sides of non-microcracked generation
At right temperature, be with mild steel (270D, cold drawing shape) the other stamping load of ad eundem, have no problem.
Fig. 9 is the figure of the relation for showing stamping started temperature and amount of opening, the longitudinal axis for products formed amount of opening (mm),
Transverse axis is stamping started temperature (DEG C).As shown in figure 9, caused by with the cooling in stamping preceding cooling mould
The reduction of stamping started temperature, amount of opening increase shows the tendency that shape freezing declines, but thinks stamping and opens
Beginning temperature is more than 400 DEG C almost without the decline of shape freezing.
As can be known from the above results：Using the cooling mould of regulation, with the cooling velocity of 100 DEG C/more than s by surface
Reason steel plate is cooled to less than 550 DEG C more than 410 DEG C of temperature, further as mentioned below after the cooling period within 5 seconds, and with
Less than 550 DEG C more than 400 DEG C of temperature starts stamping, manufactures non-microcracked with thus can not increasing stamping load
The produce, manufacturing press-molded products with sufficient hardness and shape freezing.
The stamping operation ＞ of ＜
Stamping operation (S2) be by surface treated steel plate 1 it is stamping be the operation of article shape.Stamping work
Sequence is carried out after refrigerating work procedure using press forming die 11.As shown in figure 1, press forming die 11 possesses punch die 13
With drift 17.Also, by stamping to carry out with punch die 13 and the clamping surface of drift 17 treatment steel plate 1, thus it is made into
Body 1 '.
As described above, in refrigerating work procedure, will be surface-treated with the cooling velocity of 100 DEG C/more than s with mould 3 using cooling
Steel plate 1 is cooled to less than 550 DEG C more than 410 DEG C of temperature, then extracts surface treated steel plate 1 out with mould 3 from cooling, with
Less than 550 DEG C more than 400 DEG C of temperature starts stamping, manufactures non-microcracked with thus can not increasing stamping load
The produce, manufacturing press-molded products with sufficient hardness and shape freezing.
Additionally, after refrigerating work procedure, started within 5 seconds stamping operation be due to：If to starting punching press after cooling
The time of shaping more than 5 seconds, then causes the generation of ferrite, bainite etc., it is impossible to obtain martensite before stamping beginning
Homogeneous structure, the hardness of manufacturing press-molded products becomes insufficient.Time after cooling to stamping beginning was preferably within 3 seconds.
It should be noted that being not particularly limited on lower limit, it is usually preferred to be set as more than 1 second.
It is not particularly limited on press-processing method.Can be using punch die 13 and holding pad as shown in Figure 10 (a)
The drawing forming that (blank holder) 15 clamping surfaces treatment steel plate 1 is directly formed, or as shown in Figure 10 (b), can
Being crash forming (crash forming) for declining or not using holding pad 15 and form holding pad 15 etc..From suppression
From the viewpoint of micro-crack processed, the small crash forming of the processing stage of the more preferably longitudinal wall part of manufacturing press-molded products.
＜ quenching process ＞
Quenching process (S3) is the state for keeping being hold using press forming die 11 formed body 1 ' after stamping
Formed body 1 ' is quenched, the operation of hot-forming product is obtained.After stamping, in order to using press forming die 11 pairs into
Body 1 ' is quenched, and after stamping, stops sliding in the case where lower dead center is shaped.Although dwell time is produced according to mould
Heat dissipation capacity and it is different, but preferably more than 3 seconds.Although the upper limit on dwell time is not particularly limited, from productive
Viewpoint consideration, preferably less than 20 seconds.
It should be noted that for the stipulated time being kept in mould and makes matrix steel plate for quenching structure, for example
The hot rolled steel plate or cold-rolled steel sheet constituted with following component can be used, i.e. contain C in terms of quality %：More than 0.15%
Less than 0.50%, Si：Less than more than 0.05% 2.00%, Mn：Less than more than 0.50% 3.00%, P：Less than 0.10%, S：
Less than 0.050%, Al：Less than 0.10%, N：Less than 0.010%, remainder is made up of Fe and inevitable impurity.With
Under this is illustrated into being grouped into.Here, unless otherwise specified, " % " of the content of expression composition refers to " matter
Amount % ".
