US20150064052A1 - Warm press forming method and automobile frame component - Google Patents

Warm press forming method and automobile frame component Download PDF

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Publication number
US20150064052A1
US20150064052A1 US14/382,995 US201314382995A US2015064052A1 US 20150064052 A1 US20150064052 A1 US 20150064052A1 US 201314382995 A US201314382995 A US 201314382995A US 2015064052 A1 US2015064052 A1 US 2015064052A1
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steel sheet
mass
press
forming
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Yuichi Tokita
Yoshikiyo Tamai
Toru Minote
Takeshi Fujita
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JFE Steel Corp
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JFE Steel Corp
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K7/00—Making railway appurtenances; Making vehicle parts
    • B21K7/12—Making railway appurtenances; Making vehicle parts parts for locomotives or vehicles, e.g. frames, underframes
    • 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
    • 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
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • 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
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    • C22C—ALLOYS
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
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    • C22C38/007—Ferrous alloys, e.g. steel alloys containing silver
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C—ALLOYS
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
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    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C23C2/26—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
    • 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
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/005—Ferrite

Definitions

  • This disclosure relates to a warm press forming method that can suppress defects in dimensional accuracy due to geometric changes such as springback that occur in a high strength steel sheet being press-formed.
  • the disclosure also relates to an automobile frame component produced by the warm press forming method.
  • high strength steel sheets have been increasingly applied to automotive parts. It is generally known, however, that high strength steel sheets exhibit poor press formability, undergo considerable geometric changes (springback) caused by elastic recovery after being removed from the die, and are prone to defects in dimensional accuracy. Thus, there are currently a limited number of parts that can be obtained by applying press forming to high strength steel sheets.
  • JP 2005-205416 A discloses an example of hot press forming applied to a high strength steel sheet in which a steel sheet is press-formed after being heated to a predetermined temperature.
  • the aforementioned hot press forming involves forming of a steel sheet at temperatures higher than those at which cold press forming is performed to reduce the deformation resistance of the steel sheet for press forming, in other words, to increase the deformation capacity thereof, aiming to improve the shape fixability and at the same time prevent the occurrence of press cracking.
  • press forming is based on draw forming.
  • edges of the heated steel sheet (which will be also called a “blank”) are compressed between a die and a blank holder during the formation process and, accordingly, the edges of the blank and other portions thereof contact with, e.g., the die for different times.
  • a drop in the temperature of the contact zone of the blank during the press forming process leads to a non-uniform temperature distribution in the press-formed part immediately after the formation (hereinafter also called “panel”) due to the difference in the contact time with the aforementioned die, and so on.
  • general hot press forming involves heating of a steel sheet to the austenite region as well as cooling of the steel sheet accompanying quenching and phase transformation and, consequently, the microstructure of the steel sheet tends to change after formation, causing the problem of large variations in the tensile properties such as strength and ductility, of the press-formed part.
  • the steel sheet has a microstructure containing a ferrite phase by 95% or more on an area ratio basis with respect to the entire microstructure, ferrite crystal grains constituting the ferrite phase have an average grain size of 1 ⁇ M or more, and carbides having an average particle size of 10 nm or less are dispersed and precipitated in the ferrite crystal grains
  • the warm press forming method according to any one of the aspects [4] to [9], wherein the chemical composition further contains, by mass %, at least one selected from O, Se, Te, Po, As, Bi, Ge, Pb, Ga, In, Tl, Zn, Cd, Hg, Ag, Au, Pd, Pt, Co, Rh, Ir, Ru, Os, Tc, Re, Ta, Be and Sr, in a total amount of 2.0% or less.
  • the warm press forming does not involve quenching and/or phase transformation before and after the forming process and can directly make use of the mechanical properties of steel sheets as blank material, thereby allowing for stable production of press-formed parts with desired properties.
  • FIGS. 1 a - 1 c illustrate a press forming process using draw forming, where (a) shows a state when the forming process starts, (b) shows a state during the forming process, and (c) shows a state at the press bottom dead point (a state when the forming process ends).
  • FIG. 2( a ) illustrates an exemplary automobile frame component produced from a panel obtained by press forming.
  • FIG. 2( b ) illustrates flange portions of a panel obtained by press forming using draw forming.
  • FIG. 3( a ) is a graph showing the relationship between the difference in average temperature among flange portions and other portions of a panel obtained by warm press forming using draw forming and the amount of geometric changes made to the panel from the time immediately after press forming (the time when the panel was removed from the die) until the end of air cooling.
