WO2021103805A1 - 具有优异漆膜附着力的热成形部件及其制造方法 - Google Patents

具有优异漆膜附着力的热成形部件及其制造方法 Download PDF

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Publication number
WO2021103805A1
WO2021103805A1 PCT/CN2020/118368 CN2020118368W WO2021103805A1 WO 2021103805 A1 WO2021103805 A1 WO 2021103805A1 CN 2020118368 W CN2020118368 W CN 2020118368W WO 2021103805 A1 WO2021103805 A1 WO 2021103805A1
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Prior art keywords
paint film
film adhesion
thermoformed part
layer
excellent paint
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PCT/CN2020/118368
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English (en)
French (fr)
Inventor
谭宁
刘浩
洪继要
金鑫焱
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宝山钢铁股份有限公司
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Filing date
Publication date
Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Priority to US17/779,266 priority Critical patent/US20230002843A1/en
Priority to EP20893836.5A priority patent/EP4067530A4/en
Priority to BR112022009756A priority patent/BR112022009756A2/pt
Priority to JP2022530312A priority patent/JP7326612B2/ja
Priority to AU2020389982A priority patent/AU2020389982A1/en
Priority to MX2022006471A priority patent/MX2022006471A/es
Priority to KR1020227020168A priority patent/KR20220106776A/ko
Priority to CA3159490A priority patent/CA3159490A1/en
Publication of WO2021103805A1 publication Critical patent/WO2021103805A1/zh
Priority to ZA2022/05445A priority patent/ZA202205445B/en

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/0242—Flattening; Dressing; Flexing
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • 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
    • C23C2/405—Plates of specific length
    • 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
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • 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
    • C21D2251/00—Treating composite or clad material
    • 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
    • C21D2261/00—Machining or cutting being involved

Definitions

  • the invention relates to a material and a manufacturing method thereof, in particular to a thermoformed material and a manufacturing method thereof.
  • thermoformed parts In recent years, the application of thermoformed parts in the automotive industry has become very important, especially in terms of automotive safety structural parts, which have irreplaceable advantages in some high-strength, complex-shaped parts.
  • the materials used for hot forming parts are divided into coated and uncoated materials.
  • the main purpose of the coating is to prevent oxidation of the steel sheet surface during the hot stamping process.
  • the formed parts can be directly painted and welded.
  • materials without coating must be surface shot peened after hot forming to remove the oxide layer generated on the surface, otherwise the subsequent part painting and welding will be affected.
  • the material of the hot-dip aluminum coating layer cannot be normally phosphated after hot forming, and the adhesion of the paint film after electrophoresis is completely guaranteed by the surface morphology of the coating.
  • Existing materials have the problem that the paint film adhesion cannot satisfy the use during the use process.
  • the publication number is CN104651590A
  • the publication date is May 27, 2015
  • the Chinese patent document titled "Method for manufacturing stamping products and stamping products manufactured therefrom” discloses a hot forming of aluminum or aluminum alloy coating Material and manufacturing method. This method specifically controls the thickness of the coating layer and the five-layer structure to ensure the welding performance of the hot formed parts.
  • the publication number is CN108588612A
  • the publication date is September 28, 2018,
  • the Chinese patent document entitled "Hot stamping forming components, pre-coated steel sheets for hot stamping forming and hot stamping forming process” discloses a hot stamping Forming components.
  • the thickness of the coating is reduced, and the protective effect of the coating is also reduced. Therefore, the fluctuation of the thermoforming process can easily affect the surface properties of the component, thereby affecting the subsequent Use performance.
  • the publication number is CN101583486
  • the publication date is November 18, 2009
  • the name is "coated steel strip, its preparation method, its use method, the stamping blank prepared therefrom, the stamping product prepared therefrom
  • the Chinese Patent Document "Products Containing Such Stamped Products” discloses a hot stamped product and method for coating steel strips.
  • it includes heating, transfer and cooling, but does not involve the hot stamping process, which will cause unstable quality of stamped products, such as shrinkage, cracking, etc., and do not control the furnace atmosphere during the heating process.
  • Resulting in changes in the atmosphere in the furnace during the heating process especially the large changes in oxygen content, which makes the appearance and color of the product easy to change.
  • thermoformed part with excellent paint film adhesion.
  • the thermoformed part has better paintability, good paint film adhesion and better corrosion resistance, and is very suitable for use.
  • auto parts such as: front and rear doors, left and right anti-collision bars/beams, front and rear bumpers, A-pillar reinforcement plates, B-pillar reinforcement plates, floor mid-channels, etc.
  • thermoformed part with excellent paint film adhesion which includes a substrate layer and an aluminum-plated layer plated on at least one surface of the substrate layer.
  • the average surface of the thermoformed part The roughness Ra is 1.0 ⁇ 3.0 ⁇ m, the peak height and the height of the valley Rt are 8 ⁇ 30 ⁇ m, and the roughness peak count Rpc ⁇ 50.
  • the aluminized layer includes an aluminum phase and an aluminum-silicon phase.
  • the aluminum in the aluminized layer diffuses to the substrate layer, and at the same time the iron in the substrate layer diffuses to form Al 8 Fe 2 Si phase, the formation of a new phase leads to a significant increase in surface roughness.
  • Fe 2 Al 5 phase is formed, and the surface roughness is basically maintained.
  • all FeAl alloys are formed in the aluminum coating, and the surface is rough. Instead, the degree has dropped slightly.
  • the surface of the hot formed part after heat treatment is mainly composed of Fe 2 Al 5 and FeAl alloy.
  • the silicon oxide, aluminum oxide and iron oxide produced by the surface oxidation cannot chemically react with the phosphating solution, that is, it cannot be formed.
  • Normal phosphate film therefore, the paint film adhesion of thermoformed parts is completely guaranteed by the uneven structure of the surface, that is, the roughness of the thermoformed part has an important influence on the paint film adhesion.
  • the aluminized layer includes: a diffusion layer adjacent to the substrate layer and an alloy layer on the surface of the aluminized layer, wherein the thickness of the diffusion layer is equal to The ratio of the total thickness of the aluminized layer is 0.08-0.5.