《C：Less than more than 0.15% 0.50%》
C is the element for improving the intensity of steel, and in order to realize the high intensity of hot-forming product, its amount is preferably 0.15%
More than.On the other hand, if C amounts are more than 0.50%, the weldability of hot-forming product, the punching of raw material (matrix steel plate)
(blanking) property is remarkably decreased.Therefore, C content is preferably less than more than 0.15% 0.50%, more preferably more than 0.20%
Less than 0.40%.
《Si：Less than more than 0.05% 2.00%》
It is the element for improving the intensity of steel that Si is same with C, and for the high intensity of hot-forming product, its amount is preferably
More than 0.05%.On the other hand, if Si amounts are more than 2.00%, during manufacture matrix steel plate, the surface of red rust is referred to as during hot rolling
The generation of defect is significantly increased.Therefore, Si contents are preferably less than more than 0.05% 2.00%, more preferably more than 0.10%
Less than 1.50%.
《Mn：More than 0.50% 3.00%》
Mn is the element of the quenching degree for improving steel, for the iron for suppressing matrix steel plate in the cooling procedure after hot forming
Ferritic phase transformation, make quenching degree improve for be effective element.Additionally, Mn has makes the Ac of steel3The effect of transformation temperature reduction, because
This is effective element for the heating-up temperature low temperature of the surface treated steel plate 1 before making hot forming.In order to show
Such effect, preferably Mn contents are more than 0.50%.On the other hand, if Mn amounts occur segregation, matrix more than 3.00%, Mn
The uniformity of the characteristic of steel plate and hot forming component declines.Therefore, Mn contents are preferably less than more than 0.50% 3.00%, more
Preferably less than more than 0.75% 2.50%.
《P：Less than 0.10%》
If P content is more than 0.10%, P to cyrystal boundary segregation, the low-temperature flexibility decline of matrix steel plate and hot forming component.
Therefore, P content is preferably less than 0.10%, more preferably less than 0.01%.But, excessive P reductions can cause steel operation processed
In cost increase.Therefore, P is preferably more than 0.003%.
《S：Less than 0.050%》
S is with Mn to combine to form thick sulfide and cause the element that the ductility of steel declines.Therefore, S contents are preferred
Reduce as much as possible, but can allow to 0.050%.Therefore, S contents are preferably less than 0.050%, are more preferably
Less than 0.010%.But, excessive S reductions can cause the increase of the desulphurization cost in steel operation processed.Therefore, S is preferably
More than 0.0005%.
《Al：Less than 0.10%》
If Al content is more than 0.10%, the ductility of the increase of oxide system field trash, steel is caused to decline.Therefore, Al
Content is preferably less than 0.10%, more preferably less than 0.07%.But, Al has as the effect of deoxidier, from raising steel
Cleanliness factor from the viewpoint of, its content is preferably more than 0.01%.
《N：Less than 0.010%》
If N content is more than 0.010%, the nitride such as AlN are formed in matrix steel plate, cause shaping during hot forming
The decline of property.Therefore, N content is preferably less than 0.010%, more preferably less than 0.005%.But, excessive N reductions cause
The increase of the cost in steel operation processed.Therefore, N is preferably more than 0.001%.
Above is the preferred basis of the matrix steel plate used as raw material in manufacture method of the invention, but should
Matrix steel plate can also further contain one or more of following element as needed.
Cr：Less than more than 0.01% 0.50%, V：Less than more than 0.01% 0.50%, Mo：More than 0.01% 0.50% with
Under, Ni：Less than more than 0.01 0.50%.
