WO2012128225A1 - ホットスタンプ部材用鋼板およびその製造方法 - Google Patents

ホットスタンプ部材用鋼板およびその製造方法 Download PDF

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WO2012128225A1
WO2012128225A1 PCT/JP2012/056917 JP2012056917W WO2012128225A1 WO 2012128225 A1 WO2012128225 A1 WO 2012128225A1 JP 2012056917 W JP2012056917 W JP 2012056917W WO 2012128225 A1 WO2012128225 A1 WO 2012128225A1
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Prior art keywords
steel sheet
hot
steel
hardness
less
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PCT/JP2012/056917
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English (en)
French (fr)
Japanese (ja)
Inventor
棚橋　浩之
真木　純
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新日本製鐵株式会社
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Application filed by 新日本製鐵株式会社 filed Critical 新日本製鐵株式会社
Priority to KR1020137024832A priority Critical patent/KR20130126714A/ko
Priority to BR112013023792A priority patent/BR112013023792A2/pt
Priority to CN2012800138006A priority patent/CN103443317A/zh
Priority to JP2013505953A priority patent/JP5605503B2/ja
Priority to EP12760551.7A priority patent/EP2687620A4/de
Priority to CA2829327A priority patent/CA2829327C/en
Priority to RU2013146540/02A priority patent/RU2560890C2/ru
Priority to MX2013010601A priority patent/MX360240B/es
Priority to US14/004,809 priority patent/US20140004378A1/en
Publication of WO2012128225A1 publication Critical patent/WO2012128225A1/ja
Priority to ZA2013/07377A priority patent/ZA201307377B/en

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    • 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
    • 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
    • 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 a steel sheet for a hot stamp member suitable for a hot stamp method, which is one of forming methods for obtaining a high-strength member, and a manufacturing method thereof.
  • a hot forming method called a hot stamp method has attracted attention. This is because the steel sheet (work material) is heated to a predetermined temperature (generally the temperature at which it becomes an austenite phase) to lower the strength (that is, to facilitate forming), and then at a lower temperature than the work material.
  • a predetermined temperature generally the temperature at which it becomes an austenite phase
  • the strength that is, to facilitate forming
  • a lower temperature than the work material By molding with a mold (for example, room temperature), the shape is easily imparted, and at the same time, a rapid heat treatment (quenching) utilizing the temperature difference between the two is performed to ensure the strength of the product after molding. .
  • Patent Document 1 has excellent impact characteristics and delayed fracture characteristics after hot forming (synonymous with hot stamping) by setting the relationship between the amount of elements contained in the steel sheet and the amount of elements within a predetermined range. A steel plate from which a member can be obtained is shown.
  • Patent Document 2 as described above, the amount of elements contained in a steel sheet and the relationship between the amounts of elements are set within a predetermined range, and heating before forming the steel sheet is performed in a nitriding atmosphere or a carburizing atmosphere. A method for obtaining a strength component is disclosed.
  • Patent Document 3 describes means for obtaining a hot-pressed product with high productivity by defining the chemical composition and microstructure of a steel sheet and limiting the heating and forming conditions.
  • an undercarriage part of an automobile includes not only a strength as a part but also a fatigue characteristic that is one of important important characteristics.
  • Patent Document 1 describes a steel sheet that requires any one of Ni, Cu, and Sn and has improved impact characteristics and delayed fracture characteristics. There is no mention of the surface hardness variation.
  • Patent Document 2 relates to a technique for increasing the strength of a molded product by performing heating in a carburizing atmosphere, but does not mention fatigue characteristics and variations in surface hardness before hot stamping. Heating in a carburizing atmosphere is essential, resulting in higher manufacturing costs than atmospheric heating, and when carbon monoxide is used as the carbon source, a large amount of money is required to ensure operational safety. There are also concerns about this, and it is unlikely that the technology can be easily implemented.
  • Patent Document 3 there is no mention of fatigue characteristics and surface hardness variation before hot stamping.
  • Patent Document 4 As a technique for obtaining a steel sheet for hot stamping having the same fatigue properties as “ordinary high-strength steel sheet”, there is Patent Document 4, and when using a steel sheet to which Zn plating is applied. Although it is a peculiar technique, patent document 5 is known as a technique which improves the fatigue characteristic of the member manufactured by the hot stamp method.
  • Patent Document 4 discloses a technique for improving fatigue characteristics after hot stamping by dispersing fine particles containing Ce oxide slightly inward from the steel sheet surface, but requires advanced steelmaking techniques. Therefore, even a person skilled in the art has a problem that implementation is not always easy.
  • Patent Document 5 relates to equipment for hot stamping technology, and there is a problem that even those skilled in the art cannot enjoy the benefits without new equipment investment.
  • a hot stamping steel plate for a steel plate (product) that has been strengthened by the hot stamping method, which can relatively easily ensure the same level of fatigue properties as the “normal high strength steel plate” with the same strength.
  • the present invention is a high-strength steel sheet manufactured by controlling the chemical composition of the steel sheet and the manufacturing method when a product is manufactured by applying the hot stamp method to the steel sheet ("normal high-strength steel sheet"). It is an object of the present invention to provide a steel sheet for a hot stamp member, which can be a product of a high-strength steel sheet having excellent fatigue characteristics similar to that of
  • the inventors of the present invention have made extensive studies to solve these problems. As a result, it was found that if the variation in hardness in the vicinity of the steel sheet surface layer before hot stamping is within a predetermined range, it is extremely effective in improving the fatigue characteristics of the steel plate (product) after hot stamping. It was also found that obtaining such a steel sheet can be achieved by controlling the conditions for recrystallization annealing of the cold-rolled steel sheet, and further trials were repeated to complete the present invention.
  • the gist of the invention is as follows.
  • the surface of the steel sheet has either an Al plating layer having a thickness of 5 ⁇ m to 50 ⁇ m, a Zn plating layer having a thickness of 5 ⁇ m to 30 ⁇ m, or a Zn—Fe alloy layer having a thickness of 5 ⁇ m to 45 ⁇ m.
  • the steel is further mass%, Cr: 0.01 to 2.0%, Ti: 0.001 to 0.5%, Nb: 0.001 to 0.5% B: 0.0005 to 0.01%, Mo: 0.01 to 1.0% W: 0.01-0.5% V: 0.01 to 0.5% Cu: 0.01 to 1.0% and Ni: 0.01 to 5.0%
  • the method for producing a steel sheet for a hot stamp member according to (4) comprising one or more selected from:
  • the hot rolling rate in the hot rolling step is 60 to 90%, and the cold rolling rate in the cold rolling step is 30 to 90% (4) or (5) The manufacturing method of the steel plate for hot stamp members as described in).
  • the steel sheet is immersed in a Zn bath to form a Zn plating layer on the surface, and further heated to 600 ° C. or less to form a Zn—Fe alloy layer on the surface.
  • the steel sheet for a hot stamp member of the present invention can be manufactured by an existing steel manufacturing facility, and a molded product obtained by forming a hot stamp facility using the steel sheet for a hot stamp member of the present invention (hot product) Since the fatigue characteristics of the stamp member) are also equivalent to the “normal high-strength steel plate” having the same strength, it has the effect of expanding the application range of the hot stamp member (parts).
  • the inventors of the present invention manufactured a hot stamp member using a steel plate containing C: 0.23%, Si: 0.5%, and Mn: 1.6% by mass%, and evaluated the characteristics. I was doing research. Fatigue properties are one of them, but in the process, it was found that there are hot stamp members with different fatigue properties even though the chemical composition of the steel sheet is the same and the tensile strength is almost the same. Then, when the difference was investigated in detail, it was found that there was a difference in the hardness variation in the vicinity of the surface layer of the hot stamp member.
  • % for a component means mass%.
  • C is the most important element for increasing the strength of a steel sheet by the hot stamp method. In order to obtain a strength of at least about 1200 MPa after hot stamping, it is necessary to contain 0.15% or more. On the other hand, if the content exceeds 0.35%, the upper limit is 0.35%, at which deterioration of toughness is a concern.
  • Si is a solid solution strengthening element and can be effectively used up to 1.0%.
  • the lower limit is not particularly limited, and the effects of the present invention can be obtained.
  • reducing it more than necessary only increases the steelmaking load, so it is set to 0.01% or more, which is a guideline for inclusion due to deoxidation.
  • Mn functions as a solid solution strengthening element like Si, and is a useful element that enhances the hardenability of the steel sheet, and the effect is recognized at 0.3% or more. However, even if the content exceeds 2.3%, the effect is saturated, so 2.0% is made the upper limit.
  • Al is suitable as a deoxidizing element, it may be contained in an amount of 0.01% or more. However, if it is contained in a large amount, a coarse oxide is formed and the mechanical properties of the steel sheet are impaired, so the upper limit is made 0.5%.
  • N is an unavoidable impurity, and since it is easily bonded to Ti and B, it is necessary to control so as not to reduce the intended effect of these elements. Desirably, it is 0.01% or less. On the other hand, reducing it more than necessary places a great load on the steelmaking process, so 0.0010% may be used as a lower limit guide.
  • ⁇ Cr 0.01 to 2.0%> Cr can be used as appropriate because it has the effect of improving hardenability. It is 0.01% or more that the effect becomes clear. On the other hand, even if added over 2.0%, the effect is saturated, so 2.0% is made the upper limit.
  • Ti is an element that can be effectively used because it functions to stably extract the effect of B described later through formation of the nitride. For that purpose, addition of 0.001% or more is necessary, but if it is added excessively, the nitride becomes excessive, leading to deterioration of toughness and shear surface properties, so 0.5% is made the upper limit.
  • Nb is an element that can be used effectively because it forms carbonitrides and increases strength. The effect is recognized at 0.001% or more, but if it exceeds 0.5%, the controllability of hot rolling may be impaired, so 0.5% is made the upper limit.
  • ⁇ B 0.0005 to 0.01%> B is an element that enhances hardenability, and the effect becomes clear at 0.0005% or more.
  • 0.01% is made the upper limit.
  • ⁇ Mo 0.01 to 1.0%>
  • ⁇ W 0.01 to 0.5%>
  • ⁇ V 0.01 to 0.5%>
  • Any of these elements can be used as appropriate because they have the effect of improving the hardenability. The effect becomes clear in all cases of 0.01% or more.
  • Cu has the effect of increasing the strength of the steel sheet by adding 0.01% or more of Cu. However, excessive addition impairs the surface quality of the hot rolled steel sheet, so 1.0% is made the upper limit.
  • Ni is an element that can be effectively used because it has an effect of improving hardenability, and the effect becomes clear at 0.01% or more.
  • the upper limit is 5.0% at which the effect is saturated.
  • it since it also has a function which suppresses the fall of the surface quality of the hot rolled steel sheet by said Cu, it is desirable to make it contain simultaneously with Cu.
  • components other than those described above are Fe, but inevitable impurities mixed from melting raw materials such as scrap or refractories are allowed.
  • the hardness of the steel sheet surface should ideally be measured with a hardness meter (for example, a Vickers hardness meter) with the steel sheet surface as the top surface and the thickness direction aligned with the vertical direction, but the indentation is clearly recognized.
  • a certain process such as polishing the surface (measurement surface) is required.
  • polishing the surface for example, mechanical polishing
  • at least about several tens of ⁇ m is removed from the original surface.
  • even if chemically polished with an acid or the like it is still removed, and the flatness often deteriorates on the contrary. Therefore, it is not realistic to determine (measure) the hardness of the steel sheet surface by such a method.
  • the inventors decided to determine the hardness on a cross section parallel to the thickness direction of the steel sheet. In this way, the surface of the steel sheet can be measured without being processed (without being removed). However, even in this case, the position that can be measured by the hardness meter as described above is slightly inside from the surface in the thickness direction. For this reason, as a second best measure, information on a part closer to the surface was obtained by making an indentation with a load as low as possible.
  • the measurement surface (steel plate cross section) was polished into a mirror surface.
  • the test load (load for pressing the indenter) was 10 gf
  • the pressing time was 15 seconds
  • the measurement position in the plate thickness direction was 20 ⁇ m from the surface of the steel plate.
  • the “hardness of the steel sheet surface” used in this specification refers to a value determined based on the above method.
  • the hardness of the steel sheet surface in the steel sheet having any one of the Al plating layer, the Zn plating layer, and the Zn—Fe alloy layer as the surface layer of the steel sheet is 20 ⁇ m from the boundary (interface) between the plating layer and the steel sheet. It was measured.
  • the Al plating layer of the steel plate used in the examples may be composed of two layers: an outer layer mainly composed of Al and an inner (steel plate side) layer that is considered to be a reaction layer of Al and Fe. Since it was recognized, the hardness was measured at a position of 20 ⁇ m in the thickness direction from the boundary between the inner layer and the steel plate, and this was defined as the surface hardness of the steel plate.
  • the Zn plating layer of the steel plate used in the examples is composed of an outer layer mainly composed of Zn, an inner layer that is a reaction layer of Fe and Al added in a trace amount in the Zn bath. Since it was confirmed to be composed of layers, the hardness was measured at a position of 20 ⁇ m in the thickness direction from the boundary between the inner layer and the steel plate, and this was defined as the surface hardness of the steel plate.
  • the Zn—Fe alloy layer of the steel sheet used in the examples was composed of a plurality of alloy layers composed of Zn and Fe, the plate thickness from the boundary between the innermost layer and the steel sheet was confirmed.
  • the hardness was measured at a position of 20 ⁇ m in the direction, and this was defined as the surface hardness of the steel sheet.
  • FIG. 3 is a perspective view showing a location where the hardness is measured.
  • the indenter of the Vickers hardness meter was pushed in at a position of 20 ⁇ m in the thickness direction from the surface of the steel plate or the interface between the steel plate and the plating layer. As shown in FIG. 3, this operation was performed at 300 points (measured length of 30 mm) per measurement sample in the direction parallel to the surface of the steel sheet with an indentation interval of 0.1 mm (first measurement). surface). Further, the same operation was performed on another location (second measurement surface) 5 mm away from the first measurement surface collected in advance.
  • the hardness was obtained for a total of 600 points, and the standard deviation was calculated using this as a population, and used as an indicator of variation.
  • the above-described measurement lengths of 30 mm and two locations separated by 5 mm are determined so as to coincide with the crack growth region of the fatigue test piece described later.
  • the standard deviation of the Vickers hardness at a position of 20 ⁇ m in the thickness direction from the steel sheet surface is defined as 20 or less based on such experimental results.
  • the steel sheet for a hot stamp member of the present invention is made into a cold-rolled steel sheet by performing each process of steelmaking, casting, hot rolling, pickling process, and cold rolling based on a conventional method.
  • a slab is formed in the continuous casting process.
  • hot rolling is started at a heating temperature of 1300 ° C. or less, and rolling is completed at around 900 ° C. Let For example, 600 ° C. can be selected as the winding temperature.
  • the hot rolling rate may be 60 to 90%.
  • Cold rolling is performed through a pickling process. The rolling rate can be selected from a range of 30 to 90%.
  • the annealing process is performed using a continuous annealing facility, and the first stage of heating from room temperature to temperature M (° C.) at an average heating rate of 8 to 25 ° C./second, followed by the temperature S at an average heating rate of 1 to 7 ° C./second. It consists of a two-stage configuration of the second stage that is heated to (° C.). Here, it is necessary that the temperature M is 600 to 700 (° C.) and the temperature S is 720 to 820 (° C.). These conditions were determined based on the experimental results described in the examples described below.
  • the recrystallization process of a cold-rolled steel sheet is complicated, it is not appropriate to separate the heating rate for the phenomenon of recrystallization and the meaning of the maximum heating temperature at that heating rate. Therefore, first, for the first stage, for example, a case where the heating rate is small and a case where the heating rate is small and large is considered for one temperature M (° C.).
  • the heating rate in the second stage needs to be lower than that in the first stage in order to suppress the competition for the growth of recrystallized grains.
  • the temperature range from the temperature M (° C.) to the temperature S (° C.) the reformation of carbides due to carbon diffusion becomes active, so the setting of the maximum temperature S (° C.) of the annealing process and the heating rate up to that temperature
  • the combination has an important meaning.
  • the temperature S After reaching the temperature S, the temperature S may be held for a short time, or may immediately move to the next cooling step.
  • the retention time is desirably 180 seconds or less, and more desirably 120 seconds or less, from the viewpoint of suppressing the coarsening of the crystal grain size.
  • the cooling rate from the temperature S in the cooling process is not particularly limited, but it is desirable to avoid rapid cooling of 30 ° C./second or more. Therefore, the cooling rate from the temperature S is less than 30 ° C./second, preferably 20 ° C. or less, and more preferably 10 ° C. or less. This is because hot stamping steel plates are often processed into a predetermined shape by shearing and used for hot stamping, and rapid cooling raises the concern that the shearing load may be increased to reduce the production efficiency.
  • the molten Al bath may contain 0.1 to 20% Si.
  • Si contained in the Al plating layer affects the reaction between Al and Fe generated during heating before hot stamping. Excessive reaction may impair the press formability of the plating layer itself, while suppression of excessive reaction may cause adhesion of Al to the press mold.
  • the Si content in the Al plating layer is desirably 1 to 15%, more preferably 3 to 12%.
  • a Zn plating layer may be formed by immersing in a molten Zn bath during cooling after annealing.
  • the Zn—Fe alloy layer may be formed by heating to 600 ° C. or lower.
  • the molten Zn bath can contain 0.01 to 3% Al.
  • the presence of Al strongly affects the reaction between Zn and Fe.