  • FIG. 3( b ) is a diagram explaining the amount of geometric changes made to the panel from the time immediately after press forming (the time when the panel was removed from the die) until the end of air cooling.
  • FIG. 4( a ) is a graph showing the relationship between the difference in average temperature among flange portions and other portions of panels, each being obtained by warm press forming using draw forming, and the holding time at press bottom dead point.
  • FIG. 4( b ) is a graph showing the relationship between the amount of geometric changes made to the panels from the time immediately after warm press forming using draw forming (the time when the panels were removed from the die) until the end of air cooling and the holding time at press bottom dead point.
  • FIG. 5( a ) schematically illustrates a center pillar upper press panel.
  • FIG. 5( b ) is a diagram explaining the amount of geometric changes made to the panel from the time immediately after press forming (the time when the panel was removed from the die) until the end of air cooling.
  • Heating Temperature of Steel Sheet 400° C. to 700° C.
  • the heating temperature of the steel sheet is 400° C. to 700° C.
  • the heating temperature of the steel sheet is 400° C. or higher and lower than 650° C.
  • press forming is usually performed using draw forming.
  • draw forming even a warm (or hot) press forming process is generally carried out by a blank holder arranged as shown in FIG. 1 to suppress wrinkles that would occur during the forming process, while applying tension to sidewall portions with edges of the blank being compressed between the blank holder and the upper die.
  • a die is labeled 1
  • a punch is labeled 2
  • a blank holder is labeled 3
  • a heated steel sheet (blank) is labeled 4
  • a press-formed part (panel) after the formation is labeled 5
  • flange portions are labeled 6
  • sidewall portions are labeled 7 .
  • an automobile frame component is often worked to form a closed cross section by joining members having a substantially hat-shaped cross section by spot welding and the like.
  • the edges of the blank compressed as shown in FIG. 2( b ) provide flange portions of the panel after the formation.
  • the flange portions are required to be flat since they are points at which panels are joined together by spot welding and the like. This is the reason why the formation is performed while applying blank holding force to edges of the blank as mentioned above.
  • the edges of the blank are continuously compressed between the blank holder and the upper die from the early stage of the forming process until the completion of the process. Consequently, the heated steel sheet (blank) is subject to a heat transfer from edges of the blank to the die during the press forming process, with the result that the edges of the blank are susceptible to a temperature drop, leading to a large difference in temperature among flange portions and other portions of the panel immediately after the formation.
  • the term “difference in average temperature” means a difference in average temperature immediately after press forming, unless otherwise specified.
  • the phrase “immediately after press forming” refers to a point in time that represents the end of a holding process at a press bottom dead point and the start of air cooling of a panel after being removed from the die.
  • the term “the amount of geometric changes” means a difference (variation) between the geometry of a panel after removal from the die immediately after warm press forming and the geometry of the panel after air cooling.
  • FIG. 3( a ) is a graph showing the relationship between the difference in average temperature among flange portions and other portions of a panel obtained by warm press forming using draw forming and the amount of geometric changes made to the panel from the time immediately after press forming (the time when the panel was removed from the die) until the end of air cooling.
  • a steel sheet of 980 MPa grade was used and the heating temperature thereof was set to be 600° C.
  • the aforementioned amount of geometric changes was determined by an opening amount a, which was measured at the edges of the flanges in relation to a reference panel (a panel removed from the die immediately after press forming), as shown in FIG. 3( b ).
  • a reference panel is labeled 8 (dashed line)
  • an air-cooled panel is labeled 9 (thick solid line)
  • a panel at the press bottom dead point is labeled 10 (thin solid line).
  • the larger the aforementioned difference in average temperature in a panel the larger the amount of geometric changes made to the panel from the time it is removed from the die immediately after press forming until the end of air cooling.
  • the amount of geometric changes becomes greater than 1.0 mm where the difference in average temperature exceeds 150° C., it is important that the difference in average temperature be kept within 150° C., preferably within 100° C., to reduce the amount of geometric changes caused by the temperature difference in the panel.
  • FIG. 4( a ) shows the relationship between the difference in average temperature among flange portions and other portions of those panels having a substantially hat-shaped cross section that were obtained warm press forming using draw forming and the holding time at the press bottom dead point; and FIG. 4( b ) shows the relationship between the amount of geometric changes made to the panels from the time they were removed from the die immediately after press forming until the end of air cooling and the holding time at the press bottom dead point.
  • steel sheets of 980 MPa grade were used and the heating temperatures thereof were 600° C., 650° C., and 700° C., respectively.
  • the difference in average temperature among flange portions and other portions of the panel may be kept within 150° C. and the amount of geometric changes made to the panel may be suppressed to 1.0 mm or less, by setting the holding time at press bottom dead point to one second or more.
  • the difference in average temperature among flange portions and other portions of each panel may be kept within 150° C. and the amount of geometric changes made to each panel may be suppressed to 1.0 mm or less, by setting the holding time at press bottom dead point to three seconds or more.
  • a steel sheet is held at the press bottom dead point for one second to five seconds, and preferably three to five seconds, at the time of press forming using draw forming.
  • the heating temperature of the steel sheet is set to 400° C. to 700° C. and the holding time at press bottom dead point to three seconds or more.
  • the pressing speed is preferably 10 spm to 15 spm (strokes per minute, which represents the number of parts that can be formed in one minute plus any additional time, if applicable, taken to hold parts at the press bottom dead point).
  • flange portions are continuously compressed during formation, which provides the benefit of making the flange portions less prone to wrinkle formation. Further, we hold the steel sheet at the press bottom dead point as described above, which makes it possible to suppress wrinkle formation in flange portions in a more effective manner.
  • heating the steel sheet has the same effect irrespective of the heating method used such as heating in an electric furnace, electrical heating, and rapid heating using far infrared heating.
  • the warm press forming method is applied to a steel sheet having a tensile strength of 440 MPa or more. Further, the warm press forming method may preferably be applied to a steel sheet having a tensile strength of 780 MPa or more, and even 980 MPa or more.
  • the warm press forming method makes it possible to directly make use of the mechanical properties of steel sheets as blanks, thereby allowing a press-formed part obtained by press forming of a steel sheet to have a tensile strength which is not greatly different from, or 80% to 110% of, that of the steel sheet before press forming.
  • Carbon (C) is an important element in that it forms carbides with other elements such as Ti, V, Mo, W, Nb, Zr, and Hf, which exhibit fine particle distribution in the matrix to thereby increase the strength of a steel sheet.
  • the content of C in steel is preferably 0.015 or more.
  • the content of C exceeds 0.16%, the ductility and toughness are significantly reduced, which makes it impossible to ensure good impact absorption ability (such as expressed by “tensile strength TS ⁇ total elongation El”). Therefore, the content of C is preferably 0.015% to 0.16%, more preferably 0.03% to 0.16%, and still more preferably 0.04% to 0.14%.
  • Silicon (Si) is a solid-solution-strengthening element that suppresses the reduction of strength in a high temperature range and, consequently, adversely affects formability in a warm-forming temperature range (warm formability). Therefore, the content of Si in steel is preferably kept as low as possible in the present invention, but a Si content of up to 0.2% is tolerable. In view of this, the content of Si is preferably 0.2% or less, more preferably 0.1% or less, and still more preferably 0.06% or less. Note that the content of Si may be reduced to impurity level.
  • Manganese (Mn) is also a solid-solution-strengthening element, like Si, that suppresses the reduction of strength in a high temperature range and, consequently, adversely affects the formability in a warm-forming temperature range (warm formability). Therefore, the content of Mn in steel is preferably kept as low as possible in the present invention, but a Mn content of up to 1.8% is tolerable. In view of this, the content of Mn is preferably 1.8% or less, more preferably 1.3% or less, and still more preferably 1.1% or less. Note that if the content of Mn is too low, the austenite ( ⁇ ) to ferrite ( ⁇ ) transformation temperature may rise excessively, which could lead to coarsening of carbides. Therefore, the content of Mn is preferably 0.5% or more.
  • Phosphorus (P) is an element that has a very high, solid-solution-strengthening ability, suppresses the reduction of strength in a high temperature range, and consequently adversely affects formability in a warm-forming temperature range (warm formability). Additionally, P exists in a segregated manner at grain boundaries, thereby lowering the ductility during and after warm forming.
  • the content of P in steel is preferably kept as low as possible, but a P content of up to 0.035% is tolerable. Accordingly, the content of P is preferably 0.035% or less, more preferably 0.03% or less, and still more preferably 0.02% or less.