Cr, V, Mo, Ni are the effective elements for improving the quenching degree of steel.The effect is in any of the above-described kind of element
In the case of can be obtained for more than 0.01% by making content.If however, Cr, V, Mo, Ni be content more than 0.50%,
Then the effect above saturation, causes cost to raise.Therefore, in the case of containing one or more of Cr, V, Mo, Ni, preferably each
Content is less than more than 0.01% 0.50%, more preferably less than more than 0.10% 0.40%.
Ti：Less than more than 0.01% 0.20%
Reinforcings of the Ti to steel is effective.The strength-enhancing effect produced by Ti can be by making its content be more than 0.01%
And obtain, as long as therefore present invention provide that in the range of, so that it may for the reinforcing of steel.However, if Ti contents are more than 0.20%,
Then its effect saturation, causes cost to raise.Therefore, in the case of containing Ti, preferably less than more than 0.01% 0.20%, more
Preferably less than more than 0.01% 0.05%.
Nb：Less than more than 0.01% 0.10%
Reinforcings of the Nb to steel is also effective.The strength-enhancing effect produced by Nb can be more than 0.01% by its content
And obtain, as long as therefore present invention provide that in the range of, so that it may for the reinforcing of steel.However, if Nb contents are more than 0.10%,
Then its effect saturation, causes cost to raise.Therefore, in the case of containing Nb, preferably less than more than 0.01% 0.10%, more
Preferably less than more than 0.01% 0.05%.
B：Less than more than 0.0002% 0.0050%
B is the element of the quenching degree for improving steel, for when matrix steel plate after hot forming is cooled, suppressing from austenite
Crystal boundary generation ferrite, obtain for quenching structure being effective element.Its effect can be by B content for more than 0.0002%
Obtain, if B content is more than 0.0050%, its effect saturation causes cost to raise.Therefore, in the case of containing B, it contains
Amount is preferably less than more than 0.0002% 0.0050%.More preferably less than more than 0.0005% 0.0030%.
Sb：Less than more than 0.003% 0.030%
Sb have steel plate is being heated to from before hot forming entering steel plate by a series for the treatment of of hot forming
In a period of untill row cooling, suppress the effect of the decarburized layer in the generation of matrix steel plate skin section.In order to show such effect
Really, Sb contents are preferably more than 0.003%.If however, Sb contents are more than 0.030%, causing when matrix steel plate is manufactured and rolling
The increase of load processed, productivity ratio may decline.Therefore, in the case of containing Sb, its content is preferably more than 0.003%
Less than 0.030%, more preferably less than more than 0.005% 0.010%.
It should be noted that the composition (remainder) beyond mentioned component is Fe and inevitable impurity.
The manufacturing condition for being used as the surface treated steel plate 1 of the raw material of hot forming component in the present invention is not limited especially
System.The manufacturing condition of matrix steel plate is not particularly limited, for example, the (sour into the hot rolled steel plate being grouped into of regulation can will be had
Wash steel plate) or by hot rolled steel plate implement it is cold rolling obtained from cold-rolled steel sheet be used as matrix steel plate.
Additionally, the condition when the surface of matrix steel plate forms Zn-Ni coating so as to be made surface treated steel plate 1 does not have yet
It is particularly limited to.During using hot rolled steel plate (pickled plate) as matrix steel plate, Zn- is implemented by hot rolled steel plate (pickled plate)
The treatment of Ni coating, can be made into surface treated steel plate 1.
On the other hand, during using cold-rolled steel sheet as matrix steel plate, can directly implement at Zn-Ni coating by after cold rolling
Implement the treatment of Zn-Ni coating after managing or being made annealing treatment, thus make surface treated steel plate 1.
Additionally, in the case where matrix surface of steel plate forms Zn-Ni coating, Zn-Ni can be formed for example, by following manner
Coating：By the degreasing of matrix steel plate, pickling, then in nickel sulfate hexahydrate compound, 10g/L containing more than 100g/L below 400g/L
The pH of the Zinc vitriol of below above 400g/L is the plating bath that less than more than 1.0 3.0, bath temperature is less than more than 30 DEG C 70 DEG C
In, with 10A/dm2Above 150A/dm2Following current density carries out electroplating processes, is consequently formed Zn-Ni coating.
