US20250092485A1 - Hot stamping component and manufacturing method therefor - Google Patents

Hot stamping component and manufacturing method therefor Download PDF

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Publication number
US20250092485A1
US20250092485A1 US18/965,209 US202418965209A US2025092485A1 US 20250092485 A1 US20250092485 A1 US 20250092485A1 US 202418965209 A US202418965209 A US 202418965209A US 2025092485 A1 US2025092485 A1 US 2025092485A1
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Prior art keywords
hot stamping
stamping component
component
base material
depth
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US18/965,209
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Inventor
Min Ho JANG
Seok Hyeon Kang
Min Suh Park
Seong Kyung Han
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Hyundai Steel Co
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Hyundai Steel Co
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Assigned to HYUNDAI STEEL COMPANY reassignment HYUNDAI STEEL COMPANY ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HAN, SEONG KYUNG, JANG, MIN HO, KANG, SEOK HYEON, PARK, MIN SUH
Publication of US20250092485A1 publication Critical patent/US20250092485A1/en
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • 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
    • B21D53/00—Making other particular articles
    • B21D53/88—Making other particular articles other parts for vehicles, e.g. cowlings, mudguards
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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
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—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
    • 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

Definitions

  • the present disclosure relates to a hot stamping component and a manufacturing method therefor.
  • a hot stamping process generally includes heating/forming/cooling/trimming and may use phase transformation of materials and a change in microstructures during the process.
  • a hot stamping steel In order to improve the toughness of hot stamping steel, research has been actively conducted on a method of improving the toughness of a base material by using alloy components.
  • a dew point of an annealing furnace of the base material may be ⁇ 15° C. to +15° C.
  • an annealing temperature of the base material may be 750° C. to 900° C.
  • the method of manufacturing a hot stamping component may further include: after the heating of the blank, transferring the heated blank; forming a molded body by pressing the transferred blank with a mold; and cooling the formed molded body.
  • the hot stamping component may further include: a decarburization layer formed on a surface of the base material; and an inner oxide layer formed on a surface of the decarburization layer.
  • a depth of the inner oxide layer may satisfy Relational Expression 4.
  • C denotes the depth of the inner oxide layer in the plate thickness direction of the hot stamping component.
  • a hot stamping component may comprise a base material including carbon (C), silicon (Si), manganese (Mn), chromium (Cr), boron (B), and other elements, wherein the base material has a microstructure with a martensite fraction of about 90% or more.
  • the component may include a decarburization layer located on the base material, an inner oxide layer located on the decarburization layer, and a plating layer located on the inner oxide layer.
  • the hot stamping component may satisfy the following conditions: a tensile strength (TS) of about 1350 MPa to 1680 MPa, a VDA bending angle of about 60° or more, a relational expression (A/B) ⁇ 0.7, and a relational expression C ⁇ 5 ⁇ m, where A denotes the hardness (Hv( ⁇ 50 ⁇ m)) within the depth of 50 ⁇ m in the plate thickness direction of the hot stamping component, B denotes the average hardness (Hv(avg.)) of the hot stamping component, and C denotes the depth of the inner oxide layer in the plate thickness direction of the hot stamping component.
  • TS tensile strength
  • A/B relational expression
  • C a relational expression
  • the decarburization layer may be softer than the base material and may have an average hardness of 70% or less compared to the average hardness at an about 1 ⁇ 4 plate thickness of the hot stamping component.
  • the plating layer may be a zinc (Zn)-based or aluminum (Al)-based layer with a thickness of about 10 ⁇ m to 30 ⁇ m, providing corrosion resistance and preventing toughness reduction.
  • the depth of the decarburization layer may be controlled to improve the toughness of the component without increasing the risk of liquid metal embrittlement (LME) during high-temperature forming.
  • the hardness ratio (A/B) may ensure that the hot stamping component maintains high toughness and high-temperature formability, reducing surface cracks during forming.
  • the component may have a yield strength (YP) of about 900 MPa to 1300 MPa and an elongation (EL) of about 4% to 10%.
  • the plating layer, decarburization layer, and inner oxide layer may provide a layered structure, enhancing both corrosion resistance and bendability under VDA standards.
  • the toughness of a manufactured hot stamping component may be improved.
  • an inner oxide layer formed on a surface of the decarburization layer is provided below a preset depth, cracks may be prevented from occurring during a hot stamping process.
  • the method and system suitably include use of a controller or processer.
  • vehicles are provided that comprise an apparatus as disclosed herein.
  • the term Ac1 indicates a temperature at which, during the heating, austenite's transformation begins (approximately from 700° C. to 750° C.).
  • yield strength (YP), tensile stress and elongation can be measured according to the ISO standard ISO 6892-1, published in October 2009.
  • FIG. 1 is a cross-sectional view schematically illustrating a hot stamping component, according to an embodiment of the present disclosure.
  • FIG. 2 is a flowchart schematically illustrating a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • FIGS. 3 to 5 are cross-sectional views schematically illustrating a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • FIG. 6 is a flowchart schematically illustrating a hot stamping step, according to an embodiment of the present disclosure.
  • FIG. 7 is a flowchart schematically illustrating a heating step, according to an embodiment of the present disclosure.
  • FIG. 8 is a diagram for describing a heating furnace having a plurality of sections, in a heating step of a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • a layer, region, or component when referred to as being “on” another layer, region, or component, it may be directly on the other layer, region, or component, or may be indirectly on the other layer, region, or component with intervening layers, regions, or components therebetween.
  • a plan view of an object refers to “a view of an object seen from above
  • a cross-sectional view of an object refers to “a view of an object vertically cut and seen from the side.
