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US20140004378A1 - Steel sheet for hot stamped member and method of production of same - Google Patents

Steel sheet for hot stamped member and method of production of same Download PDF

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Publication number
US20140004378A1
US20140004378A1 US14/004,809 US201214004809A US2014004378A1 US 20140004378 A1 US20140004378 A1 US 20140004378A1 US 201214004809 A US201214004809 A US 201214004809A US 2014004378 A1 US2014004378 A1 US 2014004378A1
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Prior art keywords
steel sheet
hot
inv
hardness
less
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US14/004,809
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English (en)
Inventor
Hiroyuki Tanahashi
Jun Maki
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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Assigned to NIPPON STEEL & SUMITOMO METAL CORPORATION reassignment NIPPON STEEL & SUMITOMO METAL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MAKI, JUN, TANAHASHI, HIROYUKI
Publication of US20140004378A1 publication Critical patent/US20140004378A1/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/1275—Next to Group VIII or IB metal-base component
    • Y10T428/12757—Fe
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the present invention relates to steel sheet for a hot stamped member which is suitable for the hot stamping method, one of the shaping methods giving a high strength member, and a method of production of the same.
  • the hot shaping method As one method for dealing with this situation, the hot shaping method called the “hot stamping method” has come under attention. This heats a steel sheet (worked material) to a predetermined temperature (generally, the temperature resulting in an austenite phase) to lower the strength (that is, facilitate shaping), then shapes it by a die of a lower temperature than the worked material (for example room temperature) to thereby easily impart a shape and simultaneously utilize the temperature between the two for rapid cooling heat treatment (quenching) so as to secure the strength of the shaped product.
  • a predetermined temperature generally, the temperature resulting in an austenite phase
  • the worked material for example room temperature
  • PLT 1 shows steel sheet obtained by controlling the amounts of elements which the steel sheet contains and the relationship among the amounts of the elements to predetermined ranges so as to give a member which is excellent in impart characteristics and delayed fracture characteristic after hot shaping (synonymous with hot stamping).
  • PLT 2 in the same way as the above, discloses a method comprising making the amounts of elements which the steel sheet contains and the relationship among the amounts of the elements to predetermined ranges and heating before shaping the steel sheet in a nitriding atmosphere or a carburizing atmosphere so as to obtain a high strength part.
  • PLT 3 describes means for prescribing the composition and microstructure of steel sheet and limiting the heating conditions and shaping conditions so as to obtain hot pressed parts with a high productivity.
  • steel sheet (product) made high in strength by the hot stamping method also can be expected to exhibit a commensurate fatigue characteristic, if compared with steel sheet of the same strength not using the hot stamping method (high strength steel sheet produced by controlling the composition or method of production of the strength steel sheet, below, called “ordinary high strength steel sheet”), it became clear that depending on the production conditions, the fatigue characteristics of the former were inferior to the latter.
  • PLT 1 discusses steel sheet for hot shaping use where all of Ni, Cu, and Sn are essential, wherein the impact characteristics and the delayed fracture characteristic are improved, but does not allude to the fatigue characteristic or the deviation in surface layer hardness before hot stamping.
  • PLT 2 relates to the art of heating in a carburizing atmosphere so as to raise the strength of a shaped part, but does not allude to the fatigue characteristic or the deviation in surface layer hardness before hot stamping. Heating in a carburizing atmosphere is essential. Compared with heating in the air, the production costs rise. Further, when using carbon monoxide as the source of carbon, there is a concern that tremendous costs would be required for securing the safety of operations. It is believed that this art is not easily workable.
  • PLT 3 also does not allude to the fatigue characteristic and the deviation in surface layer hardness before hot stamping.
  • PLT 4 As opposed to this, as art for obtaining steel sheet for hot stamping use which has a fatigue characteristic of the same extent as “ordinary high strength steel sheet”, there is PLT 4. Further, while as art inherent to the case of use of steel sheet which has been galvanized, PLT 5 is known as art for improving the fatigue characteristic of a member which is produced by the hot stamping method.