It should be noted that using cold-rolled steel sheet as matrix steel plate when, also can be before above-mentioned degreasing, pickling to cold rolling
Steel plate implements annealing.For the Ni contents in coating, by above-mentioned scope to the dense of Zinc vitriol
Degree, current density are suitably adjusted, and can form desired Ni contents (for example, below mass % of more than 9 mass % 25).This
Outward, for the adhesion amount of Zn-Ni coating, desired adhesion amount can be formed (for example, per one side by adjusting conduction time
10g/m2Above 90g/m2Below).
Embodiment
The experiment confirmed to the effect of the manufacture method of hot-forming product of the present invention is carried out, below to it
Illustrate.
Steel melting with the composition shown in table 1 is made slab, the slab is heated to 1200 DEG C, with 870 DEG C of essence
Roll end temp and implement hot rolling, be then wound in 600 DEG C, be made hot rolled steel plate.
[table 1]
Then, pickling is carried out to the hot rolled steel plate, is then carried out with 50% reduction ratio cold rolling, be made thickness of slab 1.6mm's
Cold-rolled steel sheet.Ac described in table 13Transformation temperature is (reference William C.Leslie works, the good fortune calculated by following (1) formula
Tian Chengkang prison translate, Xiong Jinghao, open country Tian Longyan are translated, " Lesley's ferrous materials ", Wan Shan Co., Ltd., 1985, p.273).
Ac3(DEG C)=910-203 [C]0.5+44.7×[Si]-30×[Mn]+700×[P]+400×[Al](1)
It should be noted that in (1) formula, [C], [Si], [Mn], [P], [Al] are the steel of each element (C, Si, Mn, P, Al)
Middle content (quality %).
The cold-rolled steel sheet that will as above obtain forms pure Zn coating, Zn-Fe platings as matrix steel plate on the surface of matrix steel plate
Layer, each coating of Zn-Ni coating and be made surface treated steel plate 1.Each coating is formed under the following conditions.
The pure Zn coating ＞ of ＜
Cold-rolled steel sheet is led into plate in Continuous Hot Dip Galvanizing Line, more than 800 DEG C are heated to the programming rate of 10 DEG C/s
Less than 900 DEG C of temperature range, is detained more than 10s below 120s, then with the cooling velocity of 15 DEG C/s in the temperature range
Less than more than 460 DEG C 500 DEG C of temperature range is cooled to, be impregnated in 450 DEG C of zinc plating bath, be consequently formed Zn coating.Zn coating
Adhesion amount by airblast (gas wiping) method adjust to regulation adhesion amount.
＜ Zn-Fe coating ＞
Cold-rolled steel sheet is led into plate in Continuous Hot Dip Galvanizing Line, more than 800 DEG C are heated to the programming rate of 10 DEG C/s
Less than 900 DEG C of temperature range, is detained more than 10s below 120s, then with the cooling velocity of 15 DEG C/s in the temperature range
Less than more than 460 DEG C 500 DEG C of temperature range is cooled to, be impregnated in 450 DEG C of zinc plating bath, be consequently formed Zn coating.Zn is plated
The adhesion amount of layer is adjusted to the adhesion amount of regulation by airblast method.Adjusted by airblast method to the adhesion amount of regulation
Afterwards, 500~550 DEG C and 5~60s of holding are heated in alloying furnace immediately, Zn-Fe coating is consequently formed.By above-mentioned
In the range of the holdup time under the heating-up temperature in alloying furnace or the heating-up temperature is changed, contain the Fe in coating
Amount is formed as the content of regulation.