  • vehicle or “vehicular” or other similar term as used herein is inclusive of motor vehicles in general such as passenger automobiles including sports utility vehicles (SUV), buses, trucks, various commercial vehicles, watercraft including a variety of boats and ships, aircraft, and the like, and includes hybrid vehicles, electric vehicles, plug-in hybrid electric vehicles, hydrogen-powered vehicles and other alternative fuel vehicles (e.g. fuels derived from resources other than petroleum).
  • a hybrid vehicle is a vehicle that has two or more sources of power, for example both gasoline-powered and electric-powered vehicles.
  • FIG. 1 is a cross-sectional view schematically illustrating a hot stamping component, according to an embodiment of the present disclosure.
  • a hot stamping component 1 may include a base material 100 , a decarburization layer 200 , an inner oxide layer 300 , and a plating layer 400 .
  • the base material 100 , the decarburization layer 200 , the inner oxide layer 300 , and the plating layer 400 may be sequentially stacked in a plate thickness direction of the hot stamping component 1 .
  • the base material 100 may include carbon (C), silicon (Si), manganese (Mn), phosphorus (P), sulfur(S), chromium (Cr), boron (B), remaining iron (Fe), and other unavoidable impurities.
  • the base material 100 may include about 0.15 wt % to about 0.3 wt % of carbon (C), about 0.05 wt % to about 0.8 wt % of silicon (Si), about 0.8 wt % to about 3.0 wt % of manganese (Mn), more than 0 wt % but not more than about 0.1 wt % of phosphorus (P), more than 0 wt % but not more than about 0.1 wt % of sulfur(S), about 0.1 wt % to about 0.9 wt % of chromium (Cr), about 0.001 wt % to about 0.005 wt % of boron (B), remaining iron (Fe), and other unavoidable impurities.
  • C carbon
  • Si silicon
  • Mn manganese
  • P phosphorus
  • S sulfur(S)
  • Cr chromium
  • B boron
  • Fe remaining iron
  • the base material 100 may further include at least one component from among titanium (Ti), niobium (Nb), and vanadium (V). Also, the base material 100 may further include calcium (Ca).
  • the base material 100 may further include at least one component from among about 0.01 wt % to about 0.1 wt % of titanium (Ti), about 0.01 wt % to about 0.1 wt % of niobium (Nb), about 0.01 wt % to about 0.1 wt % of vanadium (V), and about 0.0001 wt % to about 0.01 wt % of calcium (Ca).
  • Carbon (C) is a major element that determines the strength and hardness of steel and may be added to ensure a tensile strength of a steel material after a hot stamping (or hot pressing) process. Also, carbon (C) may be added to ensure hardenability characteristics of the steel material. In an embodiment, carbon (C) may be included in an amount of about 0.15 wt % to about 0.3 wt % based on a total weight of the base material 100 . When carbon (C) is included in an amount less than about 0.15 wt % based on the total weight of the base material 100 , it may be difficult to achieve a desired mechanical strength. On the other hand, when carbon (C) is included in an amount more than about 0.3 wt % based on the total weight of the base material 100 , the toughness of the steel material may be reduced or a problem of controlling brittleness of steel may occur.
  • Silicon (Si) may function as a ferrite stabilizing element in the base material 100 .
  • Silicon (Si) may improve ductility by purifying ferrite and may improve a carbon concentration in austenite by suppressing formation of low-temperature carbide.
  • silicon (Si) may be a key element for hot-rolled, cold-rolled, and hot-stamped structure homogenization (perlite and manganese segregation control) and ferrite microdispersion.
  • silicon (Si) may be included in an amount of about 0.05 wt % to about 0.8 wt % based on the total weight of the base material 100 .
  • silicon (Si) When silicon (Si) is included in an amount less than about 0.05 wt % based on the total weight of the base material 100 , the above-described effects may not be sufficiently obtained. On the other hand, when silicon (Si) is included in an amount greater than about 0.8 wt % based on the total weight of the base material 100 , hot rolling and cold rolling loads may increase, hot rolling red scale may be excessive, and adhesion may deteriorate.
  • Manganese (Mn) may be added to increase hardenability and strength during heat treatment.
  • manganese (Mn) may be included in an amount of about 0.8 wt % to about 3.0 wt % based on the total weight of the base material 100 .
  • manganese (Mn) is included in an amount less than about 0.8 wt % based on the total weight of the base material 100 , there may be a high possibility that a material after hot stamping is insufficient (e.g., insufficient hard phase fraction) due to insufficient hardenability.
  • Mn manganese
  • ductility and toughness may be reduced due to manganese (Mn) segregation or perlite bands, bending performance may be reduced, and a inhomogeneous microstructure may be generated.
  • Phosphorus (P) may be an element that easily segregates and reduces the toughness of steel.
  • phosphorus (P) may be included in an amount more than 0 wt % and less than or equal to about 0.1 wt % based on the total weight of the base material 100 .
  • a decrease in the toughness of steel may be prevented.
  • phosphorus (P) is included in an amount greater than about 0.1 wt % based on the total weight of the base material 100 , cracks may occur during the process, and an iron phosphide compound may be formed, thereby reducing the toughness of steel.
  • Sulfur(S) may be an element that reduces workability and physical properties.
  • sulfur(S) may be included in an amount more than 0 wt % and less than or equal to about 0.1 wt % based on the total weight of the base material 100 .
  • sulfur(S) is included in an amount greater than about 0.1 wt % based on the total weight of the base material 100 , hot workability may be reduced, and surface defects such as cracks may occur due to formation of large inclusions.
  • Chromium (Cr) may be added to improve the hardenability and strength of steel.
  • chromium (Cr) may be included in an amount of about 0.1 wt % to about 0.9 wt % based on the total weight of the base material 100 .