  • PLT 4 discloses to make fine particles which contain Ce oxides disperse slight inward from the steel sheet surface so as to improve the fatigue characteristic after hot stamping, but advanced steelmaking art is required, so there is the problem that even a person skilled in the art would not necessarily find it easy to work it.
  • PLT 5 relates to facilities for hot stamping technology. There is the problem that without new capital investment, even a person skilled in the art could not enjoy its benefits.
  • PLT 1 Japanese Patent Publication No. 2005-139485A
  • PLT 2 Japanese Patent Publication No. 2005-200670A
  • PLT 3 Japanese Patent Publication No. 2005-205477A
  • PLT 5 Japanese Patent Publication No. 2007-182608A
  • the present invention in view of the above situation, has as its object the provision of steel sheet for a hot stamped member which enables the production of a product of high strength steel sheet which has an excellent fatigue characteristic of the same extent as high strength steel sheet which is produced by controlling the composition of the steel sheet or method of production (“ordinary high strength steel sheet”) when producing a product by applying the hot stamping method to steel sheet and of a method of production of the same.
  • the inventors engaged in intensive research to solve this problem. As a result, they discovered that making the deviation in hardness near the surface layer of steel sheet before hot stamping within a predetermined range is extremely effective for improving the fatigue characteristic of the steel sheet after hot stamping (product). They discovered that such steel sheet can be obtained by controlling the conditions when recrystallization-annealing the cold rolled steel sheet, conducted repeated tests, and thereby completed the present invention.
  • the gist of the invention is as follows:
  • Steel sheet for a hot stamped member which includes composition which contains, by mass %,
  • a balance of Fe and unavoidable impurities and limit the impurities to P: 0.03% or less, S: 0.02% or less, and N: 0.1% or less, wherein a standard deviation of Vicker's hardness at a position of 20 ⁇ m from the steel sheet surface in the sheet thickness direction is 20 or less.
  • a method of production of steel sheet for a hot stamped member comprising recrystallization-annealing cold rolled steel sheet which includes composition which contains, by mass %,
  • step including a first stage of heating by an average heating rate of 8 to 25° C./sec from room temperature to a temperature M (° C.) and then a second stage of heating by an average heating rate of 1 to 7° C./sec to a temperature S (° C.), wherein the temperature M (° C.) is 600 to 700 (° C.) and the temperature S (° C.) is 720 to 820 (° C.).
  • the steel sheet for a hot stamped member of the present invention can be produced by a known steelmaking facility. Further, a shaped part which is obtained using the steel sheet for a hot stamped member of the present invention for shaping by widespread hot stamping facilities (hot stamped members) has a fatigue characteristic equal to “ordinary high strength steel sheet” of the same strength, so has the effect of expanding the scope of application of hot stamped members (parts).
  • FIG. 1 is perspective view which shows a sheet press die for hot stamping which is used for the examples of the present invention.
  • FIG. 2 is a view which shows fatigue test pieces.
  • FIG. 3 is a perspective view which shows locations of measurement of hardness in a test piece for hardness measurement use of the same dimensions as the crack growth region of the fatigue test piece which is shown in FIG. 2 .
  • FIG. 4 is a graph which shows the correlation between the fatigue limit ratio and standard deviation of hardness before hot stamping of steel sheet for a hot stamped member of Example 1.
  • FIG. 5 is a perspective view which schematically shows steel sheet (member) which is formed into a hat shape by the hot stamping method.
  • FIG. 6 is a graph which shows the correlation between the fatigue limit ratio and standard deviation of hardness before hot stamping of steel sheet for a hot stamped member of Example 2.
  • the inventors engaged in research using steel sheet which contains, by mass %, C: 0.23%, Si: 0.5%, and Mn: 1.6% to prepare a hot stamped member and evaluated its characteristics. They discovered that the fatigue characteristic is one of the same but that there are hot stamped members which are the same in composition of the steel sheet and almost the same in tensile strength, but differ in fatigue characteristic. Therefore, they investigated the differences of these in detail, whereupon they learned that there are differences in the deviation in hardness near the surface layers of hot stamped members.
