CN108138289A - Drop stamping component and its manufacturing method - Google Patents

Drop stamping component and its manufacturing method Download PDF

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Publication number
CN108138289A
CN108138289A CN201680061022.6A CN201680061022A CN108138289A CN 108138289 A CN108138289 A CN 108138289A CN 201680061022 A CN201680061022 A CN 201680061022A CN 108138289 A CN108138289 A CN 108138289A
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CN
China
Prior art keywords
less
drop stamping
steel plate
groups
stamping component
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Pending
Application number
CN201680061022.6A
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Chinese (zh)
Inventor
中川功
中川功一
金子真次郎
横田毅
濑户洋
濑户一洋
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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Publication of CN108138289A publication Critical patent/CN108138289A/en
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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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C23C2/04—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
    • C23C2/12—Aluminium 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
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • 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
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • 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
    • C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Abstract

The present invention provides and has both tensile strength TS：The high intensity of more than 1500MPa, uniform elongation uEl：More than 6.0% high ductibility and yield stress YS increases the drop stamping component of the excellent heat treatment hardenability complete characteristic of more than 150MPa when implementing heat treatment (sintering application).The drop stamping component of the present invention is characterized in that, with it is scheduled (particularly 0.090% less than 0.30% low C and 3.5% less than 11.0% high Mn) into be grouped as and be calculated as containing the martensitic phase that more than 70.0% is calculated as with volume fraction and with volume fraction more than 3.0% and less than 30.0% retained austenite phase tissue, dislocation density be 1.0 × 1016/m2More than.

Description

Drop stamping component and its manufacturing method
Technical field
The present invention relates to component, i.e. drop stamping component and its manufactures obtained from drop stamping is formed by sheet metal Method.
Background technology
In recent years, from the viewpoint of the protection of earth environment, the strong fuel efficiency for it is expected automobile improves.Therefore, by force The strong lightweight for requiring body of a motor car.Therefore, in order to not damage safety even if member for automobile is thinned, it is desirable that as this The high intensity of the steel plate of the former material of component.But, it is however generally that, increasing with the intensity of steel plate, formability reduces, therefore, In the manufacture using high-strength steel sheet as the component of former material, the problems such as forming becomes difficulty or shape stability variation is generated.
Therefore, for this problem, the technology of high-strength vehicle component is manufactured to steel plate application drop stamping technique Practicality is obtained.In drop stamping technique, after steel plate is heated to austenitic area, press machine is carried to, is utilized in press machine Die forming is quenched while being the component of intended shape.In cooling procedure (quenching) in the mold, the tissue of component It is undergone phase transition from austenite phase to martensitic phase, thus obtains the high strength component of intended shape.
In addition, recently, from the viewpoint of the safety for ensuring the personnel of taking, it is expected the impact resistance characteristic of member for automobile Raising.In order to meet the expectation, from viewpoint as the ability (impact energy absorbability) for improving energy when absorbing collision Consider, the uniform elongation for improving member for automobile is effective.Therefore, it is expected high intensity strongly and uniform elongation is excellent Drop stamping component.
For such expectation, propose in patent document 1 by hot press-formed method by sheet metal be formed and Obtained hot press-formed article.Hot press-formed article described in patent document 1 has contains C in terms of quality %：0.15~ 0.35%th, Si：0.5~3%, Mn：0.5~2%, P：Less than 0.05%, S：Less than 0.05%, Al：0.01~0.1%, Cr： 0.01~1%, B：0.0002~0.01%, Ti：(content of N) × 4~0.1%, N：0.001~0.01% and surplus by Fe and Inevitable impurity form into being grouped as and in terms of area occupation ratio by martensite：80~97%, retained austenite：3~ 20%th, surplus tissue：Less than 5% tissue formed.According to the technology described in patent document 1, describe：It can be remained There is the metal structure of the retained austenite of appropriate amount, can realize the drop stamping for further improving the intrinsic ductility of formed products Component.
In addition, the excellent drop stamping component of ductility is proposed in patent document 2.Heat punching described in patent document 2 Pressure component is that have to contain C in terms of quality %：0.20~0.40%, Si：0.05~3.0%, Mn：1.0~4.0%, P： Less than 0.05%, S：Less than 0.05%, Al：0.005~0.1%, N：Less than 0.01% and surplus by Fe and inevitably it is miscellaneous Texture into composition and area occupation ratio in entirety is organized shared by ferritic phase be 5~55%, the area shared by martensitic phase The drop stamping component for the microscopic structure that rate is 45~95% and the average grain diameter of ferritic phase and martensitic phase is less than 7 μm, tool There is tensile strength TS：The high intensity of 1470~1750MPa and percentage of total elongation El：More than 8% high ductibility.
Existing technical literature
Patent document
Patent document 1：Japanese Unexamined Patent Publication 2013-79441 bulletins
Patent document 2：Japanese Unexamined Patent Publication 2010-65293 bulletins
Invention content
Problem to be solved by the invention
But in the technology described in patent document 1,2, stretching is realized by the reinforcing of martensitic phase caused by C Intensity TS：The high intensity of more than 1500MPa, but from the viewpoint of impact energy absorbability is improved, there are uniform elongations The problem of becoming inadequate.
In addition, drop stamping component is usually carried out sintering application after the making of the component, during by the sintering application Heat treatment, yield stress YS increase.Here, in order to improve impact resistance characteristic, not only uniform elongation height is important, YS high Be important, it is therefore desirable to heat treatment during by being sintered application be significantly increased as far as possible YS, heat treatment hardenability it is excellent Drop stamping component.But the technology described in patent document 1,2 shows no sign of considering this heat treatment hardenability.
Therefore, in view of the above problems, the purpose of the present invention is to provide have both tensile strength TS：The height of more than 1500MPa Intensity, uniform elongation uEl：More than 6.0% high ductibility and the yield stress YS increasings when implementing heat treatment (sintering application) Add the drop stamping component of the excellent heat treatment hardenability complete characteristic of more than 150MPa and its advantageous manufacturing method.In this theory In bright book, " heat treatment hardenability is excellent " refers to：When being heat-treated to drop stamping component, the yield stress YS after heat treatment And the characteristic that the difference (hereinafter referred to as " Δ YS ") of the yield stress YS before heat treatment is more than 150MPa.
The method for solving problem
To achieve the above object, the present inventor is to tensile strength TS：The heat punching of the high intensity of more than 1500MPa Various factors in pressure component, influencing yield stress YS and uniform elongation uEl has made intensive studies, and as a result obtains following Opinion.