  • S Sulfur
  • S is an element that exists as inclusion in steel. S reduces the strength of the steel sheet when bonded to Ti, while forming sulfides when bonded to Mn, leading to a reduction of the ductility of the steel sheet at room temperature, under warm condition, and the like. Therefore, the content of S is preferably kept as low as possible, but a S content of up to 0.01% is tolerable. Accordingly, the content of S is preferably 0.01% or less, more preferably 0.005% or less, and still more preferably 0.004% or less.
  • Aluminum (Al) is an element that acts as a deoxidizer. To obtain this effect, it is desirable that Al is contained in steel by 0.02% or more. However, if the content of Al exceeds 0.1%, more oxide-based inclusions form, significantly reducing the ductility under warm condition. Therefore, the content of Al is preferably 0.1% or less, and more preferably 0.07% or less.
  • N Nitrogen
  • the content of N is preferably kept as low as possible, but a N content of up to 0.01% is tolerable. Therefore, the content of N is preferably 0.01% or less, and more preferably 0.007% or less.
  • Titanium (Ti) is an element that forms carbides when bonded to C and thereby contributes to increased strength of the steel sheet.
  • the content of Ti is preferably 0.13% or more.
  • the content of Ti is preferably 0.25% or less, more preferably 0.14% to 0.22%, and still more preferably 0.15% to 0.22%.
  • Expression (1) is a requirement to enable the strengthening by precipitation with carbides, which will be described later, and to ensure a high strength as desired after warm forming.
  • Expression (1) it is possible to allow precipitation of a desired amount of carbides, thereby ensuring a high strength as desired.
  • the steel sheet that can preferably be used in the warm press forming method may optionally contain the following elements as appropriate.
  • Vanadium (V), molybdenum (Mo), tungsten (W), niobium (Nb), zirconium (Zr), and hafnium (Hf) are elements, like Ti, that form carbides to contribute to increasing the strength of the steel sheet. Therefore, the steel sheet may contain at least one element in addition to Ti, selected from V, Mo, W, Nb, Zr, and Hf, if a further enhancement of its strength is required.
  • the content of V is 0.01% or more
  • the content of Mo is 0.01% or more
  • the content of W is 0.01% or more
  • the content of Nb is 0.01% or more
  • the content of Zr is 0.01% or more
  • the content of Hf is 0.01% or more.
  • the content of V exceeds 1.0%, carbides are more prone to coarsening; in particular, coarsening of carbides in a warm-forming temperature range makes it difficult to control the average particle size of the carbides after being cooled to room temperature to be 10 nm or less.
  • the content of V is preferably 1.0% or less, more preferably 0.5% or less, and still more preferably 0.2% or less.
  • the contents of Mo and W are more than 0.5% and 1.0%, respectively, the ⁇ -to- ⁇ transformation is exceedingly delayed. As a result, bainite phase and martensite phase exist in a mixed manner in the microstructure of the steel sheet, which makes it difficult to obtain ferrite single phase, which will be described later.
  • the contents of Mo and W are preferably 0.5% or less and 1.0% or less, respectively.
  • Nb, Zr, and Hf are contained in steel by more than 0.1%, respectively, coarse carbides are not completely dissolved and remain in slab being reheated. Consequently, micro voids form more easily during warm forming.
  • the contents of Nb, Zr, and Hf are preferably 0.1% or less, respectively.
  • the steel sheet that can preferably be used in the warm press forming method may optionally contain the following elements as appropriate.
  • Boron (B) is an element that acts to inhibit nucleation of the ⁇ -to- ⁇ transformation to lower the ⁇ -to- ⁇ transformation point, thereby contributing to the refinement of carbides. To obtain this effect, it is desirable that the content of B is 0.0002% or more. However, containing over 0.003% of B does not increase this effect, but is rather economically disadvantageous. Therefore, the content of B is preferably 0.003% or less, and more preferably 0.002% or less.
  • Magnesium (Mg), calcium (Ca), yttrium (Y), and REM all act as refining inclusions, which action provides an effect of suppressing stress concentration in the vicinity of inclusions and the base material during warm forming, and thereby improving the ductility. Therefore, these elements may optionally be contained in steel.
  • the REM which is an abbreviation for Rare Earth Metal, represents lanthanoid elements.
  • Mg, Ca, Y, and REM are contained in steel in an excessive amount over 0.2%, respectively, these elements compromise castability (which is the ability of a molten steel to flow through a mold before solidification; higher castability represents better flowability of a molten steel), rather leading to lower ductility.