  • the thickness of the diffusion layer is ⁇ 16 ⁇ m; the total thickness of the aluminized layer is ⁇ 60 ⁇ m.
  • the thickness of the diffusion layer is 5-16 ⁇ m; the total thickness of the aluminized layer is 20-60 ⁇ m.
  • the average roughness Ra of the surface of the thermoformed part is 1.5-2.5 ⁇ m.
  • the peak height and the height Rt of the peak and valley on the surface of the thermoformed part are 10-25 ⁇ m.
  • the surface roughness peak count Rpc of the thermoformed part is 50-250, such as 80-180.
  • the surface of the thermoformed part with excellent paint film adhesion according to the present invention contains Fe 2 Al 5 and FeAl alloy. Furthermore, the surface of the thermoformed part with excellent paint film adhesion according to the present invention also contains silicon oxide, aluminum oxide and iron oxide. Furthermore, the surface of the thermoformed part with excellent paint film adhesion of the present invention is mainly composed of Fe 2 Al 5 and FeAl alloy, and also contains silicon oxide, aluminum oxide and iron oxide. Moreover, the Fe 2 Al 5 content on the surface of the thermoformed part with excellent paint film adhesion according to the present invention is higher than 40 wt %.
  • the weight percentage of the chemical composition of the aluminum-plated layer is: Si: 4-14%, Fe: 0-4%, Mg: 0-10 %, Zn: 0-20%, the balance is Al and other unavoidable impurities. Further, in the thermoformed part with excellent paint film adhesion of the present invention, the weight percentage of the chemical composition of the aluminum-plated layer is: Si: 4-14%, Fe: 2-4%, Mg: 0-10 %, Zn: 0-20%, the balance is Al and other unavoidable impurities.
  • the weight average value of the aluminized layer is 20-120 g/m 2 per single side.
  • the weight average value of the aluminized layer is 30-100 g/m 2 per single side.
  • the mass percentage of the chemical composition of the substrate layer is:
  • the mass percentage of each chemical element in the substrate layer also satisfies at least one of the following items:
  • the mass percentage of each chemical element of the substrate layer also satisfies at least one of the following items:
  • the Al content is 0.03-0.09%, and the Ti content is 0.01-0.2%, preferably 0.01-0.1%.
  • the Cr content is 0.1-0.8%.
  • the content of Nb when it is contained, the content of Nb is 0.001-0.1%; when it is contained, the content of V is 0.001-0.01%.
  • the mass percentage of the chemical composition of the base material layer is: C: 0.02-0.8%, Si: 0.05-0.5%, Mn: 0.1-3 %, P ⁇ 0.1%, S ⁇ 0.05%, Al: 0.04-0.09%, Ti: 0.02-0.2%, B: 0.0005-0.09%, Cr: 0.15-0.8%, Nb: 0% or 0.001-0.1%, V is 0% or 0.002-0.008%, and the balance is Fe and other unavoidable impurities.
  • the yield strength is 400-1400 MPa
  • the tensile strength is 500-2100 MPa
  • the elongation is ⁇ 4%.
  • the volume percentage of martensite in the microstructure of the substrate of the thermoformed part with excellent paint film adhesion according to the present invention is ⁇ 70%, preferably 85 ⁇ %, more preferably ⁇ 95%.
  • another object of the present invention is to provide the above-mentioned method for manufacturing a thermoformed part with excellent paint film adhesion, by which a thermoformed part with excellent paint film adhesion can be obtained.
  • the present invention proposes the above-mentioned method for manufacturing a thermoformed part with excellent paint film adhesion, which includes the steps:
  • Transfer and hot stamping The hot blank is quickly transferred to the mold for cooling stamping forming to form the hot formed part.
  • step (4) the temperature of the heating furnace is too low or the residence time of the billet in the heating furnace is too short, which will lead to insufficient diffusion of iron and aluminum, resulting in excessive surface roughness. Low, affecting the roughness of the final thermoformed part.
  • the temperature of the heating furnace is too high or the residence time of the billet in the heating furnace is too long, it will cause excessive diffusion of iron and aluminum and complete formation of FeAl alloy, which will also reduce the roughness of the final hot formed part, and the diffusion process
  • the holes formed by the migration of middle elements will affect the surface conductivity, and the electrophoresis process will cause shrinkage holes, which will affect the paintability.
  • the mass percentage of the chemical composition of the aluminum plating solution is: Si: 5 to 11%, Fe: 2 to 4%, Zn: 0 to 15%, Mg: 0-8%, the balance is Al and other unavoidable impurities.
  • the mass percentage of the chemical composition of the aluminum plating solution is: Si: 8 to 11%, Fe: 2 to 4%, Zn: 0 to 11%, Mg: 0-8%, the balance is Al and other unavoidable impurities.
  • the mass percentage of the chemical composition of the aluminum plating solution is: Si: 5-11%, Fe: 2-4%, and the balance is Al And other unavoidable impurities.
  • the mass percentage of the chemical composition of the aluminum plating solution is: Si: 5-11%, Fe: 2-4%, optionally Zn : 2-15%, optional Mg: 0.5-8%, the balance is Al and other unavoidable impurities.
  • the heating rate does not exceed 10°C/s in the range of 400-600°C to make the coating Pre-alloying of zinc and aluminum to avoid coating damage or cracks.
  • step (5) the blank is transferred to the mold within 20 seconds.
  • the pressure-holding quenching is continued for 4-20 seconds, and the pressure-holding pressure applied to the surface of the blank is ⁇ 8MPa.
  • the holding pressure is 10-20 MPa.
  • step (5) the material of the mold satisfies: the thermal diffusion coefficient at 700° C. is greater than 3.8 mm 2 /s.
  • the clamping speed of the mold during stamping is 30-150mm/s, so that the thermoformed part can ensure good forming performance and reduce stamping defects such as The occurrence of cracking and necking.
  • step (5) the blank is cooled to 50-200°C at a cooling rate of 30-150°C/s, so that the internal structure of the thermoformed part is transformed into The required organizational structure, while ensuring that the thermoformed parts still maintain a good size and shape during the cooling process.