  • the hardenability and strength of steel may be improved, an increase in production cost may be prevented, and a decrease in the toughness of the steel material may be prevented.
  • Boron (B) is added to ensure the hardenability and strength of steel by securing a martensite structure and may have a grain refinement effect by increasing an austenite grain growth temperature.
  • boron (B) may be included in an amount of about 0.001 wt % to about 0.005 wt % based on the total weight of the base material 100 .
  • boron (B) is included in above range based on the total weight of the base material 100 , hard grain boundary brittleness may be prevented, and high toughness and bendability may be ensured.
  • Titanium (Ti) may be added to strengthen hardenability and improve a material by forming precipitates after hot stamping heat treatment. Also, titanium (Ti) may effectively contribute to refinement of austenite grains by forming a precipitated phase such as Ti (C,N) at a high temperature. In an embodiment, titanium (Ti) may be included in an amount of about 0.01 wt % to about 0.1 wt % based on the total weight of the base material 100 . When titanium (Ti) is included in the above range based on the total weight of the base material 100 , continuous casting defects may be prevented, coarsening of precipitates may be prevented, physical properties of the steel material may be easily ensured, and cracks on a surface of the steel material may be prevented or minimized.
  • Calcium (Ca) may be added to form CaS to reduce the content of sulfur in steel, and to prevent formation of MnS inclusions that are drawn during hot rolling and induce defects such as hook cracks during electrical resistance welding.
  • the base material 100 may have a microstructure with a martensite fraction of 90% or more.
  • the base material 100 may have a microstructure including 90% or more of martensite, and less than 10% of remaining other unavoidable structures and other precipitates.
  • the decarburization layer 200 may be located on the base material 100 .
  • the decarburization layer 200 may be located on a surface of the base material 100 .
  • the toughness of the hot stamping component 1 may be improved.
  • a layer having a hardness of about 70% or less compared to an average hardness at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 from the surface of the base material 100 may be defined as the decarburization layer 200 .
  • a layer having a hardness of about 70% or less compared to the average hardness at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 from a surface of the hot stamping component 1 may be defined as the decarburization layer 200 . That is, an average hardness of the decarburization layer 200 may be about 70% or less of the average hardness at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 from the surface of the base material 100 or from the surface of the hot stamping component 1 .
  • the average hardness of the decarburization layer 200 may be about 70% or less of the average hardness at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 from the surface of the base material 100 or from the surface of the hot stamping component 1 .
  • the inner oxide layer 300 may be located on the decarburization layer 200 .
  • the inner oxide layer 300 may be located on a surface of the decarburization layer 200 .
  • the inner oxide layer 300 may include silicon (Si), manganese (Mn), chromium (Cr), etc.
  • a depth (or thickness t 1 ) of the inner oxide layer 300 may be about 5 ⁇ m in the plate thickness direction of the hot stamping component 1 , which will be described below in more detail.
  • the plating layer 400 may be located on the inner oxide layer 300 .
  • the plating layer 400 may be located on a surface of the inner oxide layer 300 .
  • the plating layer 400 may be a zinc (Zn)-based plating layer or an aluminum (Al)-based plating layer.
  • the plating layer 400 may include zinc (Zn) and/or aluminum (Al).
  • the plating layer 400 when the plating layer 400 is a zinc (Zn)-based plating layer, the plating layer 400 may include iron (Fe), aluminum (Al), manganese (Mn), silicon (Si), remaining zinc (Zn), and other unavoidable impurities.
  • the plating layer 400 may include about 10 wt % to about 70 wt % of iron (Fe), more than 0 wt % but not more than about 5 wt % of aluminum (Al), more than 0 wt % but not more than about 1 wt % of manganese (Mn), more than 0 wt % but not more than about 1 wt % of silicon (Si), remaining zinc (Zn), and other unavoidable impurities.
  • Fe iron
  • Al aluminum
  • Mn manganese
  • Si silicon
  • Zn remaining zinc
  • the plating layer 400 may have a depth (or thickness t 2 ) of about 10 ⁇ m to about 30 ⁇ m in the plate thickness direction of the hot stamping component 1 .
  • a depth (or thickness t 2 ) of about 10 ⁇ m to about 30 ⁇ m in the plate thickness direction of the hot stamping component 1 .
  • the thickness t 2 of the plating layer 400 is less than about 10 ⁇ m the sacrificial effect of zinc may be reduced, and when the thickness t 2 of the plating layer 400 is greater than about 30 ⁇ m, the thickness t 2 of the plating layer 400 is too large, and thus, the toughness of the hot stamping component 1 including the plating layer 400 may be reduced.
  • the plating layer 400 has the thickness t 2 of about 10 ⁇ m to about 30 ⁇ m, the surface of the base material (or steel material) may be protected, and at the same time, a decrease in the toughness of the hot stamping component 1 may be prevented or minimized.
  • the decarburization layer 200 is softer than the base material 100 , and when the hot stamping component 1 includes the decarburization layer 200 , the toughness of the hot stamping component 1 including the decarburization layer 200 may be improved.
  • the depth (or thickness t 1 ) of the inner oxide layer 300 when the depth (or thickness t 1 ) of the inner oxide layer 300 is too large, liquid zinc may more easily penetrate into the base material 100 by the inner oxide layer 300 , the risk of cracks during hot stamping forming may increase, and thus, the bendability of the manufactured hot stamping component 1 may be reduced.
  • the depth (or the thickness t 1 ) of the inner oxide layer 300 is greater than about 5 ⁇ m, liquid zinc may more easily penetrate into the base material 100 due to the inner oxide layer 300 , the risk of cracks during hot stamping forming may increase, and thus, the bendability of the manufactured hot stamping component 1 may be reduced.