  • the reaction layer of Fe and Al becomes an obstacle and suppresses mutual diffusion of Zn and Fe.
  • the Zn—Fe alloy layer is composed of an alloy layer rich in Zn ( ⁇ phase, ⁇ 1 phase) and an alloy layer rich in Fe ( ⁇ 1 phase, ⁇ phase).
  • it is rich in adhesiveness, it is inferior in workability, and the latter is excellent in workability, but the adhesiveness is insufficient. Therefore, it is necessary to satisfy the desired characteristics (adherence to adhesion, priority to workability, or balance both, etc.) by appropriately controlling the composition ratio of these four phases.
  • This can be performed by controlling the diffusion of Fe by adding 0.01 to 3% Al to the molten Zn bath.
  • the manufacturer can select the concentration according to the capability and purpose of the equipment to be manufactured.
  • the thickness of the Al plating layer, Zn plating layer, and Zn-Fe alloy layer does not affect the fatigue characteristics of the steel plate or component after hot stamping, but if it is too thick, it may affect the press formability. There is. As shown in the examples, the occurrence of galling was observed when the thickness of the Al plating layer exceeded 50 ⁇ m, and the adhesion of Zn to the mold when the thickness of the Zn plating layer exceeded 30 ⁇ m. When the thickness of the Zn—Fe alloy layer exceeds 45 ⁇ m, the alloy layer is cracked and the productivity is impaired. Therefore, the thicknesses of these layers are preferably set to Al plating layer: 50 ⁇ m or less, Zn plating layer: 30 ⁇ m or less, and Zn—Fe alloy layer: 45 ⁇ m or less.
  • each plating layer is thin, there is no problem in terms of formability, but it is preferable to set the lower limit of each plating layer as follows from the viewpoint of corrosion resistance, which is the purpose of providing these plating layers. That is, Al plating layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more, Zn plating layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more, Zn—Fe alloy layer: preferably 5 ⁇ m or more, more preferably 10 ⁇ m or more. .
  • Example 1 Steel pieces a to f having chemical components shown in Table 1 were made and cast. These steel pieces were heated to 1250 ° C. and subjected to a hot rolling process to obtain a hot-rolled steel sheet having a finishing temperature of 900 ° C. and a winding temperature of 600 ° C. and a thickness of 3.2 mm. The hot-rolled steel sheet was pickled and then cold-rolled to obtain a cold-rolled steel sheet having a thickness of 1.6 mm.
  • the cold-rolled steel sheets were recrystallized and annealed under the conditions i to xviii described in Table 2 to obtain steel sheets 1 to 32 for hot stamp members shown in Table 3.
  • Two test pieces for hardness measurement before hot stamping were collected from a part thereof.
  • the specimen collection position was a position 5 mm away in the sheet width direction of the obtained steel sheet for hot stamp members.
  • the average heating rate 1 (first stage) and average heating rate 2 (second stage) in Table 2 are from room temperature to temperature M (° C.) and from temperature M (° C.) to temperature S (° C.), respectively. The average heating rate until is shown.
  • hot stamp member steel plates were held at 900 ° C. for 10 minutes, and then hot stamped by being sandwiched between experimental flat plate press molds shown in FIG.
  • Ten hot stamping processes were performed for each type of hot stamping steel sheet. From one of these, two tensile test pieces according to JIS No. 5 and two test pieces for hardness measurement (the same procedure as before hot stamping) were collected. From the remaining nine sheets, two fatigue test pieces shown in FIG. The processing method for sampling was electrical discharge machining.
  • a tensile test was performed to determine the tensile strength ⁇ B (average value of two tensile test pieces).
  • a plane bending fatigue test was performed using 18 test pieces, and the time strength ⁇ W was determined 1 ⁇ 10 7 times.
  • the test conditions were a stress ratio of ⁇ 1 and a repetition rate of 5 Hz.
  • the test piece for hardness measurement is a mirror-polished cross section parallel to the rolling direction of the cold-rolled steel sheet both before and after hot stamping.
  • the internal hardness of 20 ⁇ m in the thickness direction from the surface of these test pieces was measured using a Vickers hardness meter (HM-220D manufactured by Mitutoyo Corporation).
  • the indentation load was 10 gf
  • the indentation time was 15 seconds
  • the measurement interval in the direction parallel to the surface was 0.1 mm
  • 300 points were measured.