  • the content of Mg is 0.2% or less
  • the content of Ca is 0.2% or less
  • the content of Y is 0.2% or less
  • the content of REM is 0.2% or less. More preferably, the content of Mg is 0.001% to 0.1%
  • the content of Ca is 0.001% to 0.1%
  • the content of Y is 0.001% to 0.1%
  • the content of REM is 0.001% to 0.1%.
  • the total amount of these elements is adjusted to be 0.2% or less, and more preferably 0.1% or less.
  • Antimony (Sb), copper (Cu), and tin (Sn) are elements that concentrate near surfaces of a steel sheet and has an effect of suppressing softening of the steel sheet that would be caused by nitriding of the surfaces of the steel sheet during warm forming. Therefore, at least one of these elements may optionally be contained in steel.
  • Cu is also effective to improve anti-corrosion property. To obtain this effect, it is desirable that Sb, Cu, and Sn are contained in steel by 0.005% or more, respectively. However, if Sb, Cu, and Sn are contained in steel in excessive amounts over 0.1%, 0.5%, and 0.1%, respectively, the resulting steel sheet has a poor surface texture. Therefore, it is preferred that the content of Sb is 0.1% or less, the content of Cu is 0.5% or less, and the content of Sn is 0.1% or less.
  • Ni and Cr are elements that contribute to increased strength of steel. At least one of these elements may optionally be contained in steel.
  • Ni is an austenite-stabilizing element that suppresses formation of ferrite at high temperature and contributes to increased strength of the steel sheet.
  • Cr is a quench-hardenability-improving element that suppresses, as is the case with Ni, formation of ferrite at high temperature and contributes to increased strength of the steel sheet.
  • Ni and Cr are contained in steel by 0.01% or more. However, if Ni and Cr are contained in steel in an excessive amount over 0.5%, respectively, formation of a low temperature transformation phase, such as martensite phase and bainite phase, is induced. A low temperature transformation phase, such as martensite phase and bainite phase, shows recovery during heating, thereby causing a reduction in the strength after warm forming. To obtain this effect, it is preferred that Ni and Cr are contained in steel by 0.5% or less, and more preferably by 0.3% or less, respectively.
  • a total amount of 2.0% or less of the above elements is tolerable since it does not affect the strength or warm formability of the steel sheet.
  • the total amount is more preferably 1.0% or less.
  • the balance other than the aforementioned components includes Fe and incidental impurities.
  • the steel sheet has a metal structure of ferrite single phase.
  • ferrite single phase is not only intended to represent a situation where the area ratio of ferrite phase is 100%, but also to encompass a substantially ferrite single phase where the area ratio of ferrite phase is 95% or more.
  • the steel sheet having a ferrite single phase as its metal structure it is possible to retain excellent ductility and even suppress changes to the material properties caused by heating.
  • the coexistence of hard phases such as bainite phase and martensite phase in the microstructure causes recovery of dislocations introduced to the hard phases by heating and, consequently, the hard phases soften, which makes it impossible to maintain the strength of the steel sheet even after warm forming. Accordingly, the absence of pearlite, bainite phase, and martensite phase delivers better results, although the coexistence of such hard phases and even a retained austenite phase is tolerable as long as the area ratio of these phases with respect to the entire microstructure is 5% or less.
  • a steel sheet has a metal structure of substantially ferrite single phase
  • the metal structure remains as substantially ferrite single phase even when the steel sheet is heated to a temperature range of 400° C. to 700° C. (warm-forming temperature range).
  • the aforementioned steel sheet may show an increase in ductility as it is heated, achieving good total elongation in the warm-forming temperature range.
  • the forming process is conducted in connection with recovery of dislocation and, consequently, with little reduction in ductility during warm forming. Furthermore, since the steel sheet does not show any microstructural changes even when cooled to room temperature after warm forming, it maintains the metal structure of substantially ferrite single phase and exhibits excellent ductility.
  • ferrite For ferrite having an average grain size of less than 1 ⁇ M, crystal grains tend to grow during warm forming, with the result that the material properties of a press-formed part after warm forming considerably differ from those observed before warm forming, reducing the stability of the steel sheet as a material. Therefore, ferrite preferably has an average grain size of 1 ⁇ m or more.
  • ferrite if ferrite has an excessively large, average grain size over 15 ⁇ m, it is not possible to achieve strengthening through grain refinement of the microstructure, which makes it difficult to ensure a desired strength of the steel sheet. Therefore, ferrite preferably has an average grain size of 15 ⁇ m or less, and more preferably 12 ⁇ m or less.