  • the decarburization layer 200 may be formed on the base material 100 in an annealing step.
  • the inner oxide layer 300 may be simultaneously formed on the decarburization layer 200 .
  • the decarburization layer 200 may be formed on the surface of the base material 100 , and at the same time, the inner oxide layer 300 may be formed on the surface of the decarburization layer 200 .
  • a depth (or thickness) of the decarburization layer 200 may increase.
  • the depth (or thickness) of the inner oxide layer 300 may also increase. That is, in order to increase the toughness of the hot stamping component 1 , the depth (or thickness) of the decarburization layer 200 should increase.
  • the depth (or thickness) of the inner oxide layer 300 may also increase, thereby increasing the risk of cracks during hot stamping forming and reducing the bendability of the manufactured hot stamping component 1 . Accordingly, it is necessary to appropriately adjust the depth (or thickness) of the decarburization layer 200 and the depth (or thickness) of the inner oxide layer 300 .
  • the inventors of the present disclosure have derived Relational Expressions 1 and 2 through excessively repeated experiments to enable the hot stamping component 1 to have a VDA bending angle of about 60° or more.
  • the hot stamping component 1 may satisfy Relational Expressions 1 and 2.
  • a hardness within a depth of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1 and an average hardness of the hot stamping component 1 may satisfy Relational Expression 1
  • the depth (or thickness) of the inner oxide layer 300 may satisfy Relational Expression 2.
  • the hot stamping component 1 may satisfy both Relational Expression 1 and Relational Expression 2.
  • A denotes the hardness (Hv( ⁇ 50 ⁇ m)) within the depth (or thickness) of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1
  • B denotes the average hardness (Hv(avg.)) of the hot stamping component 1 .
  • the hardness within the depth of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1 may be a hardness value measured with a Vickers hardness tester at a depth of about 50 ⁇ m or less in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1
  • the average hardness (Hv(avg.)) of the hot stamping component 1 may be a hardness value measured with the Vickers hardness tester at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 .
  • C denotes the depth (or thickness) of the inner oxide layer 300 in the plate thickness direction of the hot stamping component 1 .
  • the decarburization layer 200 may be located on a portion adjacent to the surface of the hot stamping component 1 . Because the decarburization layer 200 is softer than the base material 100 , a hardness of a portion of the hot stamping component 1 adjacent to the surface of the hot stamping component 1 may be lower than the average hardness of the hot stamping component 1 . In this case, when the depth (or thickness) of the decarburization layer 200 increases, a difference between the hardness of the portion of the hot stamping component 1 adjacent to the surface of the hot stamping component 1 and the average hardness of the hot stamping component 1 may increase.
  • the depth (or thickness) of the decarburization layer 200 decreases, a difference between the hardness of the portion of the hot stamping component 1 adjacent to the surface of the hot stamping component 1 and the average hardness of the hot stamping component 1 may decrease.
  • the decarburization layer 200 is not formed (or provided) to a sufficient depth (or thickness), and thus, the toughness of the hot stamping component 1 including the decarburization layer 200 may be low.
  • a VDA bending angle of the hot stamping component 1 may be less than about 60°.
  • the ratio between the hardness (Hv( ⁇ 50 ⁇ m)) within the depth (or thickness) of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 and the average hardness (Hv(avg.)) of the hot stamping component 1 is equal to or less than 0.7, it may mean that the decarburization layer 200 is formed (or provided) to a sufficient depth (or thickness).
  • the hot stamping component 1 when the ratio between the hardness (Hv( ⁇ 50 ⁇ m)) within the depth (or thickness) of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 and the average hardness (Hv(avg.)) of the hot stamping component 1 satisfies about 0.7 or less, the decarburization layer 200 is formed (or provided) to a sufficient depth (or thickness), and thus, the toughness of the hot stamping component 1 including the decarburization layer 200 may be improved.
  • the hot stamping component 1 may have a VDA bending angle of about 60° or more.
  • the depth (or thickness) of the inner oxide layer 300 included in the hot stamping component 1 may be about 5 ⁇ m or less.
  • liquid metal embrittlement may occur due to a low melting point of zinc, which may cause cracks to occur inside and may reduce the bendability of the hot stamping component 1 .
  • LME liquid metal embrittlement
  • the depth (or thickness) of the inner oxide layer 300 is large, liquid zinc may more easily penetrate into the inside due to the inner oxide layer 300 , the risk of cracks during hot stamping forming may increase, and thus, the bendability of the manufactured hot stamping component 1 may be reduced.
  • the depth (or thickness) of the inner oxide layer 300 is greater than about 5 ⁇ m, liquid zinc may more easily penetrate into the inside due to the inner oxide layer 300 , the risk of cracks during hot stamping forming may increase, and thus, the bendability of the manufactured hot stamping component 1 may be reduced.
  • the depth (or thickness) of the inner oxide layer 300 is about 5 ⁇ m or less in the plate thickness direction of the hot stamping component 1 , cracks may be prevented from occurring during hot stamping, and thus, the high-temperature formability of the hot stamping component (or blank) may be improved.
  • the hot stamping component 1 may satisfy Relational Expression 1 and Relational Expression 2 at the same time.
  • the hot stamping component 1 may have high toughness and the high-temperature formability of the hot stamping component 1 may be excellent.
  • the hot stamping component 1 may have high toughness and the high-temperature formability of the hot stamping component 1 may be excellent.
  • the hot stamping component 1 when the hot stamping component 1 satisfies both Relational Expression 1 and Relational Expression 2, the hot stamping component 1 may have a tensile strength (TS) of about 1350 MPa to about 1680 MPa, a yield strength (YP) of about 900 MPa to about 1300 MPa, and an elongation (EL) of about 4% to about 10%. Also, the hot stamping component 1 may have a VDA bending angle of about 60° or more. In this case, the VDA bending angle may be measured in accordance with the VDA standard (VDA238-100).