＜ Zn-Ni coating ＞
Cold-rolled steel sheet is led into plate in continuous annealing generation line, more than 800 DEG C 900 are heated to the programming rate of 10 DEG C/s
Temperature range below DEG C, more than 10s below 120s are detained in the temperature range, are then cooled to the cooling velocity of 15 DEG C/s
Less than 500 DEG C of temperature range.Then, degreasing, pickling are carried out, then the nickel sulfate hexahydrate compound containing 200g/L, 10~
In the pH 1.3 of the Zinc vitriol of 300g/L, the plating bath of 50 DEG C of bath temperature, with 30~100A/dm2Current density carry out 10
The electroplating processes that~100s is powered, are consequently formed Zn-Ni coating.Zinc vitriol is suitably adjusted by above-mentioned scope
Concentration or current density, by the Ni contents in coating be formed as regulation content.Additionally, by suitable in above-mentioned scope
Regulation conduction time, the adhesion amount of Zn-Ni coating is formed as the adhesion amount of regulation.
The blanket of 200mm × 400mm is punched out from the surface treated steel plate for obtaining in the manner described above, using air gas
The electric furnace of atmosphere is heated to the blanket, and blanket then is arranged at into cooling mould (material：SKD61 in), with shown in table 2
Condition, carries out cooling, the stamping and quenching using mould.Then, after being quenched in mould, the demoulding is carried out, is thus manufactured
The manufacturing press-molded products of the hat section shape shown in Figure 11.The shape of mould uses punch shoulder R：6mm, punch die shoulder R：6mm
Mould, and make drift-punch die gap be 1.6mm.The cooling of the surface treated steel plate before stamping is used by with cooling
The contact of mould is carried out.It is stamping be with apply the drawing forming of the pressure-pad-force direct forming of 98kN with without pressure-pad-force into
The crash forming of shape is carried out.
The heating-up temperature of blanket, the species of matrix steel plate, the species of coating, heating condition, cooling condition and stamping
Condition is as shown in table 2.
Additionally, the longitudinal wall part from the manufacturing press-molded products of the hat section shape for obtaining cuts sample, scanning electron is used
Microscope (SEM) is directed to each sample to 10 visuals field of cross-section on its surface with 1000 times of multiplying power, and micro-crack (is resulted from
The presence or absence of the fine crack of sample surfaces, the interface of insertion coating-matrix steel plate reaches the fine crack of matrix steel intralamellar part),
And the mean depth of micro-crack is investigated.The mean depth of micro-crack is with the flat of the micro-crack depth of arbitrary 20 micro-cracks
The mode of average is obtained.It should be noted that so-called here " micro-crack depth " refers to, as shown in figure 12, micro-crack 21,
From length from the interface of coating 23 and matrix steel plate 25 to the measurable crackle of thickness of slab center direction (in Figure 12, the length of h).
It was observed that micro-crack number less than in the case of 20, it will be observed that whole micro-crack depth mean depth conduct
Micro-crack depth.
Additionally, for the form accuracy of the stamping component for obtaining, by rushing for hat section shape as shown in fig. 13 that
Products formed width W in products formed width W and mold shape after the demoulding of molded product0Difference (W-W0) as amount of opening
Evaluated.
These results are also shown in table 2 in the lump.
Further, the sample for Determination of Hardness is cut from the longitudinal wall part of the manufacturing press-molded products of the hat section shape for obtaining
Product.The hardness in the section of the sample is tried to achieve using micro Vickers.Tested by 9.8N of test load, determined thickness of slab
5 points of direction central portion, are averaged hardness of the value as sample.It should be noted that here, being as the hardness of target
More than 400Hv.
Additionally, cutting the B tension tests of JIS 13 from the longitudinal wall part of the manufacturing press-molded products of the hat section shape for obtaining
Piece.Tension test is carried out according to JIS G 0567 (1998) using the test film for cutting, the drawing under room temperature (22 ± 5 DEG C) is determined
Stretch intensity.It should be noted that tension test is carried out by 10mm/min of crosshead speed.It should be noted that here, making
For the tensile strength of target is more than 1180MPa.
These results are also shown in table 2 in the lump.