(A) in order to uniform elongation uEl is made to improve the group to more than 6.0% it is necessary to have the retained austenite of appropriate amount It knits.In addition, in order to C：The tissue of the retained austenite with appropriate amount is obtained less than 0.30 mass %, is needed containing 3.5% Above Mn.In addition, Mn also contributes to intensity increase, even if C is less than 0.30%, further high intensity can also ensure that.
(B) dislocation density of drop stamping component has correlation with Δ YS.Then, in order to realize Δ YS：More than 150MPa, The dislocation density for needing to make drop stamping component is 1.0 × 1016/m2More than.
(C) before drop stamping is implemented to the above-mentioned steel plate containing more than 3.5% Mn, which is carried out in advance to add It is kept for 1 hour or more under the predetermined temperature of heat to ferritic-austenitic two-phase temperature range and within this temperature range and 48 is small When below heat treatment, Mn is made to be enriched in austenite, thereby, it is possible to generate the retained austenite of appropriate amount.In addition, by right The steel plate obtained in this way implements scheduled heating process and hot press-formed process, and it is 1.0 × 10 that can obtain dislocation density16/ m2Above drop stamping component.
The present invention is completed based on above-mentioned opinion, and purport forms as described below.
(1) a kind of drop stamping component, which is characterized in that
With containing C in terms of quality %：0.090% less than 0.30%, Mn：3.5% less than 11.0%, Si：0.01~2.5%, P：Less than 0.05%, S：Less than 0.05%, Al：0.005~0.1%, N：Less than 0.01% and surplus by Fe and inevitable impurity form into being grouped as,
With containing the martensitic phase that more than 70.0% is calculated as with volume fraction and with volume fraction be calculated as more than 3.0% and The tissue of less than 30.0% retained austenite phase,
Also, with tensile strength TS：More than 1500MPa and uniform elongation uEl：More than 6.0% tensile properties,
The dislocation density of the drop stamping component is 1.0 × 1016/m2More than.
(2) the drop stamping component as described in above-mentioned (1), wherein, mentioned component composition further contains choosing in terms of quality % From 1 group in following A~E groups or 2 groups or more.
A groups：Selected from Ni：0.01~5.0%, Cu：0.01~5.0%, Cr：0.01~5.0%, Mo：In 0.01~3.0% One or more
B groups：Selected from Ti：0.005~3.0%, Nb：0.005~3.0%, V：0.005~3.0%, W：0.005~3.0% One or more of
C groups：Selected from REM：0.0005~0.01%, Ca：0.0005~0.01%, Mg：One in 0.0005~0.01% Kind is two or more
D groups：Sb：0.002~0.03%
E groups：B：0.0005~0.05%
(3) the drop stamping component as described in above-mentioned (1) or (2), wherein, there is coating on surface.
(4) the drop stamping component as described in above-mentioned (3), wherein, above-mentioned coating is Zn systems coating or Al systems coating.
(5) the drop stamping component as described in above-mentioned (4), wherein, above-mentioned Zn systems coating contains Ni：10~25 mass %.
(6) a kind of manufacturing method of drop stamping component, which is characterized in that have：
Contain C in terms of quality % to having：0.090% less than 0.30%, Mn：3.5% less than 11.0%th, Si：0.01~2.5%, P：Less than 0.05%, S：Less than 0.05%, Al：0.005~0.1%, N：Less than 0.01% And surplus by Fe and inevitable impurity form heated into the steel billet being grouped as, hot rolling and obtain the work of hot rolled steel plate Sequence；
The first temperature that above-mentioned hot rolled steel plate is heated to more than Ac1 points and below Ac3 points is simultaneously protected at this at a temperature of first It holds 1 hour or more and less than 48 hours and then is cooled down and obtain the process of the first former material steel plate；
Above-mentioned first former material steel plate is heated to more than Ac3 points and less than 1000 DEG C of second temperature and in the second temperature The lower heating process for being kept for less than 900 seconds；With
Then implement stamping and quenching simultaneously to above-mentioned first former material steel plate using molding die and obtain hot punching Press the hot press-formed process of component.
(7) manufacturing method of the drop stamping component as described in above-mentioned (6), wherein,
Have in taking a step forward for above-mentioned heating process：
Cold rolling is carried out to above-mentioned first former material steel plate and obtains the process of cold-rolled steel sheet；With
By the way that above-mentioned cold-rolled steel sheet is heated to more than Ac1 points and below Ac3 points and the annealing that keeps and then cool down And the process of the second former material steel plate is obtained,
Also, it replaces above-mentioned first former material steel plate and above-mentioned heating process and above-mentioned heat is carried out to above-mentioned second former material steel plate Stamping process.
(8) manufacturing method of the drop stamping component as described in above-mentioned (6) or (7), wherein, mentioned component composition further with Quality % meters contain 1 group or 2 groups or more in following A~E groups.
A groups：Selected from Ni：0.01~5.0%, Cu：0.01~5.0%, Cr：0.01~5.0%, Mo：In 0.01~3.0% One or more
B groups：Selected from Ti：0.005~3.0%, Nb：0.005~3.0%, V：0.005~3.0%, W：0.005~3.0% One or more of
C groups：Selected from REM：0.0005~0.01%, Ca：0.0005~0.01%, Mg：One in 0.0005~0.01% Kind is two or more
D groups：Sb：0.002~0.03%
E groups：B：0.0005~0.05%
(9) manufacturing method of the drop stamping component as described in any one of above-mentioned (6)~(8), wherein, in above-mentioned heater Sequence takes a step forward with the process for forming coating on the surface of above-mentioned first former material steel plate or above-mentioned second former material steel plate.
(10) manufacturing method of the drop stamping component as described in above-mentioned (9), wherein, above-mentioned coating is Zn systems coating or Al systems Coating.
(11) manufacturing method of the drop stamping component as described in above-mentioned (10), wherein, above-mentioned Zn systems coating contains Ni：10~ 25 mass %.
(12) manufacturing method of the drop stamping component as described in any one of above-mentioned (9)~(11), wherein, above-mentioned coating Adhesion amount is calculated as 10~90g/m with every single side2。
Invention effect
The drop stamping component of the present invention has both tensile strength TS：The high intensity of more than 1500MPa, uniform elongation uEl： More than 6.0% high ductibility and yield stress YS increases the excellent of more than 150MPa when implementing heat treatment (sintering application) It is heat-treated hardenability complete characteristic.In addition, the manufacturing method of drop stamping component according to the present invention, can advantageously result in as above The drop stamping component.
Specific embodiment
(into being grouped as)
The drop stamping component of an embodiment of the invention is illustrated into being grouped as.Hereinafter, as long as no spy Do not mentionlet alone bright, then " quality % " is only denoted as " % ".