  • FIG. 2 is a flowchart schematically illustrating a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • FIGS. 3 to 5 are cross-sectional views schematically illustrating a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • a method of manufacturing the hot stamping component 1 may include a hot rolling step S 100 , a cooling/coiling step S 200 , a cold rolling step S 300 , an annealing step S 400 , a plating step S 500 , and a hot stamping step S 600 .
  • a reheating step of the base material 100 (e.g., steel slab) prepared with the composition described with reference to FIG. 1 may be performed.
  • the steel slab reheating step the steel slab obtained through a continuous casting process may be reheated to a certain temperature so that components segregated during casting are resolved.
  • a slab reheating temperature (SRT) may be about 1,200° C. to about 1,400° C.
  • SRT slab reheating temperature
  • the components segregated during the casting may not be sufficiently resolved, and thus, it may be difficult to have the homogenization effect of alloy elements significantly and it may be difficult to have the solution effect of titanium (Ti) significantly.
  • the slab reheating temperature (SRT) When the slab reheating temperature (SRT) is high, the slab reheating temperature (SRT) is favorable for homogenization. However, when the slab reheating temperature (SRT) is higher than about 1,400° C., an austenite crystal grain size may increase, and thus, it may be difficult to ensure strength, and the manufacturing cost of a steel sheet may increase due to an excessive heating process.
  • the reheated base material 100 may be hot-rolled at a certain finishing rolling temperature.
  • a hot-rolled steel sheet may be manufactured through the hot rolling step S 100 .
  • a finishing delivery temperature (FDT) may be about 880° C. to about 950° C.
  • the finishing delivery temperature (FDT) is lower than about 880° C.
  • the workability of the steel sheet may not be ensured due to the occurrence of a mixed grain structure caused by abnormal area rolling, workability may be reduced due to microstructure unevenness, and a passing ability problem may occur during hot rolling due to a rapid phase change.
  • the finishing delivery temperature (FDT) is higher than about 950° C., austenite grains may be coarsened, TiC precipitates may be coarsened, and thus, the performance of the hot stamping component may deteriorate.
  • the hot-rolled base material 100 may be cooled and coiled to a certain coiling temperature (CT).
  • CT coiling temperature
  • the coiling temperature (CT) of the cooling/coiling step S 300 may be about 550° C. to about 800° C.
  • the coiling temperature (CT) may affect the redistribution of carbon (C), and when the coiling temperature (CT) is lower than about 550° C., a low-temperature phase fraction may increase due to subcooling, strength may increase, a rolling load may increase during cold rolling, and ductility may rapidly decrease.
  • CT coiling temperature
  • abnormal crystal grain growth or excessive crystal grain growth may cause deterioration in formability and strength.
  • the coiled base material 100 may be uncoiled, pickled, and then cold rolled.
  • the pickling may be performed to remove scale from the coiled steel sheet (or base material), that is, a hot-rolled coil manufactured through the hot rolling process described above.
  • a cold-rolled steel sheet may be manufactured through the cold rolling step S 300 .
  • the cold-rolled base material 100 may be annealed at a temperature of about 700° C. or more.
  • the annealing step S 400 may include heating the cold-rolled base material 100 and cooling the heated base material 100 at a certain cooling rate.
  • the base material may be annealed in the annealing step S 400 .
  • the annealing step S 400 may be performed in an annealing furnace.
  • the annealing of the base material 100 may be performed in a gas atmosphere including about 0.5 vol % to about 25 vol % of hydrogen and remaining nitrogen.
  • water may be sprayed into the annealing furnace together with hydrogen gas and nitrogen gas.
  • a dew point of the annealing furnace may increase. Accordingly, the dew point of the annealing furnace may be controlled by controlling the amount of water sprayed into the annealing furnace.
  • the decarburization layer 200 may be formed on the base material 100 .
  • carbon may be lost from a surface of the base material 100 to form the decarburization layer 200 .
  • the inner oxide layer 300 may be formed on the decarburization layer 200 . That is, the decarburization layer 200 may be formed on the surface of the base material 100 , and the inner oxide layer 300 may be formed on a surface of the decarburization layer 200 .
  • the decarburization layer 200 and the inner oxide layer 300 may be layers obtained by changing a portion of the base material 100 .
  • a layer having a hardness of about 80% or less compared to an average hardness at about 1 ⁇ 4 point from the surface of the base material 100 may be defined as the decarburization layer 200 . That is, an average hardness of the decarburization layer 200 may be about 80% or less of the average hardness at about 1 ⁇ 4 point from the surface of the base material 100 .
  • the dew point of the annealing furnace where the annealing of the base material 100 is performed may be about ⁇ 15° C. to about +15° C.
  • the decarburization layer 200 is formed on the base material 100 in order to improve the toughness of the manufactured hot stamping component 1 .
  • a depth (or thickness) of the decarburization layer 200 may be too small, and thus, the effect of improving the toughness of the manufactured hot stamping component may be insignificant.
  • the dew point of the annealing furnace is about +15° C.
  • a depth (or thickness t 3 ) of the inner oxide layer 300 may be too large, and thus LME cracks may occur, and operability may be reduced due to equipment oxidation.
  • a large amount of water should be supplied to the annealing furnace in order to increase the dew point of the annealing furnace.
  • equipment of the annealing furnace may be oxidized, and it may take a long time to clean the equipment, thereby reducing operability.
  • the depth (or thickness) of the decarburization layer 200 and the depth (or thickness t 3 ) of the inner oxide layer 300 may increase, and thus, cracks may occur inside during high-temperature forming due to the inner oxide layer 300 . Accordingly, when the dew point of the annealing furnace where the annealing of the base material 100 is performed satisfies about ⁇ 15° C. to about +15° C., the toughness of the manufactured hot stamping component 1 may be improved and the efficiency of a manufacturing process may be improved.
  • the productivity of the hot stamping component may be improved, and at the same time, the toughness of the manufactured hot stamping component may be improved.
  • the plating step S 500 may be a step of forming the plating layer 400 on the annealed base material 100 .
  • the plating layer 400 may be formed on the annealed base material 100 through the plating step S 500 .
  • the plating layer 400 may be formed on a surface of the inner oxide layer 300 through the plating step S 500 .
  • the plating layer 400 may include a zinc (Z)-based plating layer or an aluminum (Al)-based plating layer.
  • the annealed base material 100 may be immersed in a plating bath.
  • the plating bath may be maintained at a temperature of about 400° C. to about 700° C.
  • the adhesion amount of the plating layer may be about 40 g/m 2 to about 200 g/m 2 on both surfaces of the base material 100 (or the inner oxide layer 300 ).
  • a depth (or thickness t 4 ) of the plating layer 400 formed on the base material 100 or the decarburization layer 200 may be about 5 ⁇ m to about 20 ⁇ m in the plate thickness direction of the base material 100 .
  • the depth (or thickness) of the plating layer 400 is about 5 ⁇ m or less, the sacrificial method of the plating layer 400 may be insufficient.
  • the depth (or thickness) of the plating layer 400 is about 20 ⁇ m or more, the cost of forming the plating layer 400 may increase, thereby reducing economic feasibility. Accordingly, when the depth (or thickness t 4 ) of the plating layer 400 satisfies about 5 ⁇ m to about 20 ⁇ m, corrosion of the base material 100 of the hot stamping component 1 may be prevented or minimized.
  • the annealing step S 400 and the plating step S 500 may be performed on the same line. Accordingly, a line speed at which the plating step S 500 is performed may be about 30 mpm to about 200 mpm. When the line speed is about 30 mpm or less, the line speed may be too slow, and thus, productivity may be reduced. A plating amount is controlled by using an air knife. When the line speed is about 200 mpm or more, the line speed may be too fast, and thus, it may be difficult to control the plating amount by using the air knife. Accordingly, when the line speed at which the plating step S 500 is performed satisfies about 30 mpm to about 200 mpm, productivity may be improved, and at the same time, the plating amount may be easily controlled.
  • a plated steel sheet having the plating layer 400 formed on at least one surface of the base material 100 may be manufactured through the plating step S 500 .
  • the plated steel sheet may include the base material 100 , the decarburization layer 200 formed on the base material 100 , the inner oxide layer 300 formed on the decarburization layer 200 , and the plating layer 400 formed on the inner oxide layer 300 .
  • the plated steel sheet may include the base material 100 , the decarburization layer 200 formed on the surface of the base material 100 , the inner oxide layer 300 formed on the surface of the decarburization layer 200 , and the plating layer 400 formed on the surface of the inner oxide layer 300 .
  • FIG. 6 is a flowchart schematically illustrating a hot stamping step, according to an embodiment of the present disclosure.
  • FIG. 7 is a flowchart schematically illustrating a heating step, according to an embodiment of the present disclosure.
  • the hot stamping step S 600 may be performed after the plating step S 500 (see FIG. 2 ).
  • the hot stamping step S 600 may include a heating step S 610 , a transferring step S 620 , a forming step S 630 , and a cooling step S 640 .
  • a blank may be formed by cutting the plated steel sheet having the plating layer 400 (see FIG. 5 ) formed on at least one surface of the base material 100 (see FIG. 5 ).
  • the decarburization layer 200 (see FIG. 5 ) and the inner oxide layer 300 (see FIG. 5 ) may be located between the base material 100 and the plating layer 400 .
  • the blank may be heated in a heating furnace having a plurality of sections with different temperature ranges.
  • the heating step S 610 may include a multi-stage heating step S 611 and a soaking step S 612 .
  • the multi-stage heating step S 611 and the soaking step S 612 may be steps in which the blank is heated while passing through the plurality of sections provided in the heating furnace.
  • an overall temperature of the heating furnace may be about 680° C. to about 910° C.
  • the overall temperature of the heating furnace where the multi-stage heating step S 611 and the soaking step S 612 are performed may be about 680° C. to about 910° C.
  • a temperature of the heating furnace where the multi-stage heating step S 611 is performed may be about 680° C. to about Ac1
  • a temperature of the heating furnace where the soaking step S 612 is performed may be about Ac1 to about 910° C.
  • the soaking step S 612 may be performed after the multi-stage heating step S 611 .
  • the stepwise heated blank may be heated (or soaked) while passing through a section of the heating furnace set to a temperature of about Ac1 to about 910° C. From among the plurality of sections provided in the heating furnace, there may be at least one section in which the soaking step S 612 is performed.
  • FIG. 8 is a diagram for describing a heating furnace having a plurality of sections, in a heating step of a method of manufacturing a hot stamping component, according to an embodiment of the present disclosure.
  • a heating furnace may include a plurality of sections with different temperature ranges.
  • the heating furnace may include a first section P 1 with a first temperature range T 1 , a second section P 2 with a second temperature range T 2 , a third section P 3 with a third temperature range T 3 , a fourth section P 4 with a fourth temperature range T 4 , a fifth section P 5 with a fifth temperature range T 5 , a sixth section P 6 with a sixth temperature range T 6 , and a seventh section P 7 with a seventh temperature range T 7 .
  • the first section P 1 to the seventh section P 7 may be sequentially arranged in the heating furnace.
