EP3889314A1 - Mit einer al-fe-legierung plattiertes stahlblech für die warmverformung mit ausgezeichneter korrosionsbeständigkeit und hitzebeständigkeit, formteil aus einer heisspressung und verfahren zu seiner herstellung - Google Patents

Mit einer al-fe-legierung plattiertes stahlblech für die warmverformung mit ausgezeichneter korrosionsbeständigkeit und hitzebeständigkeit, formteil aus einer heisspressung und verfahren zu seiner herstellung Download PDF

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Publication number
EP3889314A1
EP3889314A1 EP19891044.0A EP19891044A EP3889314A1 EP 3889314 A1 EP3889314 A1 EP 3889314A1 EP 19891044 A EP19891044 A EP 19891044A EP 3889314 A1 EP3889314 A1 EP 3889314A1
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European Patent Office
Prior art keywords
steel sheet
alloy
layer
plated
weight
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP19891044.0A
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English (en)
French (fr)
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EP3889314A4 (de
Inventor
Seong-Woo Kim
Jin-Keun Oh
Sang-Heon Kim
Yeol-Rae Cho
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Posco Holdings Inc
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Posco Co Ltd
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Priority claimed from PCT/KR2019/016761 external-priority patent/WO2020111879A1/ko
Publication of EP3889314A1 publication Critical patent/EP3889314A1/de
Publication of EP3889314A4 publication Critical patent/EP3889314A4/de
Pending legal-status Critical Current

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    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/021—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal alloy layer
    • 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
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each 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
    • C22C38/06—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
    • C22C38/14—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
    • C22C38/18—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
    • C23C2/04—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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/027—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal matrix material comprising a mixture of at least two metals or metal phases or metal matrix composites, e.g. metal matrix with embedded inorganic hard particles, CERMET, MMC.
    • 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
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/028—Including graded layers in composition or in physical properties, e.g. density, porosity, grain size
    • 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

Definitions

  • the present disclosure relates to a steel sheet plated with an Al-Fe alloy for hot forming having excellent corrosion resistance and heat resistance, a hot press formed part, and a manufacturing method therefor.
  • reducing a thickness of a steel sheet used in automobiles may be a method for improving fuel efficiency of automobiles.
  • the reducing a thickness of a steel sheet may cause problems in automobile safety, and thus, in this case, improvements of strength of the steel sheet should be facilitated.
  • the hot forming method is a method forming a low temperature structure, such as martensite or the like, in a steel sheet by forming at a high temperature suitable for forming and then quenching the steel sheet at a low temperature to increase strength of a final product.
  • a low temperature structure such as martensite or the like
  • patent document 1 In the case of the aforementioned hot forming method, since the steel sheet has to be heated to a high temperature, a surface of the steel sheet is oxidized, which additionally requires a process of removing oxides on the surface of the steel sheet after press forming. In order to solve this problem, patent document 1 was proposed. In patent document 1, a steel sheet subjected to aluminum-plating is used in a process of hot forming or heating and quenching after room temperature forming (briefly, post-heat treatment). Since an aluminum-plating layer is present on the surface of the steel sheet, the steel sheet is not oxidized at the time of heating.
  • Patent document 1 U.S. Patent Publication No. 6,296,805
  • An aspect of the present disclosure is to provide a steel sheet plated with an Al-Fe alloy, capable of forming a hot press formed part having excellent corrosion resistance and heat resistance, a hot press formed part obtained using the same, and a method of manufacturing the same.
  • a steel sheet plated with an Al-Fe alloy includes a base steel sheet; and an alloy plating layer formed on the base steel sheet, wherein the alloy plating layer comprises an alloyed layer (I) formed on the base steel sheet and including Al: 5 to 30% by weight; an alloyed layer (II) formed on the alloyed layer (I) and including Al: 30 to 60% by weight; and an alloyed layer (III) formed on the alloyed layer (II) and including Al: 20 to 50% by weight, wherein FeAl(Si) alloy phases including Al: 20 to 50% and Si: 5 to 20%, by weight, are dispersed and distributed in the alloyed layer (II), and a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less is 10 3 pieces/mm 2 or more.