C：0.090% less than 0.30%
C is the increased element of intensity for making steel.In addition, in the heat treatment carried out to drop stamping component, using being dissolved C's Dislocation fixation increases yield stress.In order to obtain such effect and ensure tensile strength TS：More than 1500MPa, by C content It is set as more than 0.090%.On the other hand, when C content is more than 0.30%, solution strengthening amount caused by C increases, therefore, It is difficult to adjust the tensile strength TS of drop stamping component to less than 2300MPa.
Mn：3.5% less than 11.0%
Mn is to increase the intensity of steel and be enriched in austenite and make the stability-enhanced element of austenite, It is most important element in the present invention.In order to obtain such effect and ensure tensile strength TS：It more than 1500MPa and uniformly stretches Long rate uEl：More than 6.0%, Mn contents are set as more than 3.5%.On the other hand, when Mn contents are more than 11.0%, Mn institutes The solution strengthening amount increase of generation, accordingly, it is difficult to adjust the tensile strength TS of drop stamping component to less than 2300MPa.
If in the range of above-mentioned C content and Mn contents, can obtain in tensile strength TS：More than 1500MPa And steadily there is the drop stamping structure of tensile properties that uniform elongation is more than 6.0% in the range of preferably shorter than 2300MPa Part.It should be noted that more specifically, in order to ensure tensile strength TS：1500MPa less than 1700MPa intensity, It is preferably set to C：0.090% less than 0.12% and Mn：4.5% less than 6.5% or is set as C： 0.12% less than 0.18% and Mn：3.5% less than 5.5%.In addition, in order to ensure tensile strength TS： 1700MPa is preferably set to C less than the intensity of 1900MPa：0.090% less than 0.12% and Mn： 6.5% less than 8.5% or is set as C：0.12% less than 0.18% and Mn：5.5% less than 7.5%.In addition, in order to ensure tensile strength TS：1800MPa is preferably set to C less than the intensity of 1980MPa： 0.18% less than 0.30% and Mn：3.5% less than 4.5%.In addition, in order to ensure tensile strength TS： 2000MPa is preferably set to C less than the intensity of 2300MPa：0.090% less than 0.12% and Mn： 8.5% less than 11.0% or is set as C：0.12% less than 0.18% and Mn：More than 7.5% and low In 11.0% or being set as C：0.18% less than 0.30% and Mn：4.5% less than 6.5%.
Si：0.01~2.5%
Si is to make the increased element of the intensity of steel using solution strengthening, and such effect, Si contents are set in order to obtain It is more than 0.01%.On the other hand, when Si contents are more than 2.5%, the surface defect for being referred to as red rust is significantly generated in hot rolling, And rolling loads increase.Therefore, Si contents are set as more than 0.01% and less than 2.5%.It should be noted that Si contents are excellent It is selected as more than 0.02%.Si contents are preferably less than 1.5%.
P：Less than 0.05%
P is to be segregated in steel as the presence of inevitable impurity, generation in generations such as crystal boundaries and drop the toughness of component Low dysgenic element, it is expected to be reduced as far as, but can allow to 0.05%.Therefore, P content is set as 0.05% Hereinafter, more preferably it is set as less than 0.02%.In addition, excessive de- P processing can lead to the surging of refining cost, therefore, P content It is preferably set to more than 0.0005%.
S：Less than 0.05%
S inevitably by containing, in steel as sulfide-based field trash exist, make drop stamping component ductility, The reductions such as toughness.Therefore, it is desirable to be reduced as far as S, but can allow to 0.05%.Therefore, S contents be set as 0.05% with Under, more preferably it is set as less than 0.005%.In addition, excessive de- S processing can lead to the surging of refining cost, and therefore, S contents It is preferably set to more than 0.0005%.
Al：0.005~0.1%
Al is the element to play a role as deoxidier, and in order to show such effect, Al content is set as More than 0.005%.On the other hand, Al content be more than 0.1% when, with nitrogen with reference to and generate a large amount of nitride, as former material The punch press process of steel plate, quenching degree reduce.Therefore, Al content is set as more than 0.005% and less than 0.1%.It needs to illustrate , Al content is preferably more than 0.02%.Al content is preferably less than 0.05%.
N：Less than 0.01%
N usually in steel inevitably by containing, but N content be more than 0.01% when, hot rolling, drop stamping heating when The nitride such as AlN are formed, the punch press process of the steel plate as former material, quenching degree reduce.Therefore, N content is set as 0.01% Below.It should be noted that N content is more preferably more than 0.0030%.N content is more preferably less than 0.0050%.In addition, Inevitably contained in the case of not being adjusted especially, N content is less than 0.0025% or so.In addition, due to refining Cost increases, therefore N content preferably is set as more than 0.0025%.
In addition, other than above-mentioned basic composition, can also be set as further containing following optional member Into being grouped as.
A groups：Selected from Ni：0.01~5.0%, Cu：0.01~5.0%, Cr：0.01~5.0%, Mo：In 0.01~3.0% One or more
Ni, Cu, Cr, Mo are the elements that the intensity of steel is made to increase and contribute to quenching degree to improve, can be as needed Selection contains one or more.The content of each element is set as more than 0.01% by such effect in order to obtain.It is another Aspect, from the viewpoint of never making material cost surging, Ni, Cu, Cr content are set as 5.0% hereinafter, Mo contents are set as Less than 3.0%.The preferred content of each element is more than 0.01% and less than 1.0%.
B groups：Selected from Ti：0.005~3.0%, Nb：0.005~3.0%, V：0.005~3.0%, W：0.005~3.0% One or more of
Ti, Nb, V, W are the intensity of steel to be contributed to increase using precipitation strength and contributed to using the miniaturization of crystal grain The element that toughness improves can be selected as needed containing one or more.
Other than the effect that Ti with intensity in addition to increasing, toughness improves, also have and more preferably form nitride than B and make base In the effect that the quenching degree of solid solution B improves.Such effect in order to obtain, Ti contents are set as more than 0.005%.The opposing party Face, when Ti contents are more than 3.0%, in hot rolling, rolling loads extremely increase, and the toughness of drop stamping component reduces.Therefore, In the case of containing Ti, content is set as more than 0.005% and less than 3.0%.It is preferably set to more than 0.01%.It is preferred that It is set as less than 1.0%.
In order to obtain said effect using Nb, Nb contents are set as more than 0.005%.On the other hand, Nb contents are more than When 3.0%, the increase of carbonitride amount, ductility, resistance to delayed fracture reduce.Therefore, in the case of containing Nb, content is set It is set to more than 0.005% and less than 3.0%.It is preferably set to more than 0.01%.It is preferably set to 0.05%.
