EP2527482A1 - Hochfestes feuerverzinktes stahlblech mit hervorragender materialstabilität und verarbeitbarkeit sowie verfahren zu seiner herstellung - Google Patents

Hochfestes feuerverzinktes stahlblech mit hervorragender materialstabilität und verarbeitbarkeit sowie verfahren zu seiner herstellung Download PDF

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Publication number
EP2527482A1
EP2527482A1 EP11734786A EP11734786A EP2527482A1 EP 2527482 A1 EP2527482 A1 EP 2527482A1 EP 11734786 A EP11734786 A EP 11734786A EP 11734786 A EP11734786 A EP 11734786A EP 2527482 A1 EP2527482 A1 EP 2527482A1
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steel sheet
area ratio
phase
galvanized steel
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English (en)
French (fr)
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EP2527482A4 (de
EP2527482B1 (de
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Yoshiyasu Kawasaki
Tatsuya Nakagaito
Shinjiro Kaneko
Yasunobu Nagataki
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JFE Steel Corp
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JFE Steel Corp
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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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/12—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the shape fixability is degraded by an increase in strength and thickness reduction of a steel sheet significantly.
  • press forming it has been widely performed that changes in shape after release from a mold is predicted and the mold is designed in expectation of the amount of change in shape.
  • TS tensile strength
  • deviation from the expected amount, in which these are assumed to be constant becomes large and odd shapes occur. Consequently, rework, e.g., sheet-metal working of the shape on a one-by-one basis, becomes necessary after press-forming, and the efficiency in mass production is degraded significantly. Therefore, it is required that variations in TS of the steel sheet are minimized.
  • Japanese Unexamined Patent Application Publication No. 2001-140022 has proposed a steel sheet having excellent elongation by specifying the chemical components and specifying the volume ratios of retained austenite and martensite and methods for manufacturing the same.
  • Japanese Unexamined Patent Application Publication No. 04-026744 has proposed a steel sheet having excellent elongation by specifying the chemical components and, furthermore, specifying a special method for manufacturing the same.
  • Japanese Unexamined Patent Application Publication No. 2007-182625 has proposed a steel sheet having excellent elongation by specifying the chemical components and specifying the volume ratios of ferrite, bainitic ferrite, and retained austenite phases.
  • Japanese Unexamined Patent Application Publication No. 2000-212684 has proposed a method for manufacturing a high strength cold rolled steel sheet in which variations in elongation in the sheet width direction have been improved.
  • a high strength galvanized steel sheet having excellent formability and stability of mechanical properties having a component composition containing C: 0.04% or more, and 0.13% or less, Si: 0.7% or more, and 2.3% or less, Mn: 0.8% or more, and 2.0% or less, P: 0.1% or less, S: 0.01% or less, Al: 0.1% or less, N: 0.008% or less, and the remainder composed of Fe and incidental impurities on a percent by mass basis, wherein a steel microstructure includes 75% or more of ferrite phase, 1.0% or more of bainitic ferrite phase, and 1.0% or more, and 10.0% or less of pearlite phase on an area ratio basis, the area ratio of martensitic phase is 1.0% or more, and less than 5.0%, and the area ratio of martensitic phase/(area ratio of bainitic ferrite phase + area ratio of pearlite phase) ⁇ 0.6 is satisfied.
  • the high strength galvanized steel sheet having excellent formability and stability of mechanical properties according to the item (1) or item (2), further containing at least one type of element selected from Ti: 0.01% or more, and 0.1% or less, Nb: 0.01% or more, and 0.1% or less, and B: 0.0003% or more, and 0.0050% or less, on a percent by mass basis, as the component composition.
  • the high strength galvanized steel sheet having excellent formability and stability of mechanical properties according to any one of the items (1) to (3), further containing at least one type of element selected from Ca: 0.001% or more, and 0.005% or less and REM: 0.001% or more, and 0.005% or less, on a percent by mass basis, as the component composition.
  • the high strength galvanized steel sheet having excellent formability and stability of mechanical properties according to any one of the items (1) to (4), further containing at least one type of element selected from Ta: 0.001% or more, and 0.010% or less and Sn: 0.002% or more, and 0.2% or less, on a percent by mass basis, as the component composition.