[table 2]
In example 1~10, the species (Zn-Ni coating) of coating, cooling means (mould cooling), cool time (0.6s
~1.7s), cooling velocity (proper range：100 DEG C/more than s) and cooling stopping temperature (proper range：410 DEG C~550 DEG C),
To the time (proper range of stamping beginning after cooling：Within 5 seconds), stamping started temperature (400 DEG C of proper range~
550 DEG C) all in proper range.No generation micro-crack, amount of opening are also 0mm in sample after punching press.Thus, it is known that this hair
Bright press-processing method while good shape freezing is ensured, can suppress the generation of micro-crack.
On the other hand, comparative example 1 is not cooled down to form using cooling with mould.Additionally, comparative example 2~
4 coolings stop temperature not in proper range (410 DEG C~550 DEG C).Specifically, it is 600 that the cooling of comparative example 2 stops temperature
DEG C, to stop temperature be 340 DEG C, 290 DEG C for the cooling of comparative example 3,4.
Although amount of opening is 0mm in comparative example 1,2, micro-crack is generated.Thus, it is known that the shaping started temperature of steel plate
During higher than 550 DEG C, micro-crack is produced.
Although not producing micro-crack in comparative example 3,4, amount of opening is 8mm~9mm.Thus, it is known that cool time is long,
In the case that the cooling of steel plate stops temperature less than 410 DEG C, stamping started temperature also below 400 DEG C, in the intensity of steel plate
Rise, cause the decline of shape freezing.
In comparative example 5~7 due to cooling means be gas cooling, therefore cooling velocity not proper range (100 DEG C/s with
On) in, it is impossible to rapidly cooled down.Therefore, comparative example 5, the cooling of 6 light plates stops temperature and stamping started temperature
In proper range, (cooling does not stop temperature：410 DEG C~550 DEG C, stamping started temperature：400 DEG C~550 DEG C) in, produce
Micro-crack.Although additionally, cooled down in comparative example 7 stopping temperature for 510 DEG C, in proper range, amount of opening is 3mm and produces
The decline of shape freezing.It is thought that because gas-cooled cooling velocity is slow, causing to clamp the bending of manufacturing press-molded products
Angle formed by 2 faces of crestal line is more than die angle.
In addition, in comparative example 6,7, because slowly-cooling is to gas-cooled degree, become it is stamping after quenching,
Therefore it is stamping after hardness and tensile strength also reduce.
In comparative example 8,9, compared with 5 seconds as proper range, to stamping beginning time be respectively 10 seconds, 8
Second, it is for a long time.Therefore, in comparative example 8,9, amount of opening is 2mm, additionally, the hardness and tensile strength after stamping are also reduced.
In comparative example 10,11, the species of coating is different, i.e., comparative example 10 is that only the coating of Zn, comparative example 11 are Zn-Fe
Coating.Plating of the stamping started temperature than Zn-Ni for not producing micro-crack only in the coating of the coating of Zn and Zn-Fe
Do not produce the stamping started temperature of micro-crack lower in layer.Therefore, in comparative example 10,11, micro-crack is produced.
Description of reference numerals
1 surface treated steel plate
1 ' formed body
3 cooling moulds
5 molds
7 times moulds
9 lifter pins
11 press forming dies
13 punch dies
15 holding pads
17 drifts
19 thermocouples
21 micro-cracks
23 coating
25 matrix steel plates
Claims (3)
1. the manufacture method of hot-forming product, the manufacture method is to being formed with Zn-Ni coating on the surface of matrix steel plate
Surface treated steel plate implements hot pressing to manufacture the manufacture method of the hot-forming product of hot-forming product, and the manufacture method is included such as
Lower operation：
Above-mentioned surface treated steel plate is heated to Ac3It is more than transformation temperature, less than 1000 DEG C of temperature range；
Using the contact surface with above-mentioned surface treated steel plate for the cooling mould of plane clamps the above-mentioned surface treatment heated
Steel plate, is thus cooled to less than 550 DEG C more than 410 DEG C with the cooling velocity of 100 DEG C/more than s by above-mentioned surface treated steel plate
Temperature；
After above-mentioned cooling within 5 seconds, and above-mentioned surface treated steel plate temperature in the range of less than 550 DEG C more than 400 DEG C,
Start the stamping of above-mentioned surface treated steel plate using press forming die, obtain formed body；With
Above-mentioned formed body is hold using above-mentioned press forming die and it is directly maintained at shaping lower dead center, to above-mentioned shaping
Body is quenched, and obtains hot-forming product.