  • the “%” in the composition mean mass %.
  • C is the most important element in increasing the strength of steel sheet by hot stamping. To obtain a 1200 MPa or so strength after hot stamping, 0.15% or more has to be included. On the other hand, if over 0.35% is included, deterioration of toughness is a concern, so 0.35% is made the upper limit.
  • Si is a solution strengthening element. Up to 1.0% can be effectively utilized. However, if more than that is included, trouble is liable to occur at the time of chemical treatment or coating after shaping, so 1.0% is made the upper limit.
  • the lower limit is not particularly limited. The effect of the present invention can be obtained. However, reduction more than necessary just raises the steelmaking load, so the content is made the level of inclusion due to deoxidation, that is, 0.01% or more.
  • Mn is an element which functions as a solution strengthening element in the same way as Si and also is effective for raising the hardenability of steel sheet. This effect is recognized at 0.3% or more. However, even if over 2.3% is included, the effect becomes saturated, so 2.0% is made the upper limit.
  • the two elements are both unavoidable impurities. They affect the hot workability, so have to be limited to the above ranges.
  • Al is suitable as a deoxidizing element, so 0.01% or more should be included. However, if included in a large amount, coarse oxides are formed and the mechanical properties of the steel sheet are impaired, so the upper limit is made 0.5%.
  • N is an unavoidable impurity. It easily bonds with Ti or B, so has to be controlled so as not to reduce the targeted effect of these elements. 0.1% or less is allowable. The content is preferably 0.01% or less. On the other hand, reduction more than necessary places a massive load on the production process, so 0.0010% should be made the target for the lower limit.
  • Cr has the effect of raising the hardenability, so can be suitably used. This effect becomes clear at 0.01% or more. On the other hand, even if over 2.0% is added, this effect becomes saturated, so 2.0% is made the upper limit.
  • Ti is an element which acts to stably draw out the effect of B, explained later, through the formation of its nitride, so can be effectively used. For this reason, 0.001% or more has to be added, but if excessively added, the nitrides become excessive and deterioration in toughness or shear surface properties is invited, so 0.5% is made the upper limit.
  • Nb is an element which forms carbonitrides and raises the strength, so can be effectively used. This effect is recognized at 0.001% or more, but if over 0.5% is included, the controllability of the hot rolling is liable to be impaired, so 0.5% is made the upper limit.
  • B is an element which raises the hardenability. The effect becomes clear at 0.0005% or more. On the other hand, excessive addition leads to deterioration of hot workability and a drop in the ductility, so 0.01% is made the upper limit.
  • Cu has the effect of raising the strength of the steel sheet by addition of Cu in 0.01% or more. However, excessive addition detracts from the surface quality of the hot rolled steel sheet, so 1.0% is made the upper limit.
  • Ni is an element which has the effect of raising the hardenability, so can be effectively used. The effect becomes clear at 0.01% or more. On the other hand, it is an expensive element, so 5.0% where the effect becomes saturated is made the upper limit. Further, it also acts to suppress the drop in the surface quality of the hot rolled steel sheet due to Cu, so inclusion simultaneously with Cu is desirable.
  • composition other than the above consist of Fe, but unavoidable impurities which enter from the scrap and other melting materials or the refractories etc. are allowed.
  • the hardness of the steel sheet surface ideally should be measured by a hardness meter (for example Vicker's hardness meter) with the steel sheet surface facing upward and with the sheet thickness direction matched with the vertical direction, but to clearly determine indentations (measure dimensions of indentations precisely), the surface (measurement surface) has to be polished or other certain work is necessary. In such work (for example, mechanical polishing), at least several dozen ⁇ m or so are removed from the original surface. Further, even if removing part of the surface using an acid etc. to chemically polish it, there is no difference. Rather, the smoothness is often degraded. Therefore, using such a technique to determine (measure) the hardness of the steel sheet surface is not practical.