  • high strength galvanized steel sheet refers to a galvanized steel sheet having a tensile strength TS of 540 MPa or more.
  • galvanized steel sheets regardless of whether an alloying treatment is performed or not, steel sheets in which a zinc coating is applied to a steel sheet by galvanization are generically called galvanized steel sheets. That is, the galvanized steel sheets in the present invention include both galvanized steel sheets not subjected to an alloying treatment and galvannealed steel sheets subjected to an alloying treatment.
  • C 0.04% or more, and 0.13% or less Carbon is an austenite forming element and is an element indispensable for strengthening a steel. If the amount of C is less than 0.04%, it is difficult to ensure desired strength. On the other hand, if the amount of C exceeds 0.13% and, therefore, addition is excessive, a welded zone and a heat-affected zone are hardened significantly, and the mechanical characteristics of the welded zone are degraded, so that the spot weldability, the arc weldability, and the like are degraded. Therefore, C is specified to be 0.04% or more, and 0.13% or less.
  • Si 0.7% or more, and 2.3% or less
  • Silicon is a ferrite forming element and is also an element effective in solution hardening.
  • 0.7% or more of addition is necessary to ensure good elongation due to an improvement in work hardening property of the ferrite phase.
  • 0.7% or more of addition is also necessary to ensure a desired area ratio of bainitic ferrite phase and ensure good stretch flangeability.
  • excessive addition of Si causes degradation of surface quality due to an occurrence of red scale and the like and degradation of deposition and adhesion of the coating. Therefore, Si is specified to be 0.7% or more, and 2.3% or less, and preferably 1.2% or more, and 1.8% or less.
  • Mn 0.8% or more, and 2.0% or less
  • Mn is an element to stabilize austenite and an element necessary for adjusting the ratio of a secondary phase.
  • addition of 0.8% or more of Mn is necessary.
  • Mn is specified to be 0.8% or more, and 2.0% or less, and preferably 1.0% or more, and 1.8% or less.
  • Phosphorus is an element effective in strengthening a steel. However, if addition is excessive and exceeds 0.1%, embrittlement is caused by grain boundary segregation, and the crashworthiness is degraded. Furthermore, if 0.1% is exceeded, an alloying speed is reduced significantly. Therefore, P is specified to be 0.1% or less.
  • S 0.01% or less Sulfur forms inclusions, e.g., MnS, to cause degradation in crashworthiness and cracking along a metal flow of a welded zone and, therefore, is minimized, although S is specified to be 0.01% or less from the viewpoint of production cost.
  • inclusions e.g., MnS
  • Al 0.1% or less If Al exceeds 0.1%, coarse Al 2 O 3 is generated and the mechanical properties are degraded.
  • the amount of addition is specified to be 0.01% or more because if the amount is less than 0.01%, a large number of coarse oxides of Mn, Si, and the like are dispersed in the steel to degrade the mechanical properties. Therefore, the amount of Al is specified to be 0.1% or less, and preferably 0.01% to 0.1%.
  • N 0.008% or less Nitrogen is an element which degrades the aging resistance of a steel to a greatest extent and preferably is minimized. If 0.008% is exceeded, degradation of the aging resistance becomes significant. Therefore, N is specified to be 0.008% or less.
  • the remainder is composed of Fe and incidental impurities. However, besides these elements, at least one type selected from the following elements can be added, as necessary.
  • Ti and niobium are effective in precipitation hardening of a steel. The effect is obtained when each of them is 0.01% or more and, therefore, there is no problem in use for strengthening the steel within the bounds of the specification of the present invention. However, if each of them exceeds 0.1%, the formability and the shape fixability are degraded. Furthermore, an increase in cost is brought about. Therefore, in the case where Ti and Nb are added, the amount of addition of Ti is specified to be 0.01% or more, and 0.1% or less and Nb is specified to be 0.01% or more, and 0.1% or less.
  • B has a function of suppressing generation and growth of ferrite from austenite grain boundaries and, