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US20140150930A1 - Hot press forming steel plate, formed member using same, and method for manufacturing the plate and member - Google Patents

Hot press forming steel plate, formed member using same, and method for manufacturing the plate and member Download PDF

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Publication number
US20140150930A1
US20140150930A1 US14/232,784 US201114232784A US2014150930A1 US 20140150930 A1 US20140150930 A1 US 20140150930A1 US 201114232784 A US201114232784 A US 201114232784A US 2014150930 A1 US2014150930 A1 US 2014150930A1
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Prior art keywords
steel sheet
less
hot
excluding
temperature
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US14/232,784
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English (en)
Inventor
Kyoo-Young Lee
Jin-keun Oh
Jong-sang Kim
Tae-Kyo Han
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Posco Holdings Inc
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Individual
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Assigned to POSCO reassignment POSCO ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HAN, Tae-Kyo, KIM, JONG-SANG, LEE, KYOO-YOUNG, OH, JIN-KEUN
Publication of US20140150930A1 publication Critical patent/US20140150930A1/en
Abandoned legal-status Critical Current

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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—Rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/26—Special arrangements with regard to simultaneous or subsequent treatment of the 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/1275—Next to Group VIII or IB metal-base component
    • Y10T428/12757—Fe
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present disclosure relates to a steel sheet for hot press forming, a member formed using the steel sheet, and methods for manufacturing the steel sheet and the member, and more particularly, to a steel sheet for manufacturing high-strength and high-ductility products suitable for impact members and crashworthy members of automobiles through a hot press forming process, a member formed using the steel sheet, and methods of manufacturing the steel sheet and the member.
  • AHSS high strength steel
  • DP dual phase
  • TRIP transformation induced plasticity
  • hot press forming has been commercialized to overcome such limitations and realize ultra high-strength automotive components.
  • a steel sheet is subjected to heating to an Ac 3 temperature or higher for transformation into austenite, extracting, press forming, and die quenching, so as to form a martensite or mixed martensite-bainite microstructure.
  • Ultra high-strength members having a tensile strength of 1 GPa or greater and high dimensional precision owning to high-temperature forming can be obtained using the hot press forming method.
  • hot press forming method of the related art is suitable for satisfying rigidity and crash. safety requirements while lightening automotive components, final products have an elongation of 10% or less. That is, final products have a very low level of ductility,
  • components manufactured by a hot press forming method may be used as impact members in automobiles, but may not be suitable for use as crashworthy members that absorb crash energy to protect vehicle occupants in a crash.
  • aspects of the present disclosure may provide a steel sheet for manufacturing a. hot-press formed member having high strength and high ductility, a. member formed using the steel sheet, and methods for manufacturing the steel sheet and the member.
  • a steel sheet for hot press forming may include, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities.
  • a method for manufacturing a steel sheet for hot press forming may include: heating a steel slab to a temperature within a range of 1100° C. to 1300° C., the steel slab including, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, 0.015% or less, N: 0.01% or less, and the balance of Sc and inevitable impurities; performing a finish hot-rolling process at a temperature within a range of an Ar 3 transformation point to 950° C. to form a steel, sheet; and coiling the steel sheet at a temperature within a range of M s to 720° C.
  • a hot-press formed member may include, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0, Al: 0.01% to 2.0%, S: 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities, wherein the hot-press formed member has a dual phase microstructure formed by bainite and retained austenite.
  • a method for manufacturing a hot-press formed member may include: heating a steel sheet to a temperature equal to or higher than Ac:, the steel sheet including, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015% or less, N; 0.01% or less, and the balance of Fe and inevitable impurities; hot-press forming the heated steel sheet; cooling the hot-press formed steel sheet to a temperature within a range of M s to 550° C. at a rate of 20° C./sec or higher; and heat-treating the cooled steel sheet at a temperature within a range of M s to 550° C. in a heating furnace.
  • the present disclosure provides a high-strength, high-ductility steel sheet for hot press forming.
  • the present disclosure also provides a member formed using the steel. sheet and having dual phase microstructure constituted by bainite and retained austenite and a TS(MPa)*E1(%)value of 25,000 MPa % or greater. Since the member has high ductility as well as high strength, the member may be usefully used as a crashworthy member of an automobile.
  • FIG. is a temperature-time graph illustrating manufacturing processes of a hot-press formed member according to an embodiment of the present disclosure.