  • the alloy plating layer may further include an alloyed layer (IV) formed on the alloyed layer (III) and including Al: 30 to 60% by weight.
  • the base steel sheet may include, by weight, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al: 0.001 to 1%, N: 0.001 to 0.02%, a balance of Fe, and other impurities.
  • the base steel sheet may further include, by weight, at least one of B: 0.001 to 0.01%, Cr: 0.01 to 1%, or Ti: 0.001 to 0.2%.
  • a hot press formed part obtained by hot press forming the above-mentioned steel sheet wherein FeAl(Si) alloy phases including Al: 20 to 50% and Si: 5 to 20%, by weight, are dispersed and distributed in the alloyed layer (II), and a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less is 10 4 pieces/mm 2 or more.
  • the base steel sheet may include, by weight, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al: 0.001 to 1%, N: 0.001 to 0.02%, a balance of Fe, and other impurities.
  • the base steel sheet may further include, by weight, at least one of B: 0.001 to 0.01%, Cr: 0.01 to 1%, or Ti: 0.001 to 0.2%.
  • a method of manufacturing a hot press formed part includes heat-treating the steel sheet according to any one of claims 5 to 8 within a temperature range of Ac3 to 950°C for 1 to 15 minutes; and hot press forming the heat-treated steel sheet.
  • a steel sheet plated with an Al-Fe alloy including alloyed layers (I) to (III) or alloyed layers (I) to (IV) on a base steel sheet, and in which a plating layer, not melted even when heated for hot forming, is formed, may have an effect of excellent heat resistance.
  • a steel sheet plated with an Al-Fe alloy in which a fine FeAl(Si) alloy phase is dispersed and distributed in the alloyed layer (II), may effectively suppress formation of cracks occurring in the alloyed layer (II), a hard layer, to have an effect of obtaining excellent corrosion resistance.
  • a steel sheet plated with an Al-Fe alloy may include a base steel sheet; and an alloy plating layer formed on the base steel sheet, wherein the alloy plating layer comprises an alloyed layer (I) formed on the base steel sheet and including Al: 5 to 30% by weight; an alloyed layer (II) formed on the alloyed layer (I) and including Al: 30 to 60% by weight; and an alloyed layer (III) formed on the alloyed layer (II) and including Al: 20 to 50% by weight.
  • an alloyed layer (IV) having the same alloy composition as that of the alloyed layer (II) may be further included on the alloyed layer (III).
  • the alloyed layer (I) may include Al: 5 to 30% by weight
  • the alloyed layer (II) may include Al: 40 to 60% by weight
  • the alloyed layer (III) may include Al: 20 to 40% by weight.
  • the alloyed layer (I) may include Al: 5 to 30% by weight
  • the alloyed layer (II) may include Al: 45 to 60% by weight
  • the alloyed layer (III) may include Al: 20 to 40% by weight.
  • Fe of the base steel sheet may be diffused into the aluminum-plating layer having a high Al content.
  • alloying between Al and Fe may be performed in the plating layer, and a layer structure consisting of the alloyed layers (I) to (III) may be formed according to a degree of alloying of Fe.
  • an alloyed layer (IV) may be formed on the alloyed layer (III) according to the conditions of the alloying heat treatment.
  • the formation of the alloyed layer (IV) may be affected by alloying behavior of Fe of the base steel sheet and Al and Si of the plating layer, and whether or not the formation is carried out may be determined, according to a temperature and a time period of a batch annealing process performed after aluminum-plating in the present disclosure.
  • the formation may be carried out mainly, and a configuration, an alloy composition range, or the like thereof may be substantially identical to those of the alloyed layer (II).
  • the alloyed layer (II) and the alloyed layer (IV) may be phases with little Si solubility, and it is thought that Si present in the plating layer during alloying may move to the alloyed layer (III), an AlFe(Si) phase, and the alloyed layer (II) and the alloyed layer (IV) without Si solubility may be formed around the alloyed layer (III).