  • a hardness meter for example Vicker's hardness meter
  • the inventors decided to determine the hardness at a cross-section parallel to the sheet thickness direction of the steel sheet. By doing so, the steel sheet surface can be measured without working it (without removing the steel sheet surface). However, in this case as well, the position able to be measured by a hardness meter in this way is inside from the surface a slight amount in the sheet thickness direction. For this reason, as a next best solution, the inventors attempted to obtain information on a portion close to the surface by making an indentation by as low a load as possible.
  • the measurement surface (steel sheet cross-section) was polished to a mirror finish.
  • a Vicker's hardness meter was used with a test load (load pushing in indenter) of 10 gf, a pushing time of 15 seconds, and a measurement position in the sheet thickness direction of 20 ⁇ m from the steel sheet surface.
  • the “hardness of the steel sheet” as used in the Description indicates the hardness determined based on the above technique.
  • the hardness of the steel sheet surface in steel sheet which has as a surface layer of the steel sheet either an Al plating layer, galvanized layer, and Zn—Fe alloy layer was measured at a position 20 ⁇ m from the boundary (interface) between the plating layer and the steel sheet.
  • the Al plating layer of the steel sheet which is used in the examples is deemed to be comprised of an outside layer which has Al as its main composition and an inside (steel sheet side) layer which is believed to be a reaction layer of Al and Fe, so the hardness was measured at a position 20 ⁇ m from the boundary of the inside layer and the steel sheet in the sheet thickness direction and this was used as the surface hardness of the steel sheet.
  • the galvanized layer of the steel sheet which is used in the examples is deemed to be comprised of two layers of an outside layer which has Zn as its main composition and an inside layer which is a reaction layer of Al which was added in a fine amount in the Zn bath and Fe, so the hardness was measured at a position 20 ⁇ m from the boundary of the inside layer and the steel sheet in the sheet thickness direction and this was used as the surface hardness of the steel sheet.
  • the Zn—Fe alloy layer of the steel sheet which is used in the examples is deemed to be comprised of a plurality of alloy layers which are comprised of Zn and Fe, so the hardness was measured at a position 20 ⁇ m from the boundary of the inside-most layer and the steel sheet in the sheet thickness direction and this was used as the surface hardness of the steel sheet.
  • FIG. 3 is a perspective view which shows the location of measurement of the hardness.
  • the indenter of the Vicker's hardness meter was pushed in at a position of 20 ⁇ m from the surface or the steel sheet or the interface of the steel sheet and the plating layer in the sheet thickness direction.
  • This operation was performed at indentation intervals of 0.1 mm in a direction parallel to the surface of the steel sheet at 300 points per measurement sample (over 30 mm by measurement length) (first measurement surface). Further, the same operation was performed at another location 5 mm from the first measurement surface taken in advance (second measurement surface).
  • the standard deviation of the Vicker's hardness at a position 20 ⁇ m from the steel sheet surface in the sheet thickness direction was defined as 20 or less based on such experimental findings.
  • the steel sheet for a hot stamped member of the present invention is processed in the accordance with the usual methods by the steps of steelmaking, casting, hot rolling, pickling, and cold rolling to obtain cold rolled steel sheet.
  • the composition is adjusted to the above-mentioned scope of the present invention in the steelmaking step, the steel is cast to a slab in the continuous casting step, then the slab is started to be hot rolled at for example a 1300° C. or less heating temperature.
  • the rolling is ended around 900° C.
  • the coiling temperature can be selected as, for example 600° C. etc.
  • the hot rolling rate may be made 60 to 90%.
  • the cold rolling is performed after the pickling step.
  • the rolling rate can be selected from 30 to 90% in range.
  • the annealing step for recrystallizing the cold rolled steel sheet which was produced in this way is extremely important.
  • the annealing step is performed using a continuous annealing facility and is comprised of two stages of a first step of heating by an average heating rate of 8 to 25° C./sec from room temperature to the temperature M (° C.) and a second stage of then heating by an average heating rate of 1 to 7° C./sec down to a temperature S (° C.).