  • FIGS. 2A to 2C are images showing microstructures of hot-press formed members according to cooling rates after a forming process in a method for manufacturing a hot-press formed member, in which FIG. 2A is the case of a cooling rate of 30° C./sec, FIG. 2B is the case of a cooling rate of 5° C./sec, and FIG. 2C is an enlarged image of FIG. 2B .
  • Embodiments of the present disclosure provide a method for manufacturing a formed member having a high degree of ductility as well as high strength for use as a crashworthy member of an automobile, and a steel sheet having a high. degree of ductility for use in manufacturing such a formed member.
  • the present disclosure provides four categories: a steel sheet for hot press forming having a high degree of ductility, a method for manufacturing the steel sheet, a hot-press formed member, and a method for manufacturing the hot-press formed member.
  • the steel sheet for hot press forming has a high degree of ductility as well as a high degree of strength so that a member formed of the steel sheet through a hot press forming process may have a high degree of ductility and a high degree of strength.
  • the steel sheet for hot press forming includes, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 40%, Si; 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities.
  • Carbon (C) is an element included in the steel sheet to enhance the strength thereof. Furthermore, in the embodiment of the present disclosure, carbon (C) is diffused into retained austenite by elements such as silicon (Si) to stabilize the retained austenite and thus to prevent transformation to martensite.
  • the steel sheet for hot press forming may include 0.3 wt % to 1.0 wt % of carbon (C). If the carbon. content is less than 0.3%, the amount of retained austenite is low after forming, and thus it may be difficult to guarantee both strength and ductility. If the carbon content is greater than 1.0%, bainite transformation is markedly slowed, and the formation of pearlite is facilitated, thereby deteriorating properties of the steel sheet.
  • Manganese (Mn) is included. in the steel sheet to prevent red shortness caused by FeS formed by sulfur (S) inevitably included in the steel sheet during a manufacturing process.
  • the content of manganese (M) may be within the range of 0.01% to 4.0%. If the content of manganese (M) is less than 0.01%, red shortness may be caused by FeS. If the content of manganese (M) is greater than 4.0%, bainite transformation may be slowed. to increase the time required for a heat treatment in hot press forming process. As a result, the productivity of the hot press forming process may be lowered, and the manufacturing cost of the steel sheet may be increased.
  • Silicon (Si) is an element included in the steel sheet to guarantee the ductility of a final product. Silicon (Si) facilitates ferrite transformation and diffuses carbon (C) into retained austenite to stabilize the retained austenite by an increased amount of carbon (C) in the retained austenite, thereby preventing transformation to martensite.
  • the content of silicon (Si) may be within the range of 1.0 wt % to 2.0 wt %. If the content of silicon (Si) is less than 1.0%, the effect of stabilizing retained austenite may be poor. If the content of silicon (Si) greater than 2.0%, the roiling characteristics of the steel sheet may be deteriorated. For example, the steel sheet may be cracked during a rolling process. Therefore, the upper limit, of the content of silicon (Si) is set as 2.0%.
  • Aluminum (Al) removes oxygen from the steel sheet to prevent the inclusion of nonmetallic substances therein during solidification.
  • aluminum (Al) facilitates the diffusion of carbon (C) into retained austenite to stabilize the retained austenite.
  • the content of aluminum (Al) may be within the range of 0.01% to 2.0%. If the content of aluminum (Al) is less than 0.01%, oxygen may be insufficiently removed, and thus it may be difficult to prevent the inclusion of nonmetallic substances. If the content of aluminum (Al) is greater than 2.0%, the unit cost of steel making may be increased.
  • Sulfur (S) is an element inevitably included in the steel sheet during a manufacturing process thereof. Sulfur (S) combines with iron (Fe) to form FeS causing red shortness. Therefore, it may be necessary to keep the content of sulfur (S) as low as possible. For example, the content of sulfur (S) may be limited to 0.015% or less.
  • Nitrogen (N) is an element inevitably included in the steel sheet during a manufacturing process.
  • the content of nitrogen (N) may be kept as low as possible.
  • the content of nitrogen (N) may be limited to 0.01% or less.
  • the steel sheet for hot press forming may further include at least one element selected from the group consisting of Mo: 0.5% or less (excluding 0%), Cr: 1.5% or less (excluding 0%), Ni: 0.5% or less (excluding 0%), Nb: 0.005% to 0.1%, and V: 0.005% to 0.1%.
  • Molybdenum (Mo) may be added to the steel sheet to suppress the formation of pearlite. Since molybdenum (Mo) is relatively expensive and may increase the manufacturing cost of the steel sheet, 0.5 wt % or less of molybdenum (Mo) may be added.
  • Chromium (Cr) may be added to the steel sheet to suppress the formation of ferrite and expand bainite transformation if the content of chromium (Cr) is greater than 1.5 wt %, chromium carbide may he formed to lower the amount of dissolved. carbon (C). Therefore, 1.5 wt % or less of chromium (Cr) may be added.
  • Nickel (Ni) may be added to increase the faction of austenite and the hardenability of the steel sheet. Since nickel (Ni) is expensive and increases the manufacturing cost of the steel sheet, 0.5 wt % or less of nickel (Ni) may be added.
  • Niobium (Nb) may be added to improve the strength, grain refining characteristics, and ductility of the steel sheet. During reheating, niobium (Nb) suppresses grain. growth, and during cooling, niobium (Nb) delays transformation of austenite into ferrite, 0.005 wt % to 0.1 wt % of niobium (Nb) may be added, if the content of niobium (Nb) is less than 0.005%, it is difficult to assure the effect of grain refinement, and if the content of niobium (Nb) is greater than 0.1%, carbonitrides may excessively precipitate to cause delayed fractures in the steel sheet or decrease the workability of the steel sheet.
  • Vanadium (V) may be added to improve the strength, drain refining characteristics, and hardenability of the steel sheet. 0.005 wt % to 0.1 wt % of vanadium (V) may be added. If the content of vanadium (V) is less than 0.005%, such effects may not be obtained, and if the content of vanadium (V) is greater than 0.1%, carbonitrides may excessively precipitate to cause delayed fractures in the steel sheet or decrease the workability of the steel sheet.
  • the steel sheet for hot press forming may further include B: 0.005% or less (excluding 0%) and Ti: 0.06% or less (excluding 0%).
  • Boron (B) may be added to suppress the formation of ferrite. If the content of boron (B) is greater than 0.005 wt %, boron (B) may combine with iron (Fe) or carbon (C) to form a compound facilitating the formation of ferrite. Therefore, 0.005 wt % of less of boron (B) may be added.
  • Titanium (Ti) may be added to maximize the effect of boron (B), Titanium (Ti) combines with nitrogen (N) existing as an impurity in the steel sheet to form TiN, and thus boron (B) may not combine with nitrogen (N). Therefore, the formation of ferrite may be suppressed by boron (B). This effect may be assured by adding 0.06 wt % or less of titanium (Ti).
  • the steel sheet may be a hot-rolled or cold-rolled steel sheet.
  • the steel sheet may be a cold-rolled steel sheet coated with a plating layer for improving corrosion resistance and suppressing the formation of a surface oxide layer.
  • the steel sheet for hot press forming since the steel sheet for hot press forming has high strength and high ductility owing to the above-described composition, the steel sheet may be usefully used to manufacture hot-press formed members (described later) having high strength and ductility.
  • This embodiment is an exemplary example for manufacturing a steel sheet suitable for manufacturing a hot-press formed member having improved ductility.
  • the method for manufacturing a steel sheet for hot press forming includes: heating a steel slab to a temperature within a range of 1100° C. to 1300° C., the steel slab including, by wt %, 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities; performing a finish hot-rolling process at a temperature within a range of Ar 3 transformation point to 950° C. to form a steel sheet; and coiling the steel sheet at a temperature within a range of M s to 720° C.,
  • the continuous-casting structure of the steel slab may be insufficiently uniformized, and it may be difficult to assure a finish rolling temperature. If the steel slab is heated to a temperature greater than 1300° C., the size of crystal grains and the possibility of surface oxidation may increase to deteriorate the strength and surface properties of the steel slab. Therefore, the steel slab may be heated to a temperature within a range of 1100° C. to 1300° C.
  • the finish hot-rolling temperature is lower than Ar 3 transformation point, dual phase rolling may occur to result in hot-rolling mixed grain sizes, and if the finish hot-rolling temperature is higher than 950° C., crystal grains may be coarsened and surface oxidation may occur during the finish hot-rolling process. Therefore, the finish hot-rolling temperature may be within the range of the Ar 3 transformation point to 950° C.
  • the coiling temperature is lower than M s , austenite mar transform to martensite to decrease the ductility of the steel sheet and thus to make it difficult to perform a hot coiling process on the steel sheet. If the coiling temperature is higher than 720° C., a thick surface oxide layer may be formed on the steel sheet together with internal oxidation in the steel sheet. Therefore, the coiling temperature may be within the range of M s to 720° C.