  • the first section P 1 with the first temperature range T 1 may be adjacent to an inlet of the heating furnace into which the blank is inserted, and the seventh section P 7 with the seventh temperature range T 7 may be adjacent to an outlet of the heating furnace from which the blank is taken out.
  • the first section P 1 with the first temperature range T 1 may be a first section of the heating furnace, and the seventh section P 7 with the seventh temperature range T 7 may be a last section of the heating furnace.
  • Temperatures of the plurality of sections provided in the heating furnace may increase in a direction from the inlet of the heating furnace into which the blank is inserted to the outlet of the heating furnace from which the blank is taken out.
  • temperatures of the fifth section P 5 , the sixth section P 6 , and the seventh section P 7 may be the same.
  • a temperature difference between two adjacent sections from among the plurality of sections provided in the heating furnace may be greater than about 0° C. and less than or equal to about 100° C.
  • a temperature difference between the first section P 1 and the second section P 2 may be greater than about 0° C. and less than or equal to about 100° C.
  • a heating furnace temperature of the soaking step S 612 may be about Ac1 to about 910° C.
  • the manufactured hot stamping component may not have a desired material.
  • zinc (Zn) included in the plating layer 400 may be vaporized, resulting in loss of the plating layer 400 . Accordingly, when the heating furnace temperature of the soaking step S 612 satisfies about Ac1 to about 910° C., the manufactured hot stamping component may be formed of a desired material, and loss of the plating layer 400 may be prevented.
  • the heating furnace includes seven sections with different temperature ranges in FIG. 8 , the present disclosure is not limited thereto.
  • the heating furnace may include five, sixth, or eight sections with different temperature ranges.
  • the heating step S 610 includes the multi-stage heating step S 611 and the soaking step S 612 , a temperature of the heating furnace may be set in stages, and thus, the energy efficiency of the heating furnace may be improved.
  • the heating furnace may have a length of about 20 m to about 40 m along a transfer path of the blank.
  • the heating furnace may include the plurality of sections with different temperature ranges, and a ratio between a length of a section where the blank is stepwise heated and a length of a section where the blank is soaked from among the plurality of sections may satisfy about 1:1 to about 4:1.
  • the length of the section where the blank is soaked in the heating furnace increases and the ratio between the length of the section where the blank is stepwise heated and the length of the section where the blank is soaked is greater than about 1:1, the amount of hydrogen penetrating into the blank in the soaking section may increase, thereby increasing delayed fracture.
  • the soaking section (or time) is not sufficiently secured, and thus, the strength of the hot stamping component manufactured by the process of manufacturing a hot stamping component may be uneven.
  • the length of the soaking section from among the plurality of sections provided in the heating furnace may be about 20% to about 50% of a total length of the heating furnace.
  • a total heating time during which the heating step S 610 is performed may be about 2 min to about 20 min. That is, a total time during which the blank stays in the heating furnace may be about 2 min to about 20 min.
  • a heating time may be insufficient and thus, the manufactured hot stamping component 1 may not have a desired material.
  • the total heating time during which the heating step S 610 is performed is about 20 min or more, a heating time may be too long and thus, a production speed may decrease, and economic feasibility may decrease.
  • the manufactured hot stamping component 1 may have a desired material, and at the same time, a decrease in the economic feasibility of the manufacturing process may be prevented or minimized.
  • the heating step S 610 After the heating step S 610 , the transferring step S 620 , the forming step S 630 , and the cooling step S 640 may be further performed.
  • the transferring step S 620 may be a step of transferring the heated blank from the heating furnace to a mold.
  • the heated blank may be cooled to an atmospheric temperature (or room temperature). That is, the heated blank may be air-cooled during transfer.
  • a mold entry temperature e.g., forming start temperature
  • wrinkles or bends
  • the heated blank is air-cooled during transfer.
  • the forming step S 630 may be a step of hot stamping the transferred blank to form a molded body.
  • the blank may be pressed with the mold to form a molded body.
  • the forming start temperature may be about 500° C. to about 700° C.
  • the forming start temperature may be too low, and thus, the formability of the blank may decrease, and the manufactured hot stamping component 1 may not have a desired structure and properties.
  • the forming start temperature is higher than about 700° C., wrinkles (or bends) may occur on the surface of the manufactured hot stamping component 1 .
  • the plating layer 400 may stick to the mold. Accordingly, when the forming start signal is about 500° C. to about 700° C., the formability of the blank may be improved, the manufactured hot stamping component 1 may have a desired structure and properties, and the occurrence of wrinkles (or bends) on the surface of the manufactured hot stamping component 1 may be prevented or minimized.
  • the cooling step S 640 may be a step of cooling the molded body.
  • the cooling step S 640 may be performed in the mold in which the blank is pressed.
  • a final product may be formed by cooling the molded body at the same time as forming the molded body into a final component shape.
  • a cooling channel through which a refrigerant circulates may be provided in the mold.
  • the molded body may be rapidly cooled by circulation of the refrigerant supplied through the cooling channel provided in the mold.
  • the blank in order to prevent a spring back phenomenon of a plate material and maintain a desired shape, the blank may be pressed and rapidly cooled while the mold is closed.
  • the molded body may be cooled at an average cooling rate of at least about 10° C./s to a martensite end temperature.
  • a cooling end temperature at which the cooling step S 640 ends may be about room temperature to about 200° C.
  • the productivity of the manufacturing process may decrease.
  • the cooling end temperature is higher than about 200° C.
  • the manufactured hot stamping component 1 is air-cooled at room temperature, and in this case, distortion may occur in the hot stamping component 1 , and it may be difficult to secure a target material. Accordingly, when the cooling end temperature at which the cooling step S 640 ends satisfies room temperature to about 200° C., the productivity of the manufacturing process may be improved, and distortion of the manufactured hot stamping component 1 may be prevented or minimized.