  • the temperature M has to be 600 to 700(° C.)
  • the temperature S has to be 720 to 820(° C.).
  • recrystallization process of cold rolled steel sheet is complicated, so it is not suitable to separate and independently discuss the meanings of the heating rate for the phenomenon called recrystallization and the highest heating temperature at that heating rate.
  • the heating rate is small and where it is large with respect to a certain single temperature M (° C.). It is believed that in the former case, that is, when the heating rate is small, the density of recrystallization nuclei is (relatively) low and the individual recrystallized grains freely grow, but in the high temperature region near M (° C.), fine recrystallized grains are produced from the remaining non-recrystallization region and, at the stage where the temperature of the steel sheet reaches M (° C.), (relatively) large crystal grains and small crystal grains are mixed.
  • the heating rate of the second stage has to be made smaller than the first stage. Further, in the temperature region from the temperature M (° C.) to the temperature S (° C.), reformation of carbides due to the diffusion of carbon becomes active, so the combination of the setting of the highest temperature S (° C.) of the annealing step and the heating rate up to that temperature has important meaning.
  • the small carbides grow preferentially and it may be that a steel sheet results in which relatively uniform dimension carbides are dispersed at a suitable density, so the unevenness of hardness of the steel sheet due to carbides becomes uneven.
  • the 1 to 7° C./sec of the heating rate of the second stage and the 720 to 820° C. of the temperature S correspond to such suitable conditions.
  • the temperature S After reaching the temperature S, the temperature S may be held for a short time or the next cooling step may be immediately shifted to.
  • the holding time is preferably 180 seconds or less, more preferably 120 seconds or less.
  • the cooling rate from the temperature S in the cooling step is not particularly limited, but 30° C./sec or more rapid cooling is preferably avoided. Therefore, the cooling rate from the temperature S is less than 30° C./sec, preferably 20° C. or less, more preferably 10° C. or less.
  • Steel sheet for hot stamping use is often sheared to a predetermined shape and then used for hot stamping. This is because it is feared that rapid cooling raises the shear load and lowers the production efficiency.
  • the sheet After annealing, the sheet may be cooled down to room temperature. During cooling, it may be dipped in a hot dip Al bath to form an Al plating layer.
  • the hot dip Al bath may contain 0.1 to 20% of Si.
  • the Si which is contained in the Al plating layer affects the reaction of Al and Fe which occurs during heating before hot stamping. Excessive reaction is liable to detract from the press formability of the plating layer itself. On the other hand, excessive control of the reaction is liable to invite adherence of Al on the press forming die. To avoid such a problem, the content of Si in the Al plating layer is preferably 1 to 15%, more preferably 3 to 12%.
  • the sheet was dipped in a hot dip galvanization bath to form a galvanized layer.
  • the sheet was dipped in a hot dip galvanization bath to form a galvanized layer, then was heated to 600° C. or less to form a Zn—Fe alloy layer.
  • the hot dip galvanization bath could contain 0.01 to 3% of Al.
  • a Zn—Fe alloy layer is comprised of a Zn-rich alloy layer ( ⁇ -phase, ⁇ 1 -phase) and Fe-rich alloy layer ( ⁇ 1 -phase, ⁇ -phase), but the former is rich in adhesion with the base iron, but the workability is degraded, while the latter is excellent in workability, but is insufficient in adhesion.
  • the thicknesses of the Al plating layer, galvanized layer, and Zn—Fe alloy layer do not influence the fatigue characteristic of the steel sheet after hot stamping or the fatigue characteristic of the parts, but if excessively thick, the press formability is liable to be affected.
  • the thickness of the Al plating layer is over 50 ⁇ m, the phenomenon of galling is recognized.
  • the thickness of the Zn plating layer exceeds 30 ⁇ m, adhesion of the Zn to the die frequently occurs.