  • the present invention also includes thermoformed parts manufactured by the above-mentioned method.
  • thermoformed part with excellent paint film adhesion and its method according to the present invention have the following advantages and beneficial effects:
  • thermoformed parts with excellent paint film adhesion of the present invention have better paintability, good paint film adhesion and better corrosion resistance, and are very suitable for automotive parts, such as: front and rear doors Left and right anti-collision bars/beams, front and rear bumpers, A-pillar reinforcement plate, B-pillar reinforcement plate, floor middle channel, etc.
  • the manufacturing method of the present invention also has the above-mentioned advantages and beneficial effects.
  • thermoformed component with excellent paint film adhesion and its manufacturing method according to the present invention in conjunction with specific examples, but the explanation and description do not improperly limit the technical solution of the present invention.
  • thermoformed parts with excellent paint film adhesion of Examples 1-10 and Comparative Example 1 were prepared by the following steps:
  • the substrate is immersed in an aluminum plating solution to obtain a plate with an aluminum plating layer on the surface.
  • Transfer and hot stamping The hot blank is quickly (for example, within 20s) transferred to the mold for cooling stamping forming to form a hot formed part.
  • the hot stamping process after the mold is closed, the pressure is maintained and quenched for 4-20s.
  • the pressure on the surface of the blank is ⁇ 8MPa, and the material of the mold meets: the thermal diffusion coefficient at 700°C is greater than 3.8mm 2 /s ,
  • the clamping speed of the mold during pressing is 30-150mm/s, and the blank is cooled to 50-200°C at a cooling rate of 30-150°C/s.
  • the 1.2mm aluminum alloy coated steel plate is leveled by a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution
  • the percentage content is Si: 8.5%, Fe: 2.6%, Zn: 15%, Mg: 4%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace, the heating furnace temperature is 950°C, the residence time is 3.5min, 400 ⁇ In the range of 600°C, the heating rate is 2°C/s, the transfer time is 4s, the holding time is 5s, the holding pressure is 10MPa, the clamping speed is 50mm/s, the cooling speed is 50°C/s, cooling to 200°C, the mold is at 700
  • the thermal diffusivity at °C is 4mm 2 /s.
  • the billet enters the heating furnace, the heating furnace temperature is 940°C, the residence time is 5min, 400 ⁇ 600 In the range of °C, the heating rate is 5°C/s, the transfer time is 6s, the holding time is 15s, the holding pressure is 20MPa, the mold clamping speed is 150mm/s, the cooling speed is 150°C/s, cooling to 50°C, the mold is at 700°C
  • the thermal diffusion coefficient at that time is 5mm 2 /s.
  • the 1.0mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution
  • the percentage content is Si: 9.0%, Fe: 2.7%, and the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace.
  • the heating rate of 400-600°C is 5°C/s
  • the heating furnace temperature is 930°C
  • the residence time is 7min. It is transferred to the mold within 8s, and the thermal diffusivity of the mold at about 700°C is 7mm 2 /s.
  • the clamping speed is 70mm/s
  • the holding time is 6s
  • the holding pressure is 12MPa
  • the cooling speed is 100°C/s
  • it is cooled to 100°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 96%.
  • the 2.8mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the surface roughness of the plate before heat treatment and hot stamping as shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution The percentage content is Si: 8.8%, Fe: 2.7%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace, the heating furnace temperature is 920°C, the residence time is 7min, and the heating rate of 400-600°C is 10°C/s.
  • thermoformed part base material Transfer to the mold within 8s, clamping speed 70mm/s, holding time 6s, holding pressure 15MPa, cooling speed 60°C/s, cooling to 60°C, the thermal diffusion coefficient of the mould at 700°C is 6mm 2 /s.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 98%.
  • the 1.1mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution
  • the percentage content is Si: 10%, Fe: 3.5%, Zn: 2%, Mg: 1%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace, the heating furnace temperature is 935°C, the residence time is 4.5min, 400 ⁇
  • the heating rate is 4°C/s in the range of 600°C, and it is transferred to the mold within 7s.
  • the upper and lower mold clamping speed is 80mm/s
  • the holding time is 5s
  • the holding pressure is 15MPa
  • the thermal diffusion coefficient of the mold at 700°C is 4mm 2 /s, cooling to 100°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • the 1.5mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution
  • the percentage content is Si: 10%, Fe: 3.5%, Mg: 0.5%
  • the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace, the temperature of the heating furnace is 935°C, the residence time is 5min, and the heating is in the range of 400 ⁇ 600°C
  • the rate is 6°C/s, and it is transferred to the mold within 7s.
  • the upper and lower mold clamping speed is 80mm/s, the holding time is 5s, and the holding pressure is 15MPa.
  • the thermal diffusion coefficient of the mold at 700°C is 4mm 2 /s, and it is cooled to 120 °C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than
  • the 1.8mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution The percentage content is Si: 10%, Fe: 3.5%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace, the heating furnace temperature is 945°C, the residence time is 2.5min, and the heating rate is 7°C in the range of 400 ⁇ 600°C /s, transfer to the mold within 7s, the upper and lower mold clamping speed is 80mm/s, the holding time is 5s, the holding pressure is 15MPa, the thermal diffusion coefficient of the mold at 700°C is 6.8mm 2 /s, and it is cooled to 140°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • the 2.0mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution
  • the percentage content is Si: 10%, Fe: 3.5%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace.
  • the heating furnace temperature is 940°C
  • the residence time is 3min
  • the heating rate is 3°C/ in the range of 400 ⁇ 600°C.
  • the oxygen content of the atmosphere in the furnace is 22%, and it is transmitted to the mold within 7s, the upper and lower mold clamping speed is 80mm/s, the holding time is 5s, the holding pressure is 15MPa, and the thermal diffusion coefficient of the mold at 700°C is 7mm 2 /s , Cool to 110°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • the 2.4mm aluminum alloy coated steel plate is leveled by a leveling roller, and the surface roughness of the plate before heat treatment and hot stamping is obtained as shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution The percentage content is Si: 10%, Fe: 3.5%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace.
  • the temperature of the heating furnace is 935°C
  • the residence time is 5min
  • the heating rate is 8°C/ in the range of 400 ⁇ 600°C.
  • the oxygen content of the atmosphere in the furnace is 22%, and it is transmitted to the mold within 7s, the upper and lower mold clamping speed is 80mm/s, the holding time is 5s, the holding pressure is 15MPa, and the thermal diffusion coefficient of the mold at 700°C is 4mm 2 /s , Cool to 100°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • the 2.8mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the surface roughness of the plate before heat treatment and hot stamping as shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution The percentage content is Si: 10%, Fe: 3.5%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace.
  • the temperature of the heating furnace is 950°C
  • the residence time is 2.5min
  • the heating rate is 4°C in the range of 400 ⁇ 600°C.
  • the oxygen content of the atmosphere in the furnace is 20%, and it is transmitted to the mold within 15s, the upper and lower mold clamping speed is 80mm/s, the holding time is 5s, the holding pressure is 15MPa, and the thermal diffusion coefficient of the mold at 700°C is 5mm 2 / s, cool to 80°C.
  • the ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • the 1.5mm aluminum alloy coated steel plate is leveled with a leveling roller to obtain the plate before heat treatment and hot stamping with the surface roughness shown in Table 2.
  • the laser blanks into a blank of a certain size and shape, and the chemical composition quality of the aluminum plating solution The percentage content is Si: 10%, Fe: 3.5%, the rest is aluminum and unavoidable impurities.
  • the billet enters the heating furnace.
  • the heating furnace temperature is 935°C
  • the residence time is 5min
  • the heating rate is 6°C/ in the range of 400 ⁇ 600°C.
  • thermoformed part base material The ratio of martensite in the microstructure of the resulting thermoformed part base material is higher than 95%.
  • Table 1 lists the mass percentage ratios of the chemical elements in the base material layer of the thermoformed parts with excellent paint film adhesion of Examples 1-10 and the base material layer of Comparative Example 1.
  • the evaluation method of paintability refers to the GMW16170 standard.
  • the corrosion resistance test method refers to GMW14872.
  • the finished surface roughness Ra of the comparative thermoformed part after hot stamping in Comparative Example 1 is less than 1.8 ⁇ m, Rt is less than 12 ⁇ m, Rpc is less than 90, and the heat of Comparative Example 1
  • the paintability of the formed part is poor, the paint film adhesion does not meet the requirements, and its performance is far inferior to the thermoformed parts of the various embodiments of this case.
  • the higher the surface roughness of the material before heat treatment and hot stamping used in the hot forming part the higher the roughness of the product after heat treatment and hot stamping, and the better the adhesion to the paint film.
  • thermoformed parts with excellent paint film adhesion of the present invention have better paintability, good paint film adhesion and better corrosion resistance, and are very suitable for use in automobiles.
  • Components such as: front and rear doors, left and right anti-collision bars/beams, front and rear bumpers, A-pillar reinforcement plates, B-pillar reinforcement plates, and floor channels, etc.
  • the manufacturing method of the present invention also has the above-mentioned advantages and beneficial effects.

Abstract

一种具有优异漆膜附着力的热成形部件，其包括基材层以及镀覆在基材层的至少一个表面上的镀铝层；热成形部件表面的平均粗糙度Ra为1.0～3.0μm，峰高与峰谷的高度Rt为8～30μm，粗糙度峰计数Rpc≥50。此外,该具有优异漆膜附着力的热成形部件的制造方法包括步骤：(1)将基材浸入铝镀液，得到表面具有镀铝层的板材；(2)平整；(3)落料：将板材冲裁或切割成部件所需形状的坯料；(4)热处理；(5)传输和热冲压：将热的坯料快速传输到模具中进行冷却冲压成形，以形成热成形部件。

Description

具有优异漆膜附着力的热成形部件及其制造方法 技术领域
本发明涉及一种材料及其制造方法，尤其涉及一种热成形材料及其制造方法。
背景技术
近年来，热成形部件在汽车工业中的应用变得很重要，特别是在汽车的安全结构件方面，在一些高强度，形状复杂的零件上具有不可替代的优势。用于热成形部件的材料分为带涂覆层和不带涂覆层的，涂覆层的主要目的是钢板在热冲压成形过程中，防止钢板表面氧化。成形后的部件可以直接进行涂装及焊接使用，目前不带涂覆层的材料在热成形后必须进行表面喷丸处理以去掉表面产生的氧化物层，否则影响后续的零件涂装及焊接。热镀铝涂覆层的材料在热成形后表面无法进行正常磷化，电泳后的漆膜附着力完全依靠涂层表面形貌来保证。现有材料在使用过程中会存在漆膜附着力无法满足使用的问题。
例如：公开号为CN104651590A，公开日为2015年5月27日，名称为“冲压产品的制造方法及由其制造的冲压产品”的中国专利文献公开了一种铝或铝合金涂覆的热成形材料及制造方法，该方法针对性控制了涂覆层的厚度及五层结构，从而保证热成形件的焊接性能。
又例如：公开号为CN108588612A，公开日为2018年9月28日，名称为“热冲压成形构件、热冲压成形用预涂镀钢板及热冲压成形工艺”的中国专利文献公开了一种热冲压成形构件。在该专利文献所公开的技术方案中，降低了涂层厚度的同时，也降低了涂层的保护作用，由此，热成形工艺的波动对构件的表面性能很容易造成影响，从而影响后续的使用性能。
再例如：公开号为CN101583486，公开日为2009年11月18日，名称为“涂覆的钢带材、其制备方法、其使用方法、由其制备的冲压坯料、由其制备的冲压产品和含有这样的冲压产品的制品”的中国专利文献公开了一种涂覆钢带材的热冲压产品及方法。在该专利文献所公开的技术方案中，其包括加热、转移及冷却，而未涉 及热冲压过程，由此会造成冲压产品质量不稳定，如紧缩、开裂等，对加热过程中炉膛气氛不控制，导致加热过程中炉内气氛发生变化，尤其是氧气含量发生较大变化，带来产品外观颜色很容易发生变化，实际生产发现相同来料在同一工艺下，所得冲压产品外观颜色呈现较大不同。
发明内容
本发明的目的之一在于提供一种具有优异漆膜附着力的热成形部件，该热成形部件具有较好的涂装性、好的漆膜附着力以及较好的耐蚀性，非常适合用于汽车零部件，例如：前、后门左右防撞杆/梁、前、后保险杠、A柱加强板、B柱加强板、地板中通道等。
为了实现上述目的，本发明提出了一种具有优异漆膜附着力的热成形部件，其包括基材层以及镀覆在基材层的至少一个表面上的镀铝层，热成形部件表面的平均粗糙度Ra为1.0～3.0μm，峰高与峰谷的高度Rt为8～30μm，粗糙度峰计数Rpc≥50。
在本发明所述的技术方案中，镀铝层包括铝相和铝硅相，在加热过程中，镀铝层中的铝向基材层扩散，同时基材层的铁向镀铝层扩散形成Al 8Fe 2Si相，新相形成导致表面粗糙度显著增加，随着铁铝进一步扩散，进而形成Fe 2Al 5相，表面粗糙度基本维持，最终镀铝层中全部形成FeAl合金，表面粗糙度反而略有下降。
热处理后的热成形部件表面主要由Fe 2Al 5和FeAl合金组成，同时由于表面氧化产生的硅的氧化物、铝的氧化物以及铁的氧化物不能与磷化液发生化学反应，即不能形成正常的磷化膜，因此，热成形部件的漆膜附着力完全靠表面的凹凸不平结构来保证，即热成形部件的粗糙度对漆膜附着力有着重要影响。
镀铝层表面粗糙度越大，粗糙度峰计数Rpc值越大，铁铝扩散路径不同，新相形成的快慢不同，从而导致热处理后的成形件表面粗糙度越大，对漆膜附着力越好。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，镀铝层包括：与基材层邻接的扩散层和位于镀铝层表面的合金层，其中扩散层的厚度与镀铝层总厚度的比值为0.08-0.5。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，扩散层的厚度≤16μm；镀铝层总厚度≤60μm。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，扩散层的厚度为5～16μm；镀铝层总厚度20～60μm。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，热成形部件表面的平均粗糙度Ra为1.5～2.5μm。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，热成形部件表面的峰高与峰谷的高度Rt为10～25μm。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，热成形部件表面的粗糙度峰计数Rpc为50～250，如80～180。
进一步地，本发明所述的具有优异漆膜附着力的热成形部件的表面含有Fe 2Al 5和FeAl合金。进一步地，本发明所述的具有优异漆膜附着力的热成形部件的表面还含有硅的氧化物、铝的氧化物和铁的氧化物。进一步地，本发明所述的具有优异漆膜附着力的热成形部件的表面主要由Fe 2Al 5和FeAl合金组成，同时还含有硅的氧化物、铝的氧化物和铁的氧化物。而且，本发明所述的具有优异漆膜附着力的热成形部件的表面中Fe 2Al 5的含量高于40wt％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，镀铝层的化学成分重量百分比为：Si：4～14％，Fe：0～4％，Mg：0～10％，Zn：0～20％，余量为Al及其他不可避免的杂质。进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，镀铝层的化学成分重量百分比为：Si：4～14％，Fe：2～4％，Mg：0～10％，Zn：0～20％，余量为Al及其他不可避免的杂质。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，镀铝层的重量平均值为20～120g/m 2每单面。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，镀铝层的重量平均值为30～100g/m 2每单面。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，基材层的化学成分质量百分比为：
C：0.01～0.8％，Si：0.05～1.0％，Mn：0.1～5％，P≤0.3％，S≤0.1％，Al≤0.3％，Ti≤0.5％，B：0.0005～0.1％，Cr：0.01～3％，Nb≤0.5％，V≤0.5％，余量为Fe及其他不可避免的杂质。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，基材层的各 化学元素质量百分比还满足下列各项的至少其中之一：