  • the finisher delivery temperature is preferably at 840° C. or higher.
  • the strength of the steel sheet may be increased by allowing fine carbides having an average particle size of 10 nm or less to be precipitated in the ferrite crystal grains.
  • the average particle size of the carbides is more than 10 nm, it is difficult to obtain the aforementioned high tensile strength and/or yield ratio.
  • the average particle size of the carbides is more preferably 7 nm or less.
  • Examples of the fine carbides include Ti carbides, and furthermore, V carbides, Mo carbides, W carbides, Nb carbides, Zr carbides, and Hf carbides. These carbides do not undergo coarsening and the average particle size thereof remains 10 nm or less, as long as the heating temperature of the steel sheet is held at 700° C. or lower. The coarsening of the carbides is thus suppressed even when the steel sheet is heated to a warm-forming temperature of 400° C. to 700° C. for warm forming, with the result that the steel sheet will not show a considerable reduction in its strength after cooled to room temperature following the warm forming process.
  • the aforementioned steel sheet may comprise a coating or plating layer such as a hot dip galvanized layer.
  • a coating or plating layer include an electroplated layer, an electroless-plated layer, a hot-dipped layer, and so on.
  • a galvannealed layer may also be used.
  • the steel sheet that can preferably used in the warm press forming method is obtained by heating a steel material, then subjecting the steel material to hot rolling including rough rolling and finish rolling and, subsequently, coiling the steel material to obtain a hot rolled steel sheet.
  • the method of manufacturing a steel raw material preferably includes, without any particular limitation: preparing a molten steel having the aforementioned composition by a well-known steelmaking method such as a converter and an electric furnace; subjecting the molten steel to optional secondary refining in a vacuum degassing furnace; and casting the molten steel to obtain a steel raw material, such as slab, by a well-known casting method such as a continuous casting. Note that the continuous casting is preferred in terms of productivity and quality.
  • Heating Temperature of Steel Raw Material 1100° C. to 1350° C.
  • Coarse carbides fail to be dissolved if the heating temperature of the steel raw material is below 1100° C. and, consequently, fewer fine carbides are dispersed and precipitated in the resulting steel sheet, which makes it difficult to ensure a high strength as desired.
  • the heating temperature of the steel raw material is above 1350° C., oxidation progresses so much as to form oxide scales during hot rolling and to deteriorate the surface texture of the steel sheet, thereby lowering the warm formability of the steel sheet. Therefore, the heating temperature of the steel raw material is preferably 1100° C. to 1350° C. A more preferable range is 1150° C. to 1300° C.
  • the finisher delivery temperature is below 840° C.
  • the microstructure contains extended ferrite grains and ends up with a mixed-grain-size microstructure in which individual ferrite grains are greatly different in grain size, with the result that the strength of the steel sheet significantly decreases.
  • a finisher delivery temperature below 840° C. results in excessive strain energy being stored in the steel sheet during the rolling process, which makes it difficult to obtain a microstructure containing ferrite grains having an average grain size of 1 ⁇ m or more. Therefore, the finisher delivery temperature is preferably 840° C. or higher, and more preferably 860° C. or higher.
  • the resulting hot rolled steel sheet is subjected to forced cooling. If more than three seconds elapse before the forced cooling is initiated after completion of the hot rolling, a large amount of carbides are subject to strain-induced precipitation, which makes it difficult to ensure desired precipitation of fine carbides. Therefore, the forced cooling is preferably initiated within three seconds after completion of the hot rolling, and more preferably within two seconds.
  • the aforementioned forced cooling after the hot rolling is preferably performed at an average cooling rate of 30° C./s or higher to rapidly cool the steel sheet to a predetermined temperature.
  • the average cooling rate is more preferably 50° C./s or higher.
  • a cooling stop temperature is set such that a coiling temperature eventually falls within a target temperature range, taking into account the temperature drop that would occur in the steel sheet during a period from the end of cooling to the start of coiling. That is, since the steel sheet experiences a drop in temperature as it is air cooled after the end of cooling, the cooling stop temperature is normally set to be approximately equal to the temperature of coiling temperature+5° C. to +10° C.
  • Coiling Temperature 500° C. to 700° C.
  • a coiling temperature below 500° C. results in an insufficient amount of carbides being precipitated in the steel sheet for providing the steel sheet with as high strength as desired.