  • the batch annealing time period is sufficient, it is thought that the alloyed layer (III) is relatively grown in a surface direction due to a continuous alloying reaction, and the alloyed layer (IV) does not exist.
  • a fine FeAl(Si) alloy phase including Al: 20 to 50% and Si: 5 to 20%, by weight may be dispersed and distributed in the alloyed layer (II).
  • the FeAl(Si) alloy phase may be an Al-Fe-Si compound that may be formed in a manufacturing process of a steel sheet plated with an Al-Fe alloy of the present disclosure, and a wide variety of phases may be formed depending on the heat treatment conditions and the composition ratio of each component, and a location of formation will also be different.
  • the FeAl(Si) alloy phase may have a soft property with low hardness, as compared to the alloyed layer (II).
  • an amount of Al may be 22 to 35%, and an amount of Si may be 5 to 16%.
  • a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less in the alloyed layer (II) may be 10 3 pieces/mm 2 or more.
  • a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less in the alloyed layer (II) may be 5 ⁇ 10 3 pieces/mm 2 or more, and more preferably 10 4 pieces/mm 2 or more.
  • the equivalent circle diameter of the FeAl(Si) alloy phases refers to a diameter of a circle having the same area as a particle area when observing a cross-section perpendicular to the plating layer, and the equivalent circle diameter may be easily measured by observation with a scanning electron microscope in a cross-section perpendicular to the plating layer.
  • the number and a fraction of FeAl(Si) alloy phases present in the alloyed layer (II) may increase due to an alloying reaction of the plating layer and a base iron, but a number density of FeAl(Si) alloy phases in the plated steel sheet before hot forming may play an important role in distribution and a number density of FeAl(Si) alloy phases formed during hot forming.
  • the alloyed layer (II) which may be a main component of the alloy plating layer, since hardness thereof is high, cracks may easily occur in the alloy plating layer in areas in which a shape is complex, such as a curved portion during hot forming.
  • a number density of FeAl(Si) alloy phases in the hard alloyed layer (II) may be controlled to a certain amount or more.
  • a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less is less than 10 3 pieces/mm 2 , an effect of suppressing cracking of the plating layer in the curved portion due to dispersion and distribution of the FeAl(Si) alloy phases may be insufficient, to deteriorate corrosion resistance in the curved portion. Therefore, in the present disclosure, a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less may be limited to 10 3 pieces/mm 2 or more.
  • a number density of FeAl(Si) alloy phases may be 10 8 pieces/mm 2 or less. This may be because when a number density of FeAl(Si) alloy phases exceeds 10 8 pieces/mm 2 , a fraction of a soft phase in the plating layer may increase to deteriorate scratch resistance of the plating layer.
  • an FeAl(Si) alloy phase may be included in the alloyed layer (IV).
  • the FeAl(Si) alloy phase may not be included, since a space in which the FeAl(Si) alloy phase is formed is insufficient.
  • the base steel sheet of the present disclosure may not be particularly limited when used in hot forming.
  • the base steel sheet may include, by weight, C: 0.04 to 0.5%, Si: 0.01 to 2%, Mn: 0.1 to 5%, P: 0.001 to 0.05%, S: 0.0001 to 0.02%, Al: 0.001 to 1%, N: 0.001 to 0.02%, a balance of Fe, and other impurities.
  • C 0.04 to 0.5%
  • Si 0.01 to 2%
  • Mn 0.1 to 5%
  • P 0.001 to 0.05%
  • S 0.0001 to 0.02%
  • Al 0.001 to 1%
  • N 0.001 to 0.02%
  • a balance of Fe and other impurities.
  • Carbon (C) may be added in an appropriate amount as an essential element to increase strength of a heat treatment member.
  • C may be added in an amount of 0.04% or more.
  • a lower limit of an amount of C may be 0.1% or more.
  • carbon (C) may be added in an amount of 0.5% or less.
  • an amount of C may be 0.45% or less, and more preferably, an amount of C may be limited to be 0.4% or less.
  • Si should be added as a deoxidizer in steel making and also serves to inhibit occurrence of carbide, which has the greatest effect on strength of a hot rolled press formed member.
  • Si may be added in an amount of 0.01% or more to secure residual austenite by concentrating carbon at martensite lath grain boundaries after the formation of martensite in hot forming.
  • an upper limit of an amount of Si may be set to 2%, to ensure sufficient plating properties, when performing aluminum-plating on a steel sheet after rolling.
  • an amount of Si may be limited to 1.5% or less.
  • Manganese (Mn) may be added in an amount of 0.1% or more to lower a critical cooling rate for securing martensite in the hot press formed member, as well as securing a solid solution strengthening effect.
  • an amount of Mn may be limited to 5% or less, in view of the facts that workability of a hot forming process is secured, manufacturing cost is reduced, and spot weldability is improved by appropriately maintaining strength of the steel sheet.
  • Phosphorus (P) may be present as an impurity in steel and a less amount thereof may be advantageous. Therefore, in the present disclosure, an amount of P may be limited to 0.05% or less, and preferably, may be limited to 0.03% or less. Since a smaller amount of P is advantageous, there is no need to specifically set an upper limit of an amount of P. However, excessive lowering an amount of P may lead to an increase in manufacturing cost, and in consideration of this, a lower limit of an amount of P may be set to 0.001%.
  • sulfur (S) may be an impurity in steel and may be an element that inhibits ductility, impact characteristics, and weldability of a member, and thus, a maximum amount of S may be limited to 0.02%, and preferably, to 0.01% or less. In addition, when a minimum amount thereof is less than 0.0001%, manufacturing cost may increase. Therefore, a lower limit of an amount of S may be set to 0.0001%.
  • Aluminum (Al) may increase cleanliness of steel by deoxidizing the steel together with Si, and may be added in an amount of 0.001% or more to obtain the above effect.
  • an amount of Al may be limited to 1% or less, to prevent an Ac3 temperature from becoming too high, such that heating required during hot forming may be performed within an appropriate temperature range.
  • N Nitrogen
  • N is an element included as an impurity in the steel.
  • N may be included in an amount of 0.02% or less.
  • an amount of N may be set to 0.001% or more, in consideration of an increase in manufacturing cost.
  • the steel sheet plated with an Al-Fe alloy may further include, by weight, at least one of B: 0.001 to 0.01%, Cr: 0.01 to 1%, or Ti: 0.001 to 0.2%.
  • B boron
  • B may segregate along prior-austenite grain boundaries to inhibit embrittlement of a hot press formed member due to grain boundary segregation of P and/or S. Therefore, B may be added in an amount of 0.0001% or more. When an amount of B exceeds 0.01%, the effect may be saturated and may causes brittleness during hot press rolling. Therefore, an upper limit of an amount of B may be set to 0.01%, and an amount of B may be preferably set to 0.005% or less.
  • Cr chromium
  • Cr may be an element added to improve a solid solution strengthening effect and hardenability during hot forming, and may be added in an amount of 0.01% or more, to obtain the above effect.
  • an amount of Cr may be limited to 1% or less.
  • an effect of improving hardenability, relative to an amount added may also be weak, which may be disadvantageous in terms of cost.
  • Titanium (Ti) may be not only effective in improving strength of a heat treated member due to formation of fine precipitates and improving the collision performance of the member due to grain refinement, but also effective in maximizing an effect of adding B by first reflecting Ti with N, when B is added.
  • Ti may be added in an amount of 0.001% or more. Formation of coarse TiN caused by an increase in amount of Ti may deteriorate collision performance of the member. Therefore, an amount of Ti may be limited to 0.2% or less.
  • the balance other than the aforementioned components may include iron (Fe) and inevitable impurities, and addition of a component that may be included in the steel sheet for hot press forming may not be particularly limited.