  • the method for manufacturing a steel sheet for hot press forming may include: heating a steel slab a temperature within a range of 1100 ° C. to 1300° C., the steel slab including, by wt %, 0: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015 % or less, N: 0.01% or less, and the balance of Fe and inevitable impurities; performing a finish hot-rolling process at a temperature within a range of Ar 3 transformation point to 950° C.
  • the pickling of the steel sheet is performed to remove surface oxides formed during the heating and finish hot-rolling processes. Thereafter, the cold-rolling
  • the continuous annealing temperature for the cold-rolled steel sheet is lower than 750° C., recrystallization may occur insufficiently, and thus a desired degree of workability of the steel sheet may not be obtained.
  • the continuous annealing temperature is higher than 900° C., it may difficult to heat the steel sheet to the continuous annealing temperature due to the limitation of heating equipment.
  • the overaging temperature is lower than M s , martensite may be formed to excessively increase the strength of the steel sheet and negatively affect the ductility of the steel sheet. Therefore, before a hot press forming process, blanking may not be easily performed.
  • the overaging temperature is higher than 550° C., the processability of the steel sheet may be lowered due to roll surface deterioration in an annealing furnace, and intended carbide precipitation and bainite transformation may not occur in the overaging process.
  • the method for manufacturing a steel sheet for hot press forming may include: heating a steel slab to a temperature range of 1100° C. to 1300° C. the steel slab including, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities; performing a finish hot-rolling process at a temperature within a range of Ar 3 transformation point to 950° C.
  • a hot-dip galvanized steel, sheet may be manufactured by dipping a cold-rolling steel sheet in a galvanizing bath.
  • a galvannealed steel sheet may be manufactured by dipping a cold-rolled steel sheet in a plating bath and performing an alloying heat-treatment process on the steel sheet.
  • An electro-galvanized steel sheet may be manufactured by performing an electro galvanizing process or a Zn—Fe electroplating process on a cold-rolled steel sheet in a continuous electroplating line.
  • a hot-dip aluminized steel sheet may be manufactured by heating a cold-rolled steel sheet, dipping the steel sheet in an aluminum plating bath, and cooling the steel sheet at room temperature at a cooling rate of 5° C./sec to 15° C./sec.
  • the steel slab may further include at least one selected from the group consisting of Mo: 0.5% or less (excluding 0%), Cr: 1.5% or less (excluding 0%), Ni: 0.5% or less (excluding 0%), Nb: 0.005% to 0.1%, and V: 0.005% to 0.1%.
  • the steel slab may further include B: 0.005% or less (excluding 0%) and Ti: 0.06% or less (excluding 0%).
  • the hot-press formed member has high ductility and high strength.
  • the hot-press formed member includes, by wt %, C: 0.3% to 1.0%, Mn: 0.01% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities.
  • the hot-press formed member may have a microstructure formed of bainite and retained austenite without martensite.
  • the hot-press formed member may further include at least one selected from the group consisting of Mo: 0.5% or less (excluding 0%), Cr: 1.5% or less (excluding 0%), Ni: 0.5% or less (excluding 0), Nb: 0.005% to 0.1%, and V: 0.005% to 0.1%.
  • the hot-press formed. member may further include B: 0.005% or less (excluding 0%) and Ti: 0.06% or less (excluding 0%)
  • Hot-press formed members of the related art are manufactured to have ultra high strength, and thus martensite requisitely formed therein.
  • martensite lowers the ductility of such hot-press formed. members and thus makes such hot-press formed members unsuitable to be used as crashworthy members of automobiles. Therefore, in the embodiment of the present disclosure, the formation of martensite in the hot-press formed member is suppressed, and the amount of retained austenite is increased.
  • the hot-press formed member has dual phases: bainite and retained austenite.
  • the hot-press formed member having the above-mentioned composition and microstructure has good strength-ductility balance.
  • TS*E1 of the hot-press formed member may be 25,000 or greater so as to be used as a crashworthy member of an automobile as well as being used as an impact member, where TS denotes tensile strength [MPa] as and E1 denotes elongation [%].
  • the method is for performing a hot press forming process on the above-described steel sheet to provide an ultra high-strength automotive component having high ductility.
  • the method includes: heating a steel sheet to a temperature equal to or higher than Ac 3 , the steel sheet including, by wt %, C: 0.3% to 1.0%, Mn: 0.0l% to 4.0%, Si: 1.0% to 2.0%, Al: 0.01% to 2.0%, S: 0.015% or less, N: 0.01% or less, and the balance of Fe and inevitable impurities; hot-press forming the heated steel sheet; cooling the hot-press formed steel sheet to temperature range of M s to 550° C. at a rate of 20° C./sec or higher; and heat-treating the cooled steel sheet in a heating furnace heated at a temperature within a range of M s to 550° C.