  • the thickness of the Zn—Fe alloy layer is over 45 ⁇ m, scattered cracking of the alloy layer is seen, and the productivity is otherwise impaired. Therefore, the thicknesses of the layers are preferably made Al plating layer: 50 ⁇ m or less, galvanized layer: 30 ⁇ m or less, and Zn—Fe alloy layer: 45 ⁇ m or less.
  • the lower limits of the plating layers are preferably made as follows: That is, the limits are the Al plating layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more, the galvanized layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more, and the Zn—Fe alloy layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more.
  • the cold rolled steel sheets were recrystallized and annealed under the conditions of i to xviii described in Table 2 to obtain the steel sheets for hot stamped members 1 to 32 which are shown in Table 3. From part, two test pieces for measurement of the hardness before hot stamping were obtained. The positions for sampling the test pieces were made positions 5 mm separated in the width direction of the obtained steel sheet for hot stamped member.
  • the average heating rate 1 (first stage) and average heating rate 2 (second stage) in Table 2 respectively show the average heating rates from room temperature to temperature M (° C.) and the average heating rate from temperature M (° C.) to the temperature S (° C.).
  • a tensile test was performed to find the tensile strength ⁇ B (average value of two tensile test pieces). On the other hand, 18 test pieces were used to run a plane bending fatigue test and determine the 1 ⁇ 10 7 cycle fatigue strength ⁇ W .
  • the test conditions were a stress ratio of ⁇ 1 and a repetition rate of 5 Hz.
  • test pieces for measurement of hardness were polished to a mirror finish at cross-sections parallel to the rolling directions of cold rolled steel sheets both before and after hot stamping.
  • the hardness at 20 ⁇ m inside from the surfaces of these test pieces in the sheet thickness direction was measured using a Vicker's hardness meter (HM-2000 made by Mitsutoyo).
  • the pushing load was made 10 gf
  • the pushing time was made 15 seconds
  • the measurement interval in the direction parallel to the surface made 0.1 mm for measurement of 300 points.
  • Table 3 shows the steel number, processing conditions, standard deviation of hardness before hot stamping, tensile strength ⁇ B (average of two), strength ⁇ W , fatigue limit ratio ⁇ W / ⁇ B , and standard of hardness after hot stamping.
  • the correlation between the fatigue limit ratio ⁇ W / ⁇ B and the standard deviation of hardness before hot stamping is shown in FIG. 4 .
  • xvi 20 650 7 820 No holding. Cooling Inv. ex. by average cooling rate 6° C./sec to 670° C., holding for 10 seconds, then air cooling to room temperature.
  • xvii 20 650 8 820 No holding. Cooling Comp. ex. by average cooling rate 6° C./sec to 670° C., holding for 10 seconds, then air cooling to room temperature.
  • FIGURES indicate outside scope of present invention.
  • test pieces for measurement of hardness were obtained by the same procedure was in Example 1.
  • test pieces were used by the same procedure as in Example 1 to find the standard deviation of hardness before hot stamping and the tensile strength ⁇ B (average of two) and 1 ⁇ 10 7 cycle fatigue strength ⁇ W of the steel sheet after hot stamping (member).
  • the deviation in hardness of the surface layer before hot stamping has a standard deviation of over 20.
  • the fatigue limit ratio of the hot stamped members obtained by using these was 0.26 to 0.31. It became clear the fatigue characteristic was inferior.
  • FIGURES indicate outside scope of present invention.
  • These steel sheets were heated by an average heating rate of 19° C./sec up to 655° C., then were heated by an average heating rate of 2.5° C. to 800° C., then were immediately cooled by an average cooling rate of 6.5° C./sec. Further, they were dipped in a 670° C. hot dip Al bath (containing 10% of Si and unavoidable impurities), taken out after 5 seconds, adjusted in amount of deposition by a gas wiper, then air cooled down to room temperature.