2. the manufacture method of hot-forming product as claimed in claim 1, wherein, the Zn-Ni platings in above-mentioned surface treated steel plate
Ni contents in layer are below the mass % of more than 9 mass % 25.
3. hot-forming product, the hot-forming product are using the method manufacture described in claim 1 or 2.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014195530A JP6152836B2 (en) | 2014-09-25 | 2014-09-25 | Manufacturing method of hot press-formed product |
| JP2014-195530 | 2014-09-25 | ||
| PCT/JP2015/004533 WO2016047058A1 (en) | 2014-09-25 | 2015-09-07 | Method of manufacturing hot press-formed product, and hot press-formed product |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106714996A true CN106714996A (en) | 2017-05-24 |
| CN106714996B CN106714996B (en) | 2019-07-05 |
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| CN201580049874.9A Expired - Fee Related CN106714996B (en) | 2014-09-25 | 2015-09-07 | The manufacturing method of hot-forming product and hot-forming product |
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| Country | Link |
|---|---|
| US (1) | US20170225215A1 (en) |
| EP (1) | EP3199257B1 (en) |
| JP (1) | JP6152836B2 (en) |
| KR (1) | KR20170036086A (en) |
| CN (1) | CN106714996B (en) |
| MX (1) | MX2017003875A (en) |
| WO (1) | WO2016047058A1 (en) |
Cited By (4)
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|---|---|---|---|---|
| CN111936248A (en) * | 2018-04-13 | 2020-11-13 | 日本制铁株式会社 | Manufacturing method of thermoformed product, press-molded product, die and die set |
| CN112139335A (en) * | 2020-09-09 | 2020-12-29 | 山东钢铁集团日照有限公司 | Preparation method of high-corrosion-resistance easy-to-weld hot-pressed part |
| CN114029699A (en) * | 2021-10-22 | 2022-02-11 | 广东中辉绿建移动房屋科技有限公司 | Preparation method of galvanized roof and integrated house roof |
| CN114645233A (en) * | 2020-12-18 | 2022-06-21 | 通用汽车环球科技运作有限责任公司 | High temperature coating to mitigate weld cracking in resistance welding |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| MX2017008474A (en) * | 2014-12-25 | 2017-10-31 | Nippon Steel & Sumitomo Metal Corp | Panel-shaped molded article and production method for panel-shaped molded article. |
| JP6825747B2 (en) * | 2019-01-31 | 2021-02-03 | Ｊｆｅスチール株式会社 | Hot-pressed members, cold-rolled steel sheets for hot-pressed members, and their manufacturing methods |
| EP3929321B1 (en) | 2019-02-21 | 2023-09-27 | JFE Steel Corporation | Hot-pressed member, cold-rolled steel sheet for hot pressing, and manufacturing methods therefor |
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Also Published As
| Publication number | Publication date |
|---|---|
| EP3199257A1 (en) | 2017-08-02 |
| MX2017003875A (en) | 2017-06-08 |
| WO2016047058A1 (en) | 2016-03-31 |
| US20170225215A1 (en) | 2017-08-10 |
| EP3199257B1 (en) | 2021-02-24 |
| WO2016047058A8 (en) | 2017-01-19 |
| JP2016064440A (en) | 2016-04-28 |
| EP3199257A4 (en) | 2017-12-06 |
| CN106714996B (en) | 2019-07-05 |
| JP6152836B2 (en) | 2017-06-28 |
| KR20170036086A (en) | 2017-03-31 |
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