  • the steel sheet may further include at least one selected from the group consisting of Mo: 0.5% or less (excluding 0%), Cr: 1.5% or less (excluding 0%), 0.5% or less (excluding 0%), Nb: 0.005% to 0.1%, and V: 0.005% to 0.1%.
  • the steel sheet may further include B: 0.005% or less (excluding 0%) and Ti: 0.06% or less (excluding 0%).
  • the steel sheet may be one of a hot-rolled steel sheet, a cold-rolled steel sheet, and a plated cold-rolled steel sheet coated with a plating layer.
  • the heat-treating after the hot-press forming is controlled differently as compared with the case of the related art, so as to manufacture a hot-press formed member having a different microstructure for improving ductility as compared with a hot-press formed member of the related art. That is, in the related art, heat-treatment conditions are adjusted to form martensite as a main microstructure to finally obtain an ultra high-strength member.
  • heat treatment conditions for forming a microstructure constituted by bainite and retained austenite without martensite.
  • the steel sheet is heated to a temperature equal to Ac 3 or higher for transformation to austenite, and is then hot-press formed.
  • the heat-treatment conditions after the hot-press forming have a major effect on determining the microstructure of a product the related art, generally a hot-press formed steel sheet is directly die-quenched to a temperature equal to or lower than M s so as to form martensite as a main microstructure in a final product and thus to enhance the strength of the final product.
  • martensite is excluded from the microstructure of a final product so as to improve the ductility of the final product while maintaining the strength of the final product at a level suitable for weight reduction.
  • the hot-press formed steel sheet instead of cooling the hot-press formed steel sheet directly to room temperature equal to or lower than M s , the hot-press formed steel sheet is cooled to a temperature range of M s to 550° C., and heat-treated in a heating furnace at a temperature within a range of M s to 550° C. so as to cause the hot-press formed steel sheet to undergo transformation to bainite.
  • the cooling rate is adjusted to be within the range of M s to 550° C. to form a dual phase microstructure constituted by bainite and retained austenite.
  • Fe 3 C carbide may not be formed because elements such as silicon are sufficiently included in the steel sheet to diffuse carbon (C) into the retained austenite. That is, carbon (C) does not form carbides but is dissolved in the retained austenite to stabilize the retained austenite and thus to lower M s . Therefore, in the next cooling process, transformation to martensite is suppressed. Therefore, in a final product, the retained austenite remains instead of undergoing transformation to martensite, thereby improving ductility.
  • the cooling rate may be 20° C./sec or higher. If the cooling rate is lower than 20° C./sec, transformation to pearlite may easily occur to lower properties of a final product.
  • bainite was formed at a cooling rate of 30° C./sec.
  • FIGS. 2B and 2C a pearlite structure in which ferrite and Fe 3 C were layered was formed at a cooling rate of 5° C./sec.
  • the above-described processes for manufacturing a hot-press formed member according to the embodiment of the present disclosure may be summarized as follows. First, a steel sheet is inserted in a heating furnace to heat the steel sheet to Ac 3 or higher for forming austenite, and then the heated steel sheet is hot-press formed. After the hot press forming, the steel sheet is cooled to a temperature range of M s to 550° C. at a cooling rate of 20° C. sec or higher so as not to form pearlite, and is then heat-treated in a heating furnace at a temperature within a range of M s to 550° C.. These processes are for transformation to bainite, and during the processes, carbon (C) diffuses into austenite to lower M s . Although a hot-press formed member manufactured through the above-described processes is cooled to room temperature without any controlling, transformation to martensite does not occur. That is, a dual phase microstructure constituted by bainite and retained austenite may be obtained.
  • Steel ingots 90 mm in length and 175 mm. in width having compositions shown in Table 1 were manufactured. by vacuum melting, and were then re-heated. at 1200° C. for 1 hour, Thereafter, the steel ingots were hot-rolled to obtain steel sheets having a thickness of 3 mm, At that time, a finish hot-rolling temperature was Ar 3 or higher. Then, after cooling the steel sheets, the steel sheets were inserted into a heating furnace previously heated to 600° C. and left in the heating furnace for 1 hour. Thereafter, the steel sheets were cooled in the heating furnace to simulate hot coiling. Next, the steel sheets were cold-rolled at a reduction ratio of 60% to a thickness of 1.2 mm and were annealed at 900° C. Then, the steel sheets were allowed to undergo bainite transformation at 400° C., In Table 1, the contents of elements are given in wt % except for the contents of sulfur (S) and nitrogen (N) given in ppm.