  • a 670° C. hot dip Al bath containing 10% of Si and unavoidable impurities
  • Example 2 From the obtained steel sheets, the same procedure as in Example 1 was used to obtain test pieces for measurement of hardness. To measure the hardness, the hardness at a position 20 ⁇ m from the boundary of the inside layer of the Al plating layer (reaction layer of Al and Fe) and the steel sheet was measured by the same procedure as in Example 1. At the time of this measurement, the thickness of the Al plating layer (total of two layers) was also measured. The range of measurement of thickness was made the same length 30 mm as the range of measurement of hardness. Seven points were measured at measurement intervals of 5 mm at each of the first measurement surface and second measurement surface for a total of 14 measurement positions. The average value was found.
  • These steel sheets were heated by an average heating rate of 19° C./sec up to 655° C., then were heated by an average heating rate of 2.5° C. to 800° C., then were immediately cooled by an average cooling rate of 6.5° C./sec. Further, they were dipped in a 460° C. hot dip galvanization bath (containing 0.15% of Al and unavoidable impurities), taken out after 3 seconds, adjusted in amount of deposition by a gas wiper, then air cooled down to room temperature.
  • a 460° C. hot dip galvanization bath containing 0.15% of Al and unavoidable impurities
  • Example 2 From the obtained steel sheets, the same procedure as in Example 1 was used to obtain test pieces for measurement of hardness. To measure the hardness, the hardness at a position 20 ⁇ m from the boundary of the inside layer of the Zn plating layer (reaction layer of Al and Fe) and the steel sheet was measured by the same procedure as in Example 1. At the time of this measurement, the thickness of only the Zn plating layer may also be measured. The range of measurement of thickness was made the same length 30 mm as the range of measurement of hardness. Seven points were measured at measurement intervals of 5 mm at each of the first measurement surface and second measurement surface for a total of 14 measurement positions. The average value was found.
  • the hardness at a position 20 ⁇ m from the boundary of the inside layer of the Zn plating layer (reaction layer of Al and Fe) and the steel sheet was measured by the same procedure as in Example 1. At the time of this measurement, the thickness of only the Zn plating layer may also be measured. The range of measurement of thickness was made the same length 30 mm as the range of
  • FIGURES indicate outside scope of present invention.
  • These steel sheets were heated by an average heating rate of 19° C./sec up to 655° C., then were heated by an average heating rate of 2.5° C. to 800° C., then were immediately cooled by an average cooling rate of 6.5° C./sec. Further, they were dipped in a 460° C. hot dip galvanization bath (containing 0.13% of Al, 0.03% of Fe, and unavoidable impurities), taken out after 3 seconds, adjusted in amount of deposition by a gas wiper, then heated to 480° C. to form an Zn—Fe alloy layer, then air cooled down to room temperature.
  • a 460° C. hot dip galvanization bath containing 0.13% of Al, 0.03% of Fe, and unavoidable impurities
  • Example 2 From the obtained steel sheets, the same procedure as in Example 1 was used to obtain test pieces for measurement of hardness. To measure the hardness, the hardness at a position 20 ⁇ m from the boundary of the inner-most layer of the Zn—Fe alloy layer (reaction layer of Zn and Fe) and the steel sheet was measured by the same procedure as in Example 1. At the time of this measurement, the total thickness of the Zn—Fe alloy layer (which was comprised of four layers) was also measured. At the time of this measurement, the thickness of the Al plating layer (total of two layers) was also measured. The range of measurement of thickness was made the same length 30 mm as the range of measurement of hardness. Seven points were measured at measurement intervals of 5 mm at each of the first measurement surface and second measurement surface for a total of 14 measurement positions. The average value was found.

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WO2012128225A1 (ja) 2012-09-27
EP2687620A1 (en) 2014-01-22
JP5605503B2 (ja) 2014-10-15
CA2829327A1 (en) 2012-09-27
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RU2013146540A (ru) 2015-04-27
CA2829327C (en) 2017-02-14
JPWO2012128225A1 (ja) 2014-07-24
CN103443317A (zh) 2013-12-11
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KR20130126714A (ko) 2013-11-20
BR112013023792A2 (pt) 2016-12-06

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