  • Typical aluminum-plated hot forming steel sheets may have insufficient heat resistance because a melting point of an aluminum-plating layer is lower than a heating temperature for hot forming. For this reason, it is disadvantageous that a plating layer may melt during heating for hot forming to contaminate a roll in a heating furnace, or rapid heating is impossible.
  • a steel sheet for hot press forming may have an aluminum-iron alloy plating layer, and a melting point of an alloy plating layer may be about 1160°C or higher, which may be higher than a heating temperature for hot forming. Therefore, excellent heat resistance may be exhibited.
  • a hot press formed part may be manufactured by heat-treating a steel sheet plated with an Al-Fe alloy, including an alloy plating layer and a base steel sheet, having the above-described alloy composition and layer structure, within a temperature range of Ac3 to 950°C for 1 to 15 minutes and hot press forming the heat-treated steel sheet.
  • another aspect of the present disclosure may be a hot press formed part obtained by hot press forming the above-described steel sheet plated with an Al-Fe alloy, and may be a hot press formed part in which FeAl(Si) alloy phases including Al: 20 to 50% and Si: 5 to 20%, by weight, are dispersed and distributed in the alloyed layer (II), and a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less is 10 4 pieces/mm 2 or more.
  • a hot press formed part manufactured by hot press forming a steel sheet plated with an Al-Fe alloy, according to the present disclosure, may have an equivalent circle diameter of 5 ⁇ m or less, and soft FeAl(Si) alloy phases may be dispersed and distributed in a number density of 10 4 pieces/mm 2 or more in a hard alloyed layer (II), to suppress formation of cracks in a plating layer in areas in which a shape is complex, such as a curved portion during hot forming. Therefore, corrosion resistance may be improved.
  • a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less is preferably 2 ⁇ 10 4 pieces/mm 2 or more, more preferably 3 ⁇ 10 4 pieces/mm 2 or more.
  • a number density of FeAl(Si) alloy phases in the hot press formed part is preferred to be high, an upper limit thereof may not be limited, and, as a non-limited example, may be 10 9 pieces/mm 2 or less.
  • an upper limit thereof may not be limited, and, as a non-limited example, may be 10 9 pieces/mm 2 or less.
  • an amount of Al may be 22 to 35%, and an amount of Si may be 5 to 16%.
  • a steel sheet plated with an Al-Fe alloy of the present disclosure may be obtained by preparing a hot-rolled or cold-rolled base steel sheet, hot-dip aluminum-plating on a surface of the base steel sheet, and then annealing the plated steel sheet for alloying.
  • a base steel sheet having the above-described alloy composition may be prepared, and the base steel sheet may be aluminum-plated and coiled under appropriate conditions to obtain an aluminum-plated steel sheet (coil).
  • a surface of a rolled steel sheet may be aluminum-plated at a plating amount of 30 to 200 g/m 2 based on one surface.
  • the aluminum-plating may be a type of AlSi plating (including 80% or more of Al and 5 to 20% of Si, and additional elements may be included, as necessary), usually called type I, but may be a type of plating (including 90% or more of Al, and additional elements may be included, as necessary), called type II, both may be used.
  • hot-dip aluminum-plating may be performed, and an annealing treatment may be performed on the steel sheet before the plating.
  • a proper amount of plating may be 30 to 200 g/m 2 based on one surface. When the amount of plating is too large, it may take an excessive amount of time to alloy to the surface. When the amount of plating is too small, it may be difficult to obtain sufficient corrosion resistance.
  • cooling may be performed at a cooling rate to 20°C/sec or less up to 250°C.
  • a cooling rate after the aluminum-plating may affects formation of a diffusion suppressing layer between a plating layer and base iron.
  • a cooling rate up to 250°C after the aluminum-plating may be 20°C/second or less.
  • coiling tension of the coil may be adjusted to 0.5 to 5 kg/mm 2 .
  • an alloying behavior and a surface quality of the coil may be changed during a subsequent annealing treatment.
  • An steel sheet plated with an Al-Fe alloy may be obtained by performing annealing treatment on the aluminum-plated steel sheet under the following conditions.