C：0.05～0.6％，
Si：0.07～0.8％，
Mn：0.3～4％，
P≤0.2％，
S≤0.08％，
Al≤0.2％，
Ti≤0.4％，
B：0.0005～0.08％，
Cr：0.01～2％，
Nb≤0.3％，
V≤0.3％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，基材层的各化学元素质量百分比还满足下列各项的至少其中之一：
C：0.15～0.5％，
Si：0.1～0.5％，
Mn：0.5～3％，
P≤0.1％，
S≤0.05％，
Al≤0.1％，
Ti≤0.2％，
Cr：0.01～1％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件的基材层中，Al含量为0.03-0.09％，Ti含量为0.01-0.2％、优选0.01-0.1％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件的基材层中，Cr含量为0.1-0.8％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件的基材层中，含有时，Nb的含量为0.001-0.1％；含有时，V的含量为0.001-0.01％。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，基材层的化 学成分质量百分比为：C：0.02～0.8％，Si：0.05～0.5％，Mn：0.1～3％，P≤0.1％，S≤0.05％，Al：0.04-0.09％，Ti：0.02-0.2％，B：0.0005～0.09％，Cr：0.15～0.8％，Nb为0％或0.001-0.1％，V为0％或0.002-0.008％，余量为Fe及其他不可避免的杂质。
进一步地，在本发明所述的具有优异漆膜附着力的热成形部件中，其屈服强度为400～1400MPa，抗拉强度为500～2100MPa，延伸率≥4％。
优选地，在本发明所述的具有优异漆膜附着力的热成形部件的基材的微观组织中马氏体的体积百分比≥70％，优选85≥％，更优选≥95％。
相应地，本发明的另一目的在于提供上述的具有优异漆膜附着力的热成形部件的制造方法，通过该制造方法可以获得漆膜附着力优异的热成形部件。
为了实现上述目的，本发明提出了上述的具有优异漆膜附着力的热成形部件的制造方法，其包括步骤：
(1)将基材浸入铝镀液，得到表面具有镀铝层的板材；
(2)平整：采用粗糙度Ra为0.5～3.0μm的平整辊对板材进行平整，控制平整率≤2.0％，以使所述板材表面热辐射系数为0.1～0.8，板材表面粗糙度Ra为0.3～2.0μm，板材表面粗糙度峰计数Rpc为30～150；
(3)落料：将板材冲裁或切割成部件所需形状的坯料；
(4)热处理：将坯料放入加热炉中加热并保温，加热炉温度为880～960℃，加热炉内的气氛采用空气或氮气，坯料在加热炉中的停留时间为2.5～10min；
(5)传输和热冲压：将热的坯料快速传输到模具中进行冷却冲压成形，以形成所述热成形部件。
在本发明所述的制造方法中，在步骤(4)中，加热炉温度太低或是坯料在加热炉中的停留时间过短，均会导致铁铝扩散不够充分，进而使得表面粗糙度太低，影响最终热成形部件的粗糙度。而当加热炉温度过高或是坯料在加热炉中的停留时间过长，则会导致铁铝扩散过度，完全形成FeAl合金，这也会导致最终的热成形部件的粗糙度降低，同时扩散过程中元素迁移形成的孔洞会影响表面导电性，电泳过程中会导致缩孔，进而影响涂装性。
进一步地，在本发明所述的制造方法中，在步骤(1)中，铝镀液的化学成分质量百分含量为：Si：5～11％，Fe：2～4％，Zn：0～15％，Mg：0～8％，余量为Al及其他不可避免的杂质。
进一步地，在本发明所述的制造方法中，在步骤(1)中，铝镀液的化学成分质量百分含量为：Si：8～11％，Fe：2～4％，Zn：0～11％，Mg：0～8％，余量为Al及其他不可避免的杂质。
进一步地，在本发明所述的制造方法中，在步骤(1)中，铝镀液的化学成分质量百分含量为：Si：5～11％，Fe：2～4％，余量为Al及其他不可避免的杂质。
进一步地，在本发明所述的制造方法中，在步骤(1)中，铝镀液的化学成分质量百分含量为：Si：5～11％，Fe：2～4％，任选的Zn：2～15％，任选的Mg：0.5～8％，余量为Al及其他不可避免的杂质。
进一步地，在本发明所述的制造方法中，在步骤(4)中，在坯料加热的升温过程中，在升温至400～600℃的范围内加热速率不超过10℃/s，以使镀层中锌及铝的预合金化，避免镀层破坏或出现裂纹。
进一步地，在本发明所述的制造方法中，在步骤(5)中，坯料在20s以内被传输到模具中。
进一步地，在本发明所述的制造方法，在步骤(5)的热冲压过程中，模具合模后持续保压淬火4～20s，对坯料表面施加的保压压强≥8MPa。在一些实施方案中，保压压强为10～20MPa。
进一步地，在本发明所述的制造方法中，在步骤(5)中，模具的材质满足：在700℃时的热扩散系数大于3.8mm 2/s。
进一步地，在本发明所述的制造方法中，在步骤(5)中，冲压时模具的合模速度为30～150mm/s，以使热成形部件可以保证良好的成形性能，减少冲压缺陷例如开裂、缩颈的发生。
进一步地，在本发明所述的制造方法中，在步骤(5)中，将坯料以30～150℃/s的冷却速度冷却至50～200℃，以使得热成形部件的内部组织转变为所需要的组织结构，同时保证热成形部件在冷却过程中依然保持良好的尺寸形状。
本发明也包括采用上述方法制造得到的热成形部件。
本发明所述的具有优异漆膜附着力的热成形部件及其方法相较于现有技术具有如下所述的优点以及有益效果：
本发明所述的具有优异漆膜附着力的热成形部件具有较好的涂装性、好的漆膜附着力以及较好的耐蚀性，非常适合用于汽车零部件，例如：前、后门左右防撞杆/ 梁、前、后保险杠、A柱加强板、B柱加强板、地板中通道等。
此外，本发明所述的制造方法也同样具有上述的优点以及有益效果。
具体实施方式
下面将结合具体的实施例对本发明所述的具有优异漆膜附着力的热成形部件及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-10以及对比例1
实施例1-10的具有优异漆膜附着力的热成形部件和对比例1采用以下步骤制得：
(1)将基材浸入铝镀液，得到表面具有镀铝层的板材。
(2)平整：采用粗糙度Ra为0.5～3.0μm的平整辊对板材进行平整，控制平整率≤2.0％，以使所述板材表面热辐射系数为0.1～0.8，板材表面粗糙度Ra为0.3～2.0μm，板材表面粗糙度峰计数Rpc为30～150。
(3)落料：将板材冲裁或切割成部件所需形状的坯料。
(4)热处理：将坯料放入加热炉中加热并保温，加热炉温度为880～960℃，加热炉内的气氛采用空气或氮气，坯料在加热炉中的停留时间为2.5～10min，在坯料加热的升温过程中，在升温至400～600℃的范围内加热速率不超过10℃/s。
(5)传输和热冲压：将热的坯料快速(例如在20s内)传输到模具中进行冷却冲压成形，以形成热成形部件。其中，在热冲压过程中，模具合模后持续保压淬火4～20s，对坯料表面施加的保压压强≥8MPa，模具的材质满足：在700℃时的热扩散系数大于3.8mm 2/s，冲压时模具的合模速度为30～150mm/s，将坯料以30～150℃/s的冷却速度冷却至50～200℃。
其中，各个实施例和对比例的制造方法如下所述：
实施例1