Other than the effect that V with intensity in addition to increasing, toughness improves, also have and analysed in the form of precipitate or crystal Go out, as hydrogen capture site make resistance to hydrogen embrittlement improve effect.Such effect, V content are set as 0.005% in order to obtain More than.On the other hand, when V content is more than 3.0%, carbonitride amount significantly increases, ductility reduction.Therefore, in the feelings containing V Under condition, content is set as more than 0.005% and less than 3.0%.It is preferably set to more than 0.01%.It is preferably set to 2.0% Below.
Other than the effect that W with intensity in addition to increasing, toughness improves, also there is the effect for improving resistance to hydrogen embrittlement.It is terrible To such effect, W content is set as more than 0.005%.On the other hand, when W content is more than 3.0%, ductility reduction.Cause This, in the case of containing W, content is set as more than 0.005% and less than 3.0%.It is preferably set to more than 0.01%.It is excellent Choosing is set as less than 2.0%.
C groups：Selected from REM：0.0005~0.01%, Ca：0.0005~0.01%, Mg：One in 0.0005~0.01% Kind is two or more
REM, Ca, Mg are to control the element for improving ductility, resistance to hydrogen embrittlement by the form of field trash, can basis Selection is needed containing one or more.The effect in order to obtain, the content of each element are set as more than 0.0005%.It is another Aspect, from the viewpoint of never reducing hot-workability, REM contents, Ca contents are set as less than 0.01%.In addition, from keeping away Exempt from from the viewpoint of making ductility reduction due to the coarse oxide of generation, sulfide, Mg contents are set as less than 0.01%.Respectively The preferred content of element is 0.0006~0.01%.
D groups：Sb：0.002~0.03%
Sb inhibits the formation of the decarburized layer on steel plate surface layer in heating, the cooling of steel plate, therefore, can contain as needed Have.The effect in order to obtain, Sb contents are set as more than 0.002%.On the other hand, when Sb contents are more than 0.03%, can cause The increase of rolling loads, reduces productivity.Therefore, in the case of containing Sb, content be set as more than 0.002% and 0.03% hereinafter, be preferably set to more than 0.002% and less than 0.02%.
E groups：B：0.0005~0.05%
B contributes to quenching degree during drop stamping to improve, the toughness after drop stamping improves, and therefore, can contain as needed. The effect, B content are set as more than 0.0005% in order to obtain.On the other hand, it when B content is more than 0.05%, generates sometimes Generation martensitic phase after the increases of rolling loads during hot rolling, hot rolling, bainite phase and the rupture of steel plate occurs.Therefore, containing In the case of having B, content be set as more than 0.0005% and 0.05% hereinafter, be preferably set to more than 0.0005% and Less than 0.01%.
Surplus other than mentioned component is made of Fe and inevitable impurity.It should be noted that as inevitable Impurity, O (oxygen) can be allowed：Less than 0.0100%.
(tissue)
The tissue of the drop stamping component of an embodiment of the invention is illustrated.
Martensitic phase：More than 70.0% is calculated as with volume fraction
In order to ensure tensile strength TS：More than 1500MPa, need by be calculated as with volume fraction more than 70.0% martensitic phase As main phase.It should be noted that for the retained austenite phase containing desired amount, preferably martensitic phase is at most set as Less than 97%.
Retained austenite phase：3.0~30.0% are calculated as with volume fraction
Retained austenite is mutually to improve uniform elongation, this hair using the TRIP effects (phase change induction plasticity) when deforming Most important tissue in bright.In the present embodiment, in order to realize uniform elongation uEl：More than 6.0%, containing with volume fraction It is calculated as more than 3.0% retained austenite phase.On the other hand, it when the volume fraction of retained austenite phase is more than 30.0%, is showing Going out the hard martensitic phase of phase transformation after TRIP effects becomes excessive, and toughness reduces.Therefore, the volume fraction setting of retained austenite phase It is more than 3.0% and less than 30.0%.The volume fraction of retained austenite phase is preferably set to more than 5.0.Retained austenite phase Volume fraction is preferably set to less than 20.0%.
It should be noted that in order to generate the retained austenite phase of above-mentioned appropriate amount, it is important that：Using containing suitable The steel plate of Mn；Scheduled heat treatment is implemented to the steel plate before drop stamping and Mn is made to be enriched in austenite；Further heat is rushed Heating process during pressure optimizes.
It is calculated as it should be noted that the surplus other than martensitic phase and retained austenite phase can allow to add up to volume fraction Less than 10% (including 0%), bainite phase, ferritic phase, cementite, pearlite.
It should be noted that in the present invention, the determining of the volume fraction of each phase carries out in the following manner.
First, the volume fraction of retained austenite is obtained by the following method.X-ray diffraction is cut from drop stamping component to use Test film implements mechanical lapping, chemical grinding in a manner of making 1/4 face of wall thickness for aspect of measure, then, carries out X-ray diffraction.Enter X ray is penetrated using CoK alpha rays, to { 200 } face of retained austenite (γ), { 220 } face, { 311 } face peak integrated intensity and { 200 } face of ferrite (α), the peak in { 211 } face integrated intensity be measured.For α { 200 }-γ { 200 }, α { 200 }-γ { 220 }, α { 200 }-γ { 311 }, α { 211 }-γ { 200 }, α { 211 }-γ { 220 }, α { 211 }-γ { 311 } amount to 6 groups, respectively It calculates by integrated intensity than the remaining γ volume fractions that are obtained.Using their average value as " volume fraction of retained austenite phase ".
Then, the volume fraction of surplus tissue is obtained by the following method.From drop stamping component so as to be put down with rolling direction It goes and the face vertical with rolling surface cuts structure observation test film for the mode of viewing surface.Viewing surface is ground, profit Corroded with 3 volume % nitals and expose tissue, utilize scanning electron microscope (multiplying power：1500 times) to becoming The tissue of the position of plate thickness 1/4 is observed and is taken pictures.By obtained macrograph, the mirror of tissue is carried out by image analysis Determine and tissue percentage is obtained.By using smoother face compared with unregistered land be observed mutually as ferritic phase, will be in crystal boundary It is membranaceous or it is blocky be observed more in vain mutually as cementite, using ferritic phase and cementite be formed as stratiform mutually as pearl Body of light, by the phase that generation has the phase of carbide and is made of the bainite ferrite without carbide in crystal grain between lath It is accredited as bainite phase.The occupied area rate of each phase in macrograph is obtained, tissue is considered as three dimensional homogenous, therefore, by face Product rate is as volume fraction.
" volume fraction of martensitic phase " is set as subtracting the volume fraction and residual austenite of above-mentioned surplus tissue from 100% Value obtained from the volume fraction of body phase.