  • a coiling temperature above 700° C. induces coarsening of precipitated carbides, which also makes it difficult to provide the steel sheet with as high strength as desired. Therefore, the coiling temperature is preferably 500° C. to 700° C., and more preferably 550° C. to 680° C.
  • the resulting hot rolled steel sheet may be subjected to a coating or plating process using a well-known method to form a coating or plating layer on its surface.
  • the coating or plating layer is preferably a hot-dip galvanized layer, a galvannealed layer, an electroplated layer, or the like.
  • the preferred steel sheet has the following mechanical properties:
  • the warm press forming method is applied to a steel sheet having a tensile strength at room temperature of 440 MPa or more
  • the aforementioned manufacturing method may be used to obtain a steel sheet having TS 1 of 780 MPa or more and a yield ratio at room temperature of 0.85 or more.
  • TS 1 represents a tensile strength at room temperature and “room temperature” refers to a temperature of (22 ⁇ 5)° C.
  • the deformation resistance of the steel sheet is not sufficiently reduced at the time of warm forming and accordingly increased load (press load) is required for warm forming, leading to a shortened die life.
  • the body size of the processing machine (press machine) must be necessarily increased for applying a large load (press load). As the body size of the processing machine (press machine) increases, it takes a longer time to transfer a steel sheet heated to a warm forming temperature to a processing machine, which causes a temperature drop in the blank and accordingly makes it difficult to perform warm forming at a desired temperature range.
  • shape fixability is not improved sufficiently and, consequently, the effect to be obtained by warm forming is reduced.
  • the yield strength YS 2 in the warm-forming temperature of 400° C. to 700° C. is preferably 80% or less, and more preferably 70% or less of the yield strength YS 1 at room temperature.
  • the total elongation El 2 in the warm-forming temperature of 400° C. to 700° C. is preferably 1.1 times or more, and more preferably 1.2 times or more the total elongation El 1 at room temperature.
  • a steel sheet which exhibits the following mechanical properties in addition to the above after being formed into a press-formed part, may more preferably be used in the warm press forming method.
  • Yield Strength YS 3 at Room Temperature and Total Elongation El 3 at Room Temperature of a Press-Formed Part 80% or More of the Yield Strength YS 1 at Room Temperature and the Total Elongation El 1 at Room Temperature of the Material Steel Sheet Prior to Press Forming
  • the strength and total elongation of the resulting member after warm forming are insufficient. If such a steel sheet is subjected to warm press forming to produce an automobile component of desired shape, the resulting component offers insufficient crash worthiness upon crash of the automobile, resulting in reduced reliability as an automobile component.
  • a press-formed part has a yield strength YS 3 at room temperature and a total elongation El 3 at room temperature that are 80% or more, and more preferably 90% or more of the yield strength YS 1 at room temperature and the total elongation El 1 at room temperature of the material steel sheet prior to press forming.
  • the steel sheets were heated in an electric furnace.
  • the in-furnace time was set to be 300 seconds so that each blank can be heated in the furnace, resulting in a uniform temperature distribution throughout the blank.
  • the heated blanks were then removed from the furnace and fed into a press machine after a transfer time of 10 seconds, respectively, where the blanks were subjected to forming processes with different holding times at the press bottom dead point as shown in Table 1.
  • the temperature difference between flange portions and other portions of each of the formed panels was measured. That is, the temperature was measured in each panel at six points (indicated by “X” in FIG. 5( a )) in flange portions and five points in other portions (indicated by “Y” in FIG. 5( a )) using a contactless thermometer, and the difference between the average temperature of the X points and the average temperature of the Y points was defined as the difference in average temperature among the flange portions and the other portions.
  • a servo press was used as a press machine, where the pressing speed was set to be 15 spm (strokes per minute, which represents the number of parts that can be formed in one minute plus any additional time, if applicable, taken to hold the parts at the press bottom dead point).
  • the formed panels were air cooled for a sufficiently long period of time, after which, regarding the cross sectional shape of each center pillar upper press panel as shown in FIG. 5( b ), measurements were made with a laser displacement sensor of the amount of geometric changes a made to the edges of each panel until the end of air cooling, in relation to the reference panel shape (which is the shape the panel took when it was removed from the die immediately after the press forming process). The measurement results are also shown in Table 1.
  • each of steel Nos. 1, 2, 5 to 9 of our examples in which steel sheets were held at the press bottom dead point for one second or more, yielded good dimensional accuracy such that the difference in average temperature among flange portions and other portions of each press-formed part was kept within 150° C. and the amount of geometric changes a was 1.0 mm or less.