采用平整辊对1.2mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：8.5％，Fe：2.6％，Zn：15％，Mg：4％，其余为铝及不可避 免杂质，坯料进入加热炉，加热炉温度950℃，停留时间3.5min，400～600℃的范围内加热速率为2℃/s，传输时间4s，保压时间5s，保压压强10MPa，合模速度50mm/s，冷速为50℃/s，冷却至200℃，模具在700℃时的热扩散系数为4mm 2/s。
实施例2
采用平整辊对0.9mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：5％，Fe：2.4％，Zn：8％，Mg：8％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度940℃，停留时间5min，400～600℃的范围内加热速率为5℃/s，传输时间6s，保压时间15s，保压压强20MPa，合模速度150mm/s，冷速为150℃/s，冷却至50℃，模具在700℃时的热扩散系数为5mm 2/s。
实施例3
采用平整辊对1.0mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：9.0％，Fe：2.7％，其余为铝及不可避免杂质，坯料进入加热炉，400-600℃的加热速率为5℃/s，加热炉温度930℃，停留时间7min，8s内传输至模具，700℃左右模具的热扩散系数为7mm 2/s。合模速度70mm/s，保压时间6s，保压压强12MPa，冷速100℃/s，冷却至100℃。所得热成形部件基材微观组织中马氏体比例高于96％。
实施例4
采用平整辊对2.8mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：8.8％，Fe：2.7％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度920℃，停留时间7min，400-600℃的加热速率为10℃/s，8s内传输至模具，合模速度70mm/s，保压时间6s，保压压强15MPa，冷速60℃/s，冷却至60℃，模具在700℃时的热扩散系数为6mm 2/s。所得热成形部件基材微观组织中马氏体比例高于98％。
实施例5
采用平整辊对1.1mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，Zn：2％，Mg：1％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度935℃，停留时间4.5min，400～600℃的范围内加热速率为4℃/s，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为4mm 2/s，冷却至100℃。所得热成形部件基材微观组织中马氏体比例高于95％。
实施例6
采用平整辊对1.5mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，Mg：0.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度935℃，停留时间5min，400～600℃的范围内加热速率为6℃/s，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为4mm 2/s，冷却至120℃。所得热成形部件基材微观组织中马氏体比例高于95％。
实施例7
采用平整辊对1.8mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度945℃，停留时间2.5min，400～600℃的范围内加热速率为7℃/s，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为6.8mm 2/s，冷却至140℃。所得热成形部件基材微观组织中马氏体比例高于95％。
实施例8
采用平整辊对2.0mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度940℃，停留时间3min，400～600℃的范围内加热速率为3℃/s，炉内气氛氧含量为22％，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为7mm 2/s，冷却至110℃。所得热成形部件基材微观组织中马氏体比例高于95％。
实施例9
采用平整辊对2.4mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度935℃，停留时间5min，400～600℃的范围内加热速率为8℃/s，炉内气氛氧含量为22％，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为4mm 2/s，冷却至100℃。所得热成形部件基材微观组织中马氏体比例高于95％。
实施例10
采用平整辊对2.8mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成分质量百分含量为Si：10％，Fe：3.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度950℃，停留时间2.5min，400～600℃的范围内加热速率为4℃/s，炉内气氛氧含量为20％，15s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为5mm 2/s，冷却至80℃。所得热成形部件基材微观组织中马氏体比例高于95％。
对比例1
采用平整辊对1.5mm带铝合金镀层钢板进行平整，得到表面粗糙度如表2所示的热处理和热冲压前的板材，激光落料成一定尺寸和形状的坯料，铝镀液的化学成 分质量百分含量为Si：10％，Fe：3.5％，其余为铝及不可避免杂质，坯料进入加热炉，加热炉温度935℃，停留时间5min，400～600℃的范围内加热速率为6℃/s，7s内传输至模具，上下模具合模速度80mm/s，保压时间5s，保压压强15MPa，模具在700℃时的热扩散系数为4mm 2/s，冷却至120℃。所得热成形部件基材微观组织中马氏体比例高于95％。
表1列出了实施例1-10的具有优异漆膜附着力的热成形部件的基材层以及对比例1的基材层的各化学元素的质量百分配比。
表1.(wt％，余量为Fe和其他不可避免的杂质)
实施例 C Si Mn P S Al Ti B Cr Nb V
1 0.02 0.05 0.12 0.059 0.038 0.09 0.090 0.0005 0.15 - -
2 0.06 0.23 1.19 0.015 0.001 0.04 0.030 0.040 0.27 - -
3 0.49 0.50 2.51 0.024 0.04 0.08 0.027 0.0052 0.51 0.002 0.002
4 0.39 0.36 3.00 0.044 0.03 0.07 0.05 0.0062 0.71 0.003 0.005
5 0.78 0.48 0.50 0.081 0.02 0.05 0.48 0.0071 0.20 0.1 -
6 0.15 0.10 2.90 0.059 0.038 0.09 0.090 0.0031 0.15 - -
7 0.25 0.23 1.19 0.015 0.001 0.04 0.030 0.0040 0.27 - -
8 0.49 0.50 2.51 0.024 0.04 0.08 0.027 0.0052 0.51 0.005 0.008
9 0.39 0.36 3.00 0.044 0.03 0.07 0.05 0.0062 0.71 - -
10 0.50 0.9 0.50 0.081 0.02 0.05 0.20 0.09 0.20 - -
对比例1 0.25 0.23 1.19 0.015 0.001 0.04 0.030 0.0040 0.27 - -