  • the inventors of the present disclosure have derived Relational Expressions 3 and 4 through excessively repeated experiments to enable the manufactured hot stamping component 1 to have a VDA bending angle of about 60° or more.
  • the manufactured hot stamping component 1 may satisfy Relational Expressions 3 and 4.
  • a hardness within a depth of 50 ⁇ m in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1 and an average hardness of the hot stamping component 1 may satisfy Relational Expression 3
  • a depth (or thickness) of the inner oxide layer 300 may satisfy Relational Expression 4.
  • the hot stamping component 1 may satisfy both Relational Expression 3 and Relational Expression 4.
  • A denotes the hardness (Hv( ⁇ 50 ⁇ m)) within the depth (or thickness) of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1
  • B denotes the average hardness (Hv(avg.)) of the hot stamping component 1 .
  • the hardness within the depth of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1 may be a hardness value measured with a Vickers hardness tester at a depth of about 50 ⁇ m or less in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1
  • the average hardness (Hv(avg.)) of the hot stamping component 1 may be a hardness value measured with the Vickers hardness tester at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 .
  • C denotes the depth (or thickness) of the inner oxide layer 300 in the plate thickness direction of the hot stamping component 1 .
  • the toughness of the hot stamping component 1 manufactured through the method of manufacturing a hot stamping component may be improved.
  • the hot stamping component 1 manufactured through the method of manufacturing a hot stamping component may have a VDA bending angle of about 60° or more.
  • the hot stamping component 1 manufactured through the method of manufacturing a hot stamping component may have a tensile strength (TS) of about 1350 MPa to about 1680 MPa, a yield strength (YP) of about 900 MPa to about 1300 MPa, and an elongation (EL) of about 4% to about 10%.
  • TS tensile strength
  • YP yield strength
  • EL elongation
  • Embodiment 1, Embodiment 2, Comparative Example 1, and Comparative Example 2 are hot stamping components (samples) manufactured using a slab having a composition shown in Table 1 under process conditions shown in Table 2.
  • A denotes the hardness (Hv( ⁇ 50 ⁇ m)) within the depth (or thickness) of about 50 ⁇ m in the plate thickness direction of the hot stamping component
  • B denotes the average hardness (Hv(avg.)) of the hot stamping component
  • C denotes the depth (or thickness) of the inner oxide layer 300 in the plate thickness direction of the hot stamping component.
  • the hardness within the depth of about 50 ⁇ m in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1 may be a hardness value measured with a Vickers hardness tester at a depth of about 50 ⁇ m or less in the plate thickness direction of the hot stamping component 1 from the surface of the hot stamping component 1
  • the average hardness (Hv(avg.)) of the hot stamping component 1 may be a hardness value measured with the Vickers hardness tester at about 1 ⁇ 4 point in the plate thickness direction of the hot stamping component 1 .
  • the VDA bending angle was evaluated by using the VDA standard (VDA238-100), and the crack depth was measured by using a scanning electron microscope.
  • the crack depth corresponds to a deepest crack depth measured through the scanning electron microscope.
  • the VDA bending angle of the hot stamping component required by the present disclosure is 60° or more. Also, when the crack depth in the hot stamping component is large, the VDA bending angle of the hot stamping component may decrease, and the toughness of the hot stamping component may decrease. Accordingly, the crack depth in the hot stamping component required by the present disclosure is 10 ⁇ m or less. When the crack depth is out of the range, it corresponds to a case where the required conditions are not satisfied.
  • Embodiments 1 and 2 correspond to a case where both Relational Expression 1 ((A/B) ⁇ 0.7) and Relational Expression 2 (C ⁇ 5) are satisfied, Comparative Example 1 corresponds to a case where Relational Expression 2 (C ⁇ 5) is not satisfied, and Comparative Example 2 corresponds to a case where Relational Expression 1 ((A/B) ⁇ 0.7) is not satisfied.
  • Embodiment 1, Embodiment 2, Comparative Example 1, and Comparative Example 2 correspond to samples manufactured using the base material 100 (or steel sheet) satisfying the composition of FIG. 1 according to the method of manufacturing a hot stamping component. However, Comparative Example 1 and Comparative Example 2 are samples that do not satisfy Relational Expression 1 ((A/B) ⁇ 0.7) and/or Relational Expression 2 (C ⁇ 5) due to a difference in process control conditions.
  • Relational Expression 2 (C ⁇ 5) when Relational Expression 2 (C ⁇ 5) is not satisfied, it may be found that the VDA bending angle, and the crack depth do not satisfy the required conditions. In detail, when Relational Expression 2 (C ⁇ 5) is not satisfied, it may be found that the VDA bending angle is less than 60° and the crack depth is greater than 10 ⁇ m.
  • Relational Expression 1 ((A/B) ⁇ 0.7) is not satisfied, it may be found that the VDA bending angle does not satisfy the required condition. In detail, when Relational Expression 1 ((A/B) ⁇ 0.7) is not satisfied, it may be found that the VDA bending angle is less than 60°.
  • the hot stamping component 1 when the hot stamping component 1 satisfies both Relational Expression 1 ((A/B) ⁇ 0.7) and Relational Expression 2 (C ⁇ 5), the hot stamping component 1 may have the required VDA bending angle, and the crack depth in the hot stamping component 1 may be formed below a preset value. That is, when the hot stamping component 1 satisfies both Relational Expression 1 ((A/B) ⁇ 0.7) and Relational Expression 2 (C ⁇ 5), the hot stamping component 1 may have excellent toughness and high-temperature formability.

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KR20230166780A (ko) 2023-12-07
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