  • the warm press forming method may suppress the difference in average temperature among flange portions and other portions of a panel, and thereby reduce the amount of geometric changes made to the panel from the time immediately after press forming until the end of air cooling, thereby providing the press-formed part with significantly improved dimensional accuracy.
  • Molten steels having the chemical compositions shown in Table 2 were prepared by steelmaking in a converter, and subjected to continuous casting to obtain slabs (steel raw materials).
  • the slabs (steel raw materials) were heated to the heating temperatures shown in Table 3, then subjected to soaking, rough rolling, finish rolling under the hot rolling conditions shown in Table 3, cooling, and subsequent coiling to obtain hot rolled steel sheets (sheet thickness: 1.6 mm).
  • sheet thickness 1.6 mm. Note that each of the steel sheets a, i, k, m was heated to 700° C. in a continuous galvanizing line and immersed in a hot-dip galvanizing bath at a liquid temperature of 460° C.
  • the coating weight was set to be 45 g/m 2 for each steel sheet.
  • test pieces were collected from the hot rolled steel sheets thus obtained and analyzed by microstructure observation, precipitation observation, and tensile tests. The analysis was carried out as follows.
  • Test pieces were collected from the obtained hot rolled steel sheets for microstructure observation. Each test piece was polished and etched (etching solution: 5% nital solution) at its cross section parallel to the rolling direction (L-section), and then its center part in the sheet thickness direction was observed and imaged in ten fields of view under a scanning electron microscope (at magnification of ⁇ 400). The micrographs thus obtained were analyzed using an image processing technique to identify the microstructure and to measure the microstructure proportion and the average grain size of each phase.
  • the obtained micrographs were used to distinguish ferrite phase from other phases so as to measure the area of the ferrite phase, thereby determining an area ratio of the ferrite phase to the entire fields of view being observed. While the ferrite phase is observed with smoothly curved grain boundaries with no corrosion marks appeared in the grains, any grain boundaries appeared in linear form were construed as part of the ferrite phase.
  • the obtained micrographs were also used to determine the average grain size of ferrite by a cutting method in conformity with ASTM E 112-10.
  • test pieces were collected from the center portions in the sheet thickness direction of the obtained hot rolled steel sheets, and subjected to mechanical and chemical polish to obtain thin films for observation under a transmission electron microscope (TEM).
  • the thin films thus obtained were observed under a TEM (at magnification of ⁇ 120,000) for precipitates (carbides).
  • Measurements were made of the particle size of 100 or more carbides to determine an arithmetic mean value thereof, which was defined as the average particle size of carbides in each steel sheet. Note that coarse cementite and nitride particles greater than 1 ⁇ m in diameter were excluded from the measurements.
  • JIS No. 13B tensile test pieces were collected from the obtained hot rolled steel sheets with a direction orthogonal to the rolling direction being the tensile direction, in accordance with JIS Z 2201 (1998).
  • the collected test pieces were subjected to tensile tests in accordance with JIS G 0567 (1998) to measure mechanical properties (yield strength YS 1 , tensile strength TS 1 , total elongation El 1 ) at room temperature (22 ⁇ 5° C.) and high-temperature mechanical properties (yield strength YS 2 , tensile strength TS 2 , total elongation El 2 ) at temperatures shown in Table 4.
  • Tables 3 and 4 list the test results (1) to (3).
  • JIS No. 13B tensile test pieces were collected from the formed panels and subjected to tensile tests at room temperature under the same conditions as described above, to measure their mechanical properties (yield stress (YS 3 ), tensile strength (TS 3 ), and total elongation (El 3 )).
  • each of steel Nos. 17 to 42 of our examples yielded good dimensional accuracy such that the difference in average temperature between flange portions and other portions was kept within 150° C. and the amount of geometric changes a was 1.0 mm or less.
  • steel Nos. 17 to 22, 29 to 36, 40, and 41 of our examples using steel sheets having preferred chemical compositions and microstructures yielded good dimensional accuracy in the press-formed parts after the formation, despite the use of high strength steel sheets having a tensile strength of 780 MPa or more, and furthermore, the press-formed parts exhibited extremely good mechanical properties such that, for example, the tensile strength TS 3 of these press-formed parts was 99% to 104% of the tensile strength TS 1 of the respective material steel sheets before press forming.

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