为了验证本案的实施效果，同时证明本案较之现有技术的优异效果，本案将实施例1-10的具有优异漆膜附着力的热成形部件以及对比例1的对比热成形部件进行测试，表2列出了各个实施例以及对比例的测试结果。
表2
Figure PCTCN2020118368-appb-000001
Figure PCTCN2020118368-appb-000002
*漆膜附着力的测试方法：
参考GB/T 9286-1998百格法，用刀在表面划百格，用胶带贴在形成的格子中心，然后平稳的扯离，观察漆膜脱落的现象，并通过计算划格中格子中的状态对应标准进行评级判定。
涂装性的评价方法参考GMW16170标准。
耐蚀性的测试方法参考GMW14872。
由表2可以看出,本案各个实施例的屈服强度为400～1350MPa，抗拉强度为500～2000MPa，延伸率为4～19％。
此外，由表2还可以看出，对比例1中的对比热成形部件在热冲压后的成品表面粗糙度Ra低于1.8μm，Rt低于12μm，Rpc低于90，并且对比例1的热成形件的涂装性较差，漆膜附着力不满足要求，其性能远远不如本案的各个实施例的热成形 部件。另外，由表2可以看出，热成形部件所采用的热处理和热冲压前的材料表面粗糙度越高，热处理和热冲压后产品粗糙度也相对较高，对漆膜附着力更好。
综上所述可以看出，本发明所述的具有优异漆膜附着力的热成形部件具有较好的涂装性、好的漆膜附着力以及较好的耐蚀性，非常适合用于汽车零部件，例如：前、后门左右防撞杆/梁、前、后保险杠、A柱加强板、B柱加强板、地板中通道等。
此外，本发明所述的制造方法也同样具有上述的优点以及有益效果。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。
此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (20)

  1. 一种具有优异漆膜附着力的热成形部件，其包括基材层以及镀覆在基材层的至少一个表面上的镀铝层；其特征在于，所述热成形部件表面的平均粗糙度Ra为1.0～3.0μm，峰高与峰谷的高度Rt为8～30μm，粗糙度峰计数Rpc≥50。
  2. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，所述镀铝层包括：与基材层邻接的扩散层和位于镀铝层表面的合金层，其中扩散层的厚度与镀铝层总厚度的比值为0.08-0.5。
  3. 如权利要求1或2所述的具有优异漆膜附着力的热成形部件，其特征在于，所述扩散层的厚度≤16μm；所述镀铝层总厚度≤60μm。
  4. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，所述的镀铝层的化学成分重量百分比为：Si：4～14％，Fe：0～4％，Mg：0～10％，Zn：0～20％，余量为Al及其他不可避免的杂质；优选地，所述镀铝层的化学成分重量百分比为：Si：4～14％，Fe：2～4％，Mg：0～10％，Zn：0～20％，余量为Al及其他不可避免的杂质。
  5. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，所述镀铝层的重量平均值为20～120g/m 2每单面。
  6. 如权利要求5所述的具有优异漆膜附着力的热成形部件，其特征在于，所述镀铝层的重量平均值为30～100g/m 2每单面。
  7. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，所述基材层的化学成分质量百分比为：
    C：0.01～0.8％，Si：0.05～1.0％，Mn：0.1～5％，P≤0.3％，S≤0.1％，Al≤0.3％，Ti≤0.5％，B：0.0005～0.1％，Cr：0.01～3％，Nb≤0.5％，V≤0.5％，余量为Fe及其他不可避免的杂质。
  8. 如权利要求7所述的具有优异漆膜附着力的热成形部件，其特征在于，所述基材层的各化学元素质量百分比还满足下列各项的至少其中之一：
    C：0.05～0.6％，
    Si：0.07～0.8％，
    Mn：0.3～4％，
    P≤0.2％，
    S≤0.08％，
    Al≤0.2％，
    Ti≤0.4％，
    B：0.0005～0.08％，
    Cr：0.01～2％，
    Nb≤0.3％，
    V≤0.3％。
  9. 如权利要求7或8所述的具有优异漆膜附着力的热成形部件，其特征在于，所述基材层的各化学元素质量百分比还满足下列各项的至少其中之一：
    C：0.15～0.5％，
    Si：0.1～0.5％，
    Mn：0.5～3％，
    P≤0.1％，
    S≤0.05％，
    Al≤0.1％，
    Ti≤0.2％，
    Cr：0.01～1％。
  10. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，其屈服强度为400～1400MPa，抗拉强度为500～2100MPa，延伸率≥4％。
  11. 如权利要求1所述的具有优异漆膜附着力的热成形部件，其特征在于，所述的具有优异漆膜附着力的热成形部件的表面含有Fe 2Al 5和FeAl合金；或主要由Fe 2Al 5和FeAl合金组成，同时还含有硅的氧化物、铝的氧化物和铁的氧化物。
  12. 如权利要求9所述的具有优异漆膜附着力的热成形部件，其特征在于，所述的具有优异漆膜附着力的热成形部件的基材层的显微组织中马氏体的体积百分比≥95％。
  13. 如权利要求1-12中任意一项所述的具有优异漆膜附着力的热成形部件的制造方法，其特征在于，包括步骤：
    (1)将基材浸入铝镀液，得到表面具有镀铝层的板材；
    (2)平整：采用粗糙度Ra为0.5～3.0μm的平整辊对板材进行平整，控制平整率≤2.0％，所述板材表面热辐射系数为0.1～0.8，板材表面粗糙度Ra为0.3～2.0μm，板材表面粗糙度峰计数Rpc为30～150；
    (3)落料：将板材冲裁或切割成部件所需形状的坯料；
    (4)热处理：将坯料放入加热炉中加热并保温，加热炉温度为880～960℃，加热炉内的气氛采用空气或氮气，坯料在加热炉中的停留时间为2.5～10min；
    (5)传输和热冲压：将热的坯料快速传输到模具中进行冷却冲压成形，以形成所述热成形部件。
  14. 如权利要求13所述的制造方法，其特征在于，在所述步骤(1)中，铝镀液的化学成分质量百分含量为：Si：5～11％，Fe：2～4％，Zn：0～15％，Mg：0～8％，余量为Al及其他不可避免的杂质；优选为：Si：8～11％，Fe：2～4％，Zn：0～11％，Mg：0～8％，余量为Al及其他不可避免的杂质。
  15. 如权利要求13所述的制造方法，其特征在于，在所述步骤(4)中，在坯料加热的升温过程中，在升温至400～600℃的范围内加热速率不超过10℃/s。
  16. 如权利要求13所述的制造方法，其特征在于，在所述步骤(5)中，坯料在20s以内被传输到模具中。
  17. 如权利要求13所述的制造方法，其特征在于，在所述步骤(5)的热冲压过程中，所述模具合模后持续保压淬火4～20s，对坯料表面施加的保压压强≥8MPa。
  18. 如权利要求13所述的制造方法，其特征在于，在所述步骤(5)中，所述模具的材质满足：在700℃时的热扩散系数大于3.8m 2/s。
  19. 如权利要求13所述的制造方法，其特征在于，在所述步骤(5)中，冲压时模具的合模速度为30～150mm/s。
  20. 如权利要求13所述的制造方法，其特征在于，在所述步骤(5)中，将坯料以30～150℃/s的冷却速度冷却至50～200℃。
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