  • the aluminum-plated steel sheet (coil) may be heated in a batch annealing furnace (BAF).
  • BAF batch annealing furnace
  • a target temperature and a holding time period of the heat treatment may be within a range of 550 to 750°C for 30 minutes to 50 minutes, based on a temperature of the steel sheet (in the present disclosure, the highest temperature at which a material reaches this temperature range may be referred to as the heating temperature).
  • the target temperature of the heat treatment may be within a range of 600 to 750°C
  • the holding time period of the heat treatment may be 30 minutes to 10 hours.
  • the holding time period may be a time period until a time point of starting cooling after the coil temperature reaches the target temperature.
  • the heating temperature may be set to 550°C or higher for sufficient alloying.
  • the heating temperature may be 750°C or less.
  • the holding time period may be set to 30 minutes to 50 hours.
  • a temperature of the steel sheet may have a heating pattern in which the temperature continues to rise without a cooling process until it reaches the heating temperature, and a heating pattern in which the temperature rises after maintaining a certain time period at a temperature below the target temperature may be applied thereto.
  • an average temperature increase rate may be set to be 10 to 100°C/h, based on a temperature of the steel sheet (coil) for the entire temperature range (a range from room temperature to the heating temperature).
  • the average temperature increase rate is more preferably 10 to 50°C/h, and most preferably 10 to 30°C/h.
  • the average temperature increase rate may be entirely controlled within the above numerical range, but in one embodiment of the present disclosure, it may be heated by setting the average temperature increase rate in the range of 400 to 500°C to 1 to 15°C/h when increasing a temperature, in order to prevent from causing surface stains or the like due to remaining of portion of rolling oil mixed during rolling in a temperature section in which the rolling oil is vaporized, and to secure sufficient productivity.
  • the average temperature increase rate in the range of 400 to 500°C is more preferably 2 to 10°C/h.
  • a difference between an ambient temperature in the batch annealing furnace and a temperature of the steel sheet may be 5 to 80°C.
  • the difference between the ambient temperature in the batch annealing furnace and the temperature of the steel sheet is more preferably 5 to 50°C, and most preferably 5 to 30°C.
  • Conventional heating of the batch annealing furnace may take a method of heating a steel sheet (coil) by increasing an atmosphere temperature inside an annealing furnace, rather than a method of directly heating a steel sheet (coil).
  • a difference between the atmosphere temperature and the coil temperature may not be avoided, but in order to minimize a difference in material and plating quality by location within the steel sheet, the difference between the atmosphere temperature and the steel sheet temperature may be set to 80°C or less, based on a point in time when a target temperature of the heat treatment is reached.
  • the temperature difference should be as small as possible, but it may be difficult to meet entirely the average temperature increase rate condition by slowing the temperature increase rate. Considering this, the temperature difference may be set to 5°C or higher.
  • the temperature of the steel sheet refers to measurement of a temperature of a bottom portion of the charged steel sheet (coil) (the bottom portion means the lowest portion of the coil), and the ambient temperature refers to a temperature measured at a center of an inner space of a heating furnace.
  • a hot press formed part may be manufactured by performing hot press forming on a steel sheet plated with an Al-Fe alloy for hot forming, manufactured by the above-described manufacturing method.
  • the hot press forming may use a method conventionally used in the art, and as a non-limiting example, after heat treatment at a temperature range of Ac3 to 950°C for 1 to 15 minutes, hot press forming may be performed.
  • a cold rolled steel sheet for hot forming having the composition illustrated in Table 1 below, was prepared as a base steel sheet, and a surface of the steel sheet was plated with a type I plating bath having an Al-9%Si-2.5%Fe composition. During the plating, an amount of the plating was adjusted to 70 g/m 2 per surface, and a cooling rate to 250°C after the aluminum-plating was cooled at 12°C/sec, and coiling tension was adjusted to 2.2 kg/mm 2 .