  • the 1.2 mm thickness steel sheets manufactured as described above were heated to a temperature of 900°C. and maintained at the temperature for 30 seconds, Then, the steel sheets were cooled to cooling temperatures at a rate of 30°C./sec. Next, the steel sheets were inserted into a heating furnace and heat-treated in the heating furnace at the same temperatures as the cooling temperatures for 400 seconds to 10,800 seconds. Thereafter, the steel sheets were air-cooled. In this way, hot-press formed. members were obtained. The process conditions and mechanical properties of the hot-press formed members are shown in Table 2 below.
  • TS*E1 of Comparative Steel 1 cooled. at a cooling rate of 400° C. is 16,735 MPa %
  • Comparative Steel 1 is not suitable as a crashworthy member of an automobile.
  • the reason for this may be that the insufficient content of carbon (C) led to failure in stabilizing retained austenite.
  • the cooling rate was 250° C.
  • Comparative Steel 1 was cooled to a temperature lower than M s to result in a large amount of transformation to martensite, and thus Comparative Steel 1 had high strength but low ductility.
  • TS*El of Comparative Steel 1 is 9,066 MPa %, and Comparative Steel 1 is not suitable to form a crashworthy member of an automobile.
  • Comparative Steel 2 The carbon (C) content and silicon (Si) content of Comparative Steel 2 are also not sufficient to stabilize retained austenite, and the cooling temperature of Comparative Steel 2 is equal to or lower than M s to result in transformation to martensite. Therefore, Comparative Steel 2 has low ductility, and TS*E1 thereof is low at 10,150 MPa %. Comparative Steel 3 also has an insufficient content of carbon (C), and the cooling temperature of Comparative Steel 3 is equal to or lower than M s . Therefore, TS*E1 of Comparative Steel 3 is low at 8,940 MPa %, and Comparative Steel 3 is not suitable to form a. crashworthy member of an automobile.
  • Comparative Steel 4 has a sufficient content of carbon (C), the silicon (Si) content of Comparative Steel 4 is not sufficient to fully diffuse carbon (C) into retained austenite. Therefore, although TS*E1 of Comparative Steel 4 is relatively high at 19,216 MPa % as compared with other comparative steels, TS*E1 of Comparative Steel 4 is not greater than 25,000 MPa %. That is, Comparative Steel 4 is not suitable for forming a crashworthy member of an automobile.
  • Samples of inventive Steel 7 having a composition within the range of the present disclosure were cooled at a cooling rate of 30° C./sec and at a cooling rate of 5° C./sec, respectively.
  • TS*E1 of Inventive Steel 7 was high at 46,923 MPa % and suitable for a crashworthy member of an automobile.
  • TS*E1 of Inventive Steel 7 was low at 12,480 MPa % and not suitable for a crashworthy member of an automobile. The reason for this may be that the low cooling rate led. to the formation of pearlite as shown in FIGS. 2A to 2C and deterioration of properties thereof.

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US20080295923A1 (en) * 2005-12-26 2008-12-04 Posco Carbon Steel Sheet Superior in Formability and Manufacturing Method Thereof
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US10385419B2 (en) 2016-05-10 2019-08-20 United States Steel Corporation High strength steel products and annealing processes for making the same
US11268162B2 (en) 2016-05-10 2022-03-08 United States Steel Corporation High strength annealed steel products
US11560606B2 (en) 2016-05-10 2023-01-24 United States Steel Corporation Methods of producing continuously cast hot rolled high strength steel sheet products
US11993823B2 (en) 2016-05-10 2024-05-28 United States Steel Corporation High strength annealed steel products and annealing processes for making the same
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US11090907B2 (en) 2016-12-23 2021-08-17 Posco Hot dip aluminized steel material having excellent corrosion resistance and workability, and manufacturing method therefor
US12291759B2 (en) 2019-12-19 2025-05-06 Nippon Steel Corporation Steel sheet and manufacturing method thereof

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EP2733228A4 (fr) 2015-08-12
CN103687973A (zh) 2014-03-26
CN103687973B (zh) 2016-08-31
WO2013012103A1 (fr) 2013-01-24
EP2733228A1 (fr) 2014-05-21
JP2014520961A (ja) 2014-08-25
EP2733228B1 (fr) 2019-06-19

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