(dislocation density)
Dislocation density：1.0×1016/m2More than
The dislocation density of drop stamping component is most important index in the present invention for influence Δ YS.Think to drop stamping component When implementing heat treatment (sintering application), solid solution C is fixed on mobile dislocation, yield stress YS raisings.In order to realize Δ YS：150MPa More than, the dislocation density for needing drop stamping component is 1.0 × 1016/m2More than.The upper limit of dislocation density is essentially 5.0 × 1016/m2.The dislocation density of drop stamping component is preferably 1.2 × 1016/m2More than.The dislocation density of drop stamping component is preferably 4.5×1016/m2Below.
In the present invention, dislocation density is obtained by the following method.X-ray diffraction experiment is cut from drop stamping component Piece implements mechanical lapping, chemical grinding in a manner of making 1/4 face of wall thickness for aspect of measure, then, carries out X-ray diffraction.Incident X Ray uses CoK α1Ray, practical measurement α { 110 }, α { 211 }, α { 220 } peak half-peak breadth.Use the standard of no strain The half-peak breadth at peak of the α { 110 } of practical measurement, α { 211 }, α { 220 } are corrected to true value half-peak breadth by test film (Si), then, Strain (ε) is obtained based on Williamson-Hall (Willaimson-Hall) method.Dislocation density (ρ) by using strain (ε) and Burgers vector (b=0.286nm) is obtained using following formula.
ρ=14.4 × ε2/b2
(characteristic)
The drop stamping component of present embodiment has tensile strength TS：The height of more than 1500MPa, preferably shorter than 2300MPa Intensity, uniform elongation uEl：More than 6.0%, be essentially less than 20% high ductibility and Δ YS be more than 150MPa, it is real It is the characteristic of below 300MPa in matter.
(coating)
The drop stamping component of an embodiment of the invention preferably has coating.
In the case where the steel plate used as the former material of drop stamping component is coated steel sheet, in obtained drop stamping structure The surface layer of part can remain coating.In this case, oxide skin generation is can inhibit during the heating of drop stamping.Therefore, it is possible to not into By drop stamping component for using in the case of the oxide skin stripping on row surface, productivity improves.
Coating is preferably set to Zn systems coating or Al systems coating.In the case where needing corrosion resistance, with Al systems coating phase Than Zn systems coating is more excellent.This is because, using the sacrifice corrosion-resisting function of zinc, the corrosion rate of base steel can be reduced.Separately Outside, in the case where carrying out drop stamping to coated steel sheet, the heating initial stage in drop stamping process forms Zinc oxide film, later Drop stamping component processing in can prevent the evaporation of Zn.
It should be noted that as Zn systems coating, general hot galvanized layer (GI), alloyed hot-dip zinc layers are may be exemplified (GA), Zn-Ni systems coating etc., wherein, preferred Zn-Ni systems coating.Zn-Ni systems coating can be significantly inhibited when drop stamping is heated Oxide skin generates, but also can prevent liquid metal embrittlement.From the viewpoint of the effect is obtained, Zn-Ni systems coating is preferred Ni containing 10~25 mass %.Even if containing the Ni for having more than 25%, the effect also saturation.
As Al systems coating, Al-10 mass %Si coating may be exemplified.
(manufacturing method)
The manufacturing method of drop stamping component in an embodiment of the invention is illustrated.First, to upper That states is heated into the steel billet being grouped as, and is carried out hot rolling, is obtained hot rolled steel plate.Then, the hot rolled steel plate is implemented aftermentioned Scheduled heat treatment (Mn enrichments heat treatment), obtains the first former material steel plate.Then, optionally above-mentioned first former material steel plate is carried out Cold rolling obtains cold-rolled steel sheet, then carries out scheduled annealing to the cold-rolled steel sheet, obtains the second former material steel plate.
Scheduled heating process and hot press-formed is carried out to the first former material steel plate obtained in this way or the second former material steel plate Process obtains drop stamping component.Hereinafter, each process is described in detail.
＜ obtains the process ＞ of hot rolled steel plate
The process for obtaining hot rolled steel plate is not particularly limited, and carries out according to conventional methods.It will be with above-mentioned ingredient The molten steel of composition carries out melting using converter etc., and preferably steel billet is made by continuous metal cast process in gross segregation in order to prevent.It needs to illustrate , continuous metal cast process can also be replaced using ingot casting method or sheet blank continuous casting method.
After obtained steel billet is temporarily cooled to room temperature, it is encased in heating furnace to be reheated.But It can apply and steel billet is not cooled to room temperature and the technique in heating furnace is encased in warm piece state, steel billet is subjected to short time guarantor The energy saving techniques such as the technique of hot rolling are carried out after heat immediately.
After obtained heating steel billet to scheduled heating temperature, carry out hot rolling and hot rolled steel plate is made.As heating Temperature may be exemplified 1000~1300 DEG C.By the steel billet after heating usually finish rolling entrance side temperature be less than 1100 DEG C, finish rolling Outlet side temperature carries out hot rolling under conditions of being 800~950 DEG C, is carried out under conditions of average cooling rate is 5 DEG C/more than s Cooling, coiled material shape is batched under 300~750 DEG C of coiling temperature, hot rolled steel plate is made.
＜ Mn enrichment heat treatments ＞
Then, hot rolled steel plate is heated to the first temperature more than Ac1 points and below Ac3 points, is protected at a temperature of first at this It holds 1 hour or more and 48 hours hereinafter, then cooled down, obtains the first former material steel plate.The processing is that Mn is made to be enriched in Ovshinsky Processing in body becomes for manufacturing the retained austenite with appropriate amount and realizes uniform elongation uEl：More than 6.0%, simultaneously And dislocation density is made to be 1.0 × 1016/m2Δ YS is realized above：The most important technique of the drop stamping component of more than 150MPa.
Heating temperature：More than Ac1 points and below Ac3 points
Hot rolled steel plate is heated to ferritic-austenitic two-phase temperature range, Mn is made to be enriched in austenite.For enrichment For having the austenite of Mn, martensitic traoformation end temp is room temperature hereinafter, easily generating retained austenite.Heating temperature is less than During Ac1 points, austenite will not be generated, Mn can not be made to be enriched with to austenite.On the other hand, when heating temperature is more than Ac3 points, become Austenite one phase temperature range, enrichments of the Mn to austenite will not carry out.In addition, heating temperature less than Ac1 points situation and In the case that heating temperature is more than Ac3 points, the dislocation density that can not make drop stamping component is 1.0 × 1016/m2More than.Therefore, Heating temperature is set as more than Ac1 points and below Ac3 points.Heating temperature is preferably set to more than (+20 DEG C of Ac1 points).Heating temperature Degree is preferably set to (- 20 DEG C of Ac3 points) below.
It should be noted that Ac1 points (DEG C) and Ac3 points (DEG C) use the value calculated using following formula.
Ac1 points (DEG C)=751-16C+11Si-28Mn-5.5Cu-16Ni+13Cr+3.4Mo
Ac3 points (DEG C)=910-203C1/2+44.7Si-4Mn+11Cr
Here, C, Si, Mn, Ni, Cu, Cr, Mo in formula are the content (quality %) of each element, above-mentioned element is not being contained When, the content of the element is calculated with zero.
Heated hold time：1 hour or more and less than 48 hours
Mn is elapsed to the enrichment heat tracing retention time of austenite and is carried out.When heated hold time is less than 1 hour, Mn Enrichment to austenite is insufficient, cannot get desired uniform elongation.In addition, when heated hold time is less than 1 hour, Mn is rich Collect insufficient, the Ms points in drop stamping process will not reduce, and the dislocation density that can not make drop stamping component is 1.0 × 1016/m2With On.On the other hand, when heated hold time is more than 48 hours, pearlite is generated, cannot get desired uniform elongation.In addition, The dislocation density that can not make drop stamping component is 1.0 × 1016/m2More than.Therefore, heated hold time is set as 1 hour or more And less than 48 hours.Heated hold time is preferably set to 1.5 hours or more.Heated hold time be preferably set to 24 hours with Under.
It should be noted that Ms points (DEG C) use the value calculated using following formula.
Ms points (DEG C)=539-423C-30.4Mn-17.7Ni-12.1Cr-7.5Mo
Here, C, Mn, Ni, Cr, Mo in formula are the content (quality %) of each element, it, will when not containing above-mentioned element The content of the element is calculated with zero.
Cooling after heating is kept is not particularly limited, but is preferably appropriately set at certainly according to used heating furnace etc. So cooling (slow cooling) or control cooling.
Mn enrichment heat treatments are carried out preferably by batch anneal stove or continuous annealing furnace.About utilization batch anneal stove Treatment conditions, other than above-mentioned condition, be not particularly limited, for example, from Mn enrichment from the viewpoint of, preferably will heating speed Degree is set as 40 DEG C/h or more, the cooling velocity heated after keeping is set as 40 DEG C/h or more.In addition, about utilization The treatment conditions of continuous annealing furnace in addition to the foregoing, are also not particularly limited, for example, from the viewpoint of manufacturing, preferably Following processing：After carrying out above-mentioned heating and keeping, hot rolled steel plate is cooled to the average cooling rate of 10 DEG C/more than s Cooling in 350~600 DEG C of temperature ranges stops temperature, then stops 10~300 seconds, then carries out cold within this temperature range But it, batches.
The the first former material steel plate made in this way can be used as drop stamping with steel plate.The spy of the tissue of first former material steel plate Sign is, when being set as Mns by the Mn concentration in the second phase of lath-shaped, the Mn concentration in the ferrite of lath-shaped be set as Mn α, Mns/Mn α are more than 1.2." the second phase " refers to surplus tissue (austenite, martensite, pearlite, the bayesian other than ferrite Body).Mns/Mn α are insufficient less than 1.2 enrichments for meaning Mn to austenite, can not be obtained after drop stamping process adequately Even elongation and dislocation density.
＜ obtains the process ＞ of cold-rolled steel sheet
It is then possible to not by the first former material steel plate for aftermentioned heating process and hot press-formed process, and to first Former material steel plate carries out cold rolling, and cold-rolled steel sheet is made.Reduction ratio during about cold rolling, in order to prevent carry out after annealing, will Abnormal grain growth during heating process before drop stamping, is preferably set to more than 30%, is more preferably set as more than 50%. In addition, since rolling load increase, productivity reduce, reduction ratio is preferably set to less than 85%.
＜ annealing operations ＞
Then, by the way that cold-rolled steel sheet is heated to more than Ac1 points and below Ac3 points and what is kept and then cool down moves back Fire obtains the second former material steel plate.Annealing temperature is preferably set to the predetermined temperature more than Ac1 points and below Ac3 points.This be for Further promote enrichments of the Mn to austenite in the annealing operation.Retention time under the predetermined temperature does not limit especially It is fixed, preferably 30 seconds or more and less than 300 seconds.If 30 seconds or more, then the effect of Mn enrichments can be fully obtained, if 300 seconds Hereinafter, it will not then damage productivity.
It should be noted that the process for carrying out pickling, the work for carrying out temper rolling can be suitably added between each process Sequence, this is self-evident.
The the second former material steel plate made in this way can be used as drop stamping with steel plate.The spy of the tissue of second former material steel plate Sign is, ferritic average grain diameter is less than 10 μm, the average grain diameter of the second phase is 10 μm hereinafter, the Mn in the second phase is dense When degree is set as Mns, the Mn concentration in ferrite is set as Mn α, Mns/Mn α are more than 1.5.It is it should be noted that " ferritic Average grain diameter " and " average grain diameter of the second phase " are obtained by the following method.From the second former material steel plate so that and rolling direction Parallel and vertical with rolling surface face cuts structure observation test film for the mode of viewing surface.Viewing surface is ground, Corroded using 3 volume % nitals and expose tissue, utilize scanning electron microscope (multiplying power：1500 times) into The tissue of position for plate thickness 1/4 is observed and is taken pictures.By obtained macrograph, based on the benchmark of above description to group It knits and is identified.The average grain diameter of ferrite and the second phase is obtained by JIS G 0551 (2005) segment methods recorded.
Mns/Mn α are obtained by the following method.After cutting structure observation test film, viewing surface is ground, profit Corroded with 3 volume % nitals and expose tissue, utilize EPMA (Electron Probe Micro Analyzer；Electron probe microanalyzer) tissue of position to becoming plate thickness 1/4 observes, for ferrite and Respectively 30 particles carry out the quantitative analysis of Mn for two-phase.About the quantitative analysis results of Mn, ferritic average value is set as Mn α, the average value of the second phase is set as Mns, by value obtained from the average value Mns of the second phase divided by ferritic average value Mn α It is set as Mns/Mn α.
＜ plating process ＞
In the case of not forming coating on the surface of the first former material steel plate or the second former material steel plate, need in drop stamping process The oxide skins lift-off processings such as shot-peening are carried out to drop stamping component afterwards.In contrast, in the first former material steel plate or the second former material steel plate Surface formed coating in the case of, can inhibit in the heating of drop stamping oxide skin generation, therefore, there is no need to drop stamping process Oxide skin lift-off processing afterwards, productivity improve.
The adhesion amount of coating is preferably set to 10~90g/m in terms of every single side2, more preferably it is set as 30~70g/m2.This is Because adhesion amount 10g/m2More than when, can fully be inhibited heating when oxide skin generation effect, adhesion amount is 90g/m2When following, productivity will not be hindered.The ingredient of coating is as described above.
＜ heating processes ＞
Then, into be about to the first former material steel plate or the second former material steel plate be heated to more than Ac3 points and less than 1000 DEG C Two temperature simultaneously keep the heating process of less than 900 seconds under the second temperature.
Heating temperature：More than Ac3 points and less than 1000 DEG C
When heating temperature is lower than the Ac3 points as austenite one phase area, austenitizing becomes inadequate, and can not make drop stamping Component ensures desired martensite volume, cannot get desired tensile strength.In addition, the dislocation density that can not make drop stamping component is 1.0×1016/m2More than, it is impossible to realize Δ YS：More than 150MPa.On the other hand, it when heating temperature is more than 1000 DEG C, is enriched in Mn in austenite is homogenized, and can not ensure desired remained austenite content, cannot get desired uniform elongation.In addition, Due to the homogenization of Mn, the reduction of Ms points can not be made, the dislocation density that can not make drop stamping component is 1.0 × 1016/m2More than, no It can realize Δ YS：More than 150MPa.Therefore, heating temperature is set as more than Ac3 points and less than 1000 DEG C.Heating temperature is preferably set It is set to (Ac3 points+30) DEG C or more.Heating temperature is preferably set to less than 950 DEG C.
The speed to heat up to heating temperature (second temperature) is not particularly limited, and is preferably set to 1~400 DEG C/s, more excellent Choosing is set as 10~150 DEG C/s.When heating rate is 1 DEG C/more than s, productivity will not be damaged, heating rate for 400 DEG C/s with When lower, temperature control will not become unstable.
Retention time：Less than 900 seconds (including 0 second)
Along under heating temperature (second temperature) retention time elapse, the Mn being enriched with to surrounding spread and it is uniform Change.Therefore, when the retention time is more than 900 seconds, it can not ensure desired remained austenite content, cannot get desired even elongation Rate.In addition, due to the homogenization of Mn, the reduction of Ms points can not be made, the dislocation density that can not make drop stamping component is 1.0 × 1016/m2 More than, it is impossible to realize Δ YS：More than 150MPa.Therefore, the retention time is set as less than 900 seconds.Retention time can be 0 second, Heating is immediately finished after reaching second temperature.
Heating means are not particularly limited, as common heating means, electric furnace, gas furnace, infrared heating, high frequency Heating, direct-electrifying heating etc. can apply.In addition, about atmosphere, also it is not particularly limited, in air, inactive gas Atmosphere is medium can be applied.
The hot press-formed process ＞ of ＜
In hot press-formed process, using molding die to the first former material steel plate or second after heating process Former material steel plate implements stamping and quenching simultaneously, obtains the drop stamping component of predetermined shape." hot press-formed " is will to heat The technique that sheet metal afterwards is quenched while carrying out stamping using mold, also referred to as " hot forming ", " drop stamping Forming (hot stamping) ", " die quenching " etc..
Forming start temperature in press machine is not particularly limited, and is preferably set to more than Ms points.It is low to shape start temperature When Ms points DEG C, forming loading increase, being applied to the load of press machine increases.It should be noted that until forming starts In the carrying of former material steel plate, it is usually set to air-cooled.Therefore, the upper limit for shaping start temperature is close to before in manufacturing process Above-mentioned heating process in heating temperature.It is carried out in the environment of accelerating cooling velocity using refrigerants such as gas, liquid In the case of carrying, cooling velocity is reduced preferably by heat insulating fixtures such as thermal protection casees.
Cooling velocity in mold is not particularly limited, average cold until near 200 DEG C from the viewpoint of productivity But speed is preferably set to 20 DEG C/more than s, is more preferably set as 40 DEG C/more than s.
About from the cooling velocity after the time and taking-up that mold takes out, it is not particularly limited.As cooling means, such as Plunger chip die in bottom dead centre is kept for 1~60 second, drop stamping component is cooled down using punching die and plunger chip die.So Afterwards, drop stamping component is taken out from mold, is cooled down.It in mold and can be combined from the cooling after mold taking-up and utilize gas The cooling means of the refrigerants such as body, liquid can also improve productivity as a result,.
Embodiment
It will be small-sized true with being utilized shown in table 1 and table 4 into the molten steel for being grouped as (surplus is Fe and inevitable impurity) Empty melting furnace carries out melting, and steel billet is made.By heating steel billet to 1250 DEG C, the hot rolling comprising roughing and finish rolling is further carried out, Obtain hot rolled steel plate.It is 1100 DEG C to be set as finish rolling entrance side temperature, and finish rolling outlet side temperature is 850 DEG C of condition.Hot rolling knot Cooling velocity after beam is set as 15 DEG C/s in terms of 800~600 DEG C of average value, and coiling temperature is set as 650 DEG C.
Obtained hot rolled steel plate is heated to the heating temperature T1 (the first temperature) of table 2 and table 5, is kept at such a temperature It time shown in table 2 and table 5, is then cooled down, obtains the first former material steel plate.In A partial experiment example, to the first former material Steel plate carries out pickling, carries out cold rolling with 54% reduction ratio, cold-rolled steel sheet (plate thickness is made：1.6mm).And then by cold-rolled steel sheet The heating temperature T2 of table 2 and table 5 is heated to, then the time shown in holding table 2 and table 5 is carried out cold with 15 DEG C/s of cooling velocity But, stop cooling at 500 DEG C, keep 150s at such a temperature, obtain the second former material steel plate.
In the test example that cold rolling is not carried out, structure observation is carried out to the first former material steel plate, passes through the method for above description Mns/Mn α are obtained.It shows the result in table 2 and table 5.In addition, in test example in addition to this, the second former material steel plate is carried out Ferritic average grain diameter, the average grain diameter of the second phase and Mns/Mn α is obtained by the method for above description in structure observation.It will As a result it is shown in table 2 and table 5.
As shown in table 2 and table 5, in A partial experiment example, plating is implemented to the second former material steel plate.Table 2 and table 5 In, " GI " is hot galvanized layer, " GA " is alloyed hot-dip zinc layers, " Zn-Ni " is Zn-12 mass %Ni coating, " Al-Si " is Al-10 mass %Si coating, the adhesion amount of coating is 60g/m in terms of every single side2。
For the hot rolled steel plate (the first former material steel plate) or cold-rolled steel sheet (the second former material steel plate) obtained in this way, in 3 He of table Implement heating process and hot press-formed process under conditions of shown in table 6, obtain the drop stamping component of hat shape.Drop stamping uses wide Degree：70mm, shoulder radius R：The plunger chip die of 6mm and shoulder radius R：The punching die of 7.6mm is carried out with the Forming depth of 30mm.
It should be noted that the feelings that the heating process before hot press-formed process is carried out in an atmosphere using electric furnace Under condition, heating speed from room temperature to 750 DEG C of average value to be calculated as 7.5 DEG C/s.From 750 DEG C to the heating speed of heating temperature with Average value is calculated as 2.0 DEG C/s.In the case where being kept after reaching heating temperature, kept under the heating temperature.Separately Outside, in the case where direct-electrifying heating device is used to carry out in an atmosphere, heating speed is with flat from room temperature to heating temperature Mean value is calculated as 100 DEG C/s.It is 750 DEG C to shape start temperature.In addition, in cooling, plunger chip die is kept into 15s, profit in bottom dead centre With using punching die and what plunger chip die carried out sandwiches with being cooled to 150 DEG C from the air-cooled combination sandwiched on open punch die Below.Average cooling rate from forming start temperature to 200 DEG C is 100 DEG C/s.
To 170 DEG C of obtained drop stamping component implementation, the heat treatment (Low Temperature Heat Treatment) of 20 minutes.This is equivalent to usually Automobile component manufacturing process in sintering application condition.Before and after the Low Temperature Heat Treatment, from the position of crown plate portion It puts and cuts No. 5 tension test sheet (parallel portions of JIS：25mm wide, parallel portion length：60mm, GL=50mm), based on JIS Z 2241 implement tension test, and yield stress YS, tensile strength TS, percentage of total elongation tEl and uniform elongation uEl is obtained.By result It is shown in table 3 and table 6.
In addition, by the method for above description to volume fraction, the remnants of the martensitic phase in obtained drop stamping component The volume fraction of austenite phase, the volume fraction of surplus tissue and dislocation density are measured, and are shown the result in table 3 and table 6.
Example of the present invention can realize tensile strength TS：More than 1500MPa, uniform elongation uEl：More than 6.0% and Δ YS：More than 150MPa.In contrast, comparative example is unsatisfactory for a certain item characteristic.
Industrial availability
The drop stamping component of the present invention, which can be suitable as collision prevention girders, central post, bumper of automobile etc., needs high touch The structural elements for hitting energy absorption capability uses.

Claims (12)

1. a kind of drop stamping component, which is characterized in that
With containing C in terms of quality %：0.090% less than 0.30%, Mn：3.5% less than 11.0%, Si： 0.01~2.5%, P：Less than 0.05%, S：Less than 0.05%, Al：0.005~0.1%, N：Less than 0.01% and surplus by Fe With inevitable impurity form into being grouped as,
With containing the martensitic phase that more than 70.0% is calculated as with volume fraction and with volume fraction be calculated as more than 3.0% and 30.0% with Under retained austenite phase tissue,
Also, with tensile strength TS：More than 1500MPa and uniform elongation uEl：More than 6.0% tensile properties,
The dislocation density of the drop stamping component is 1.0 × 1016/m2More than.
2. drop stamping component as described in claim 1, wherein, it is described into being grouped as further in terms of quality % containing being selected from down 1 group or 2 groups or more in A~E groups is stated,
A groups：Selected from Ni：0.01~5.0%, Cu：0.01~5.0%, Cr：0.01~5.0%, Mo：One in 0.01~3.0% Kind is two or more,
B groups：Selected from Ti：0.005~3.0%, Nb：0.005~3.0%, V：0.005~3.0%, W：In 0.005~3.0% One or more,
C groups：Selected from REM：0.0005~0.01%, Ca：0.0005~0.01%, Mg：One kind in 0.0005~0.01% or It is two or more,
D groups：Sb：0.002~0.03%,
E groups：B：0.0005~0.05%.
3. drop stamping component as claimed in claim 1 or 2, wherein, there is coating on surface.
4. drop stamping component as claimed in claim 3, wherein, the coating is Zn systems coating or Al systems coating.
5. drop stamping component as claimed in claim 4, wherein, Zn systems coating contains Ni：10~25 mass %.
6. a kind of manufacturing method of drop stamping component, which is characterized in that have：
Contain C in terms of quality % to having：0.090% less than 0.30%, Mn：3.5% less than 11.0%, Si：0.01~2.5%, P：Less than 0.05%, S：Less than 0.05%, Al：0.005~0.1%, N：Less than 0.01% and surplus by What Fe and inevitable impurity were formed heated into the steel billet being grouped as, hot rolling and obtain the process of hot rolled steel plate；
The first temperature that the hot rolled steel plate is heated to more than Ac1 points and below Ac3 points simultaneously keeps 1 small at a temperature of first at this When more than and less than 48 hours and then cooled down and obtain the process of the first former material steel plate；
The first former material steel plate is heated to more than Ac3 points and less than 1000 DEG C of second temperature and is protected under the second temperature Hold the heating process of less than 900 seconds；With
Then implement stamping and quenching simultaneously to the first former material steel plate using molding die and obtain drop stamping structure The hot press-formed process of part.
7. the manufacturing method of drop stamping component as claimed in claim 6, wherein,
Have in taking a step forward for the heating process：
Cold rolling is carried out to the first former material steel plate and obtains the process of cold-rolled steel sheet；With
By the cold-rolled steel sheet is heated to more than Ac1 points and below Ac3 points and the annealing that keeps and then cool down and To the process of the second former material steel plate,
Also, it replaces the first former material steel plate and the heating process and the drop stamping is carried out to the second former material steel plate Forming process.
8. the manufacturing method of drop stamping component as claimed in claims 6 or 7, wherein, it is described into being grouped as further with matter It measures % meters and contains 1 group or 2 groups or more in following A~E groups,
A groups：Selected from Ni：0.01~5.0%, Cu：0.01~5.0%, Cr：0.01~5.0%, Mo：One in 0.01~3.0% Kind is two or more,
B groups：Selected from Ti：0.005~3.0%, Nb：0.005~3.0%, V：0.005~3.0%, W：In 0.005~3.0% One or more,
C groups：Selected from REM：0.0005~0.01%, Ca：0.0005~0.01%, Mg：One kind in 0.0005~0.01% or It is two or more,
D groups：Sb：0.002~0.03%,
E groups：B：0.0005~0.05%.
9. the manufacturing method of the drop stamping component as described in any one of claim 6~8, wherein, the heating process it It takes a step forward with the process for forming coating on the surface of the first former material steel plate or the second former material steel plate.
10. the manufacturing method of drop stamping component as claimed in claim 9, wherein, the coating is plated for Zn systems coating or Al systems Layer.
11. the manufacturing method of drop stamping component as claimed in claim 10, wherein, Zn systems coating contains Ni：10~25 Quality %.
12. the manufacturing method of the drop stamping component as described in any one of claim 9~11, wherein, the attachment of the coating Amount is calculated as 10~90g/m with every single side2。
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Application publication date: 20180608