  • the plated steel sheet in this state was taken as Comparative Example 1, and a photograph of a cross-section of the plating layer of Comparative Example 1 observed with a scanning electron microscope is shown in FIG. 3 .
  • the plated steel sheet was heated to 650°C under the following conditions in a batch annealing furnace.
  • Inventive Example 1 A structure of a plating layer, and a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less in an alloyed layer (II) were confirmed by observing a cross-section of the steel sheet with a scanning electron microscope (see FIG. 1 ), and were illustrated in Table 3.
  • a melting point of the alloyed layer (II) of Inventive Example 1 was measured, and was found to have a melting point of about 1160°C.
  • a cold rolled steel sheet for hot forming having the composition illustrated in Table 2 below, was prepared as a base steel sheet, and a surface of the steel sheet was plated with a type I plating bath having an Al-8%Si-1.5%Fe composition. During the plating, an amount of the plating was adjusted to 60 g/m 2 per surface, and a cooling rate to 250°C after the aluminum-plating was cooled at 7.5°C/sec, and coiling tension was adjusted to 3.5 kg/mm 2 . The plated steel sheet in this state was taken as Comparative Example 2. [Table 2] Element C Si Mn Al P S N Cr Ti B Ac3 Amount (%) 0.24 0.25 1.55 0.02 0.01 0.0024 0.009 0.2 0.04 0.003 821°C
  • the plated steel sheet was heated to 670°C under the following conditions in a batch annealing furnace.
  • Inventive Example 2 A structure of a plating layer, and a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less in an alloyed layer (II) were confirmed by observing a cross-section of the steel sheet with a scanning electron microscope (see FIG. 2 ), and were illustrated in Table 3.
  • alloyed layers (I), (II), and (III) were sequentially formed on the base steel sheet, as shown in FIG. 2 .
  • Comparative Examples 1 and 2 it was confirmed that an alloyed layer made of Fe and Al was formed on the base steel sheet, and an aluminum layer containing 95% or more of Al was formed on the alloyed layer, as shown in FIG. 3 .
  • the alloy-plated steel sheets of Inventive Examples 1 and 2 and the plated steel sheets of Comparative Examples 1 and 2 were heated at 900°C for 6 minutes, and then hot press formed with the mold of FIG. 6 , to obtain hot press formed parts.
  • FIG. 4 A photograph of a cross-section of a plating layer of the plated steel sheet, after hot forming, manufactured according to Inventive Example 1, observed with a scanning electron microscope, was illustrated in FIG. 4 , and it was confirmed that alloyed layers (I), (II), and (III) were sequentially formed on the base steel sheet, in the hot press formed part according to Inventive Example 1.
  • FIG. 5 a photograph of a cross-section of a plating layer of the plated steel sheet, after hot forming, manufactured according to Comparative Example 1, observed with a scanning electron microscope, was illustrated in FIG. 5 , and three (3) alloyed layers were sequentially formed on the base steel sheet, in the hot press formed part according to Comparative Example 1.
  • weight loss per unit area was measured for the part after 26 cycles of CCT, and it was determined that the part was deteriorated, when the weight loss per unit area was 10 mg/cm 2 or more.
  • CE refers to Comparative Example
  • Number Density refers to a number density of FeAl(Si) alloy phases having a circle-equivalent diameter of 5 ⁇ m or less in the alloyed layer (II).

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EP19891044.0A 2018-11-30 2019-11-29 Mit einer al-fe-legierung plattiertes stahlblech für die warmverformung mit ausgezeichneter korrosionsbeständigkeit und hitzebeständigkeit, formteil aus einer heisspressung und verfahren zu seiner herstellung Pending EP3889314A4 (de)

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PCT/KR2019/016761 WO2020111879A1 (ko) 2018-11-30 2019-11-29 내식성 및 내열성이 우수한 열간성형용 알루미늄-철 합금 도금 강판, 열간 프레스 성형 부재 및 이들의 제조방법

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US11578397B2 (en) 2018-11-30 2023-02-14 Posco Co., Ltd Hot press-formed part, and manufacturing method thereof
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