  • Table 3 shows steel codes, processing conditions, standard deviation of hardness before hot stamping, and tensile strength ⁇ B (average value of two), strength ⁇ W , fatigue limit ratio ⁇ W / ⁇ B , and hot stamping The standard deviation of the hardness afterwards is shown.
  • FIG. 4 shows the correlation between the fatigue limit ratio ⁇ W / ⁇ B and the standard deviation of hardness before hot stamping.
  • the first heating is performed from room temperature to temperature M (° C.) at an average heating rate of 15 to 25 ° C./second.
  • M is 620-680 (° C.)
  • S is 780-820 (° C.)
  • Became clear is performed from room temperature to temperature M (° C.) at an average heating rate of 15 to 25 ° C./second.
  • Example 2 Steel pieces 2a to 2h having chemical components shown in Table 4 were made and cast. With these steel pieces, hot-rolled steel sheets having a thickness of 3.0 mm were obtained under the same conditions as in Example 1. These hot-rolled steel sheets were pickled and cold-rolled to 1.2 mm.
  • FIG. 6 shows the correlation between the fatigue limit ratio ⁇ W / ⁇ B and the standard deviation of hardness before hot stamping.
  • the hardness variation of the surface layer before hot stamping is more than 20 in standard deviation, and the hot stamping obtained using them
  • the fatigue limit ratio of the members was 0.26 to 0.31, and it was revealed that the fatigue characteristics were inferior.
  • Example 3 Steel plates 3a to 3d having chemical components shown in Table 6 were made and cast. With these steel pieces, hot rolled steel sheets having a thickness of 2.5 mm were obtained under the same conditions as in Example 1. These hot-rolled steel sheets were pickled and cold-rolled to 1.2 mm.
  • a test piece for hardness measurement was collected from the obtained steel sheet in the same manner as in Example 1.
  • the hardness at the position of 20 ⁇ m from the boundary between the inner layer (the reaction layer of Al and Fe) of the Al plating layer and the steel plate was measured in the same manner as in Example 1.
  • the thickness of the Al plating layer (total of two layers) was also measured.
  • the thickness measurement range is 30 mm in length, the same as the hardness measurement range, 7 points are measured at a measurement interval of 5 mm, and 14 points are measured in total for the measurement positions of the first measurement surface and the second measurement surface, and the average value is measured. Asked.
  • the fatigue test piece shown in FIG. 2 and the JIS No. 5 tensile test piece were collected from the hat head.
  • Example 4 Steel plates 3a to 3d having chemical components shown in Table 6 were made and cast. With these steel pieces, hot rolled steel sheets having a thickness of 2.5 mm were obtained under the same conditions as in Example 1. These hot-rolled steel sheets were pickled and cold-rolled to 1.2 mm.
  • a test piece for hardness measurement was collected from the obtained steel sheet in the same manner as in Example 1.
  • the hardness at a position of 20 ⁇ m from the boundary between the inner layer (Al and Fe reaction layer) of the Zn plating layer and the steel plate was measured in the same manner as in Example 1.
  • the thickness of only the Zn plating layer was also measured.
  • the thickness measurement range is 30 mm in length, the same as the hardness measurement range, 7 points are measured at a measurement interval of 5 mm, and 14 points are measured in total for the measurement positions of the first measurement surface and the second measurement surface, and the average value is measured. Asked.
  • the fatigue test piece shown in FIG. 2 and the JIS No. 5 tensile test piece were collected from the hat head.
  • Example 5 Steel plates 3a to 3d having chemical components shown in Table 6 were made and cast. With these steel pieces, hot rolled steel sheets having a thickness of 2.5 mm were obtained under the same conditions as in Example 1. These hot-rolled steel sheets were pickled and cold-rolled to 1.2 mm.
  • a test piece for hardness measurement was collected from the obtained steel sheet in the same manner as in Example 1.
  • the hardness at a position of 20 ⁇ m from the boundary between the innermost layer (Zn and Fe reaction layer) of the Zn—Fe alloy layer and the steel plate was measured in the same manner as in Example 1.
  • the total thickness of the Zn—Fe alloy layer (consisting of four layers) was also measured.
  • the thickness of the Al plating layer (total of two layers) was also measured.
  • the thickness measurement range is 30 mm in length, the same as the hardness measurement range, 7 points are measured at a measurement interval of 5 mm, and 14 points are measured in total for the measurement positions of the first measurement surface and the second measurement surface, and the average value is measured. Asked.
  • the fatigue test piece shown in FIG. 2 and the JIS No. 5 tensile test piece were collected from the hat head.

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CN103443317A (zh) 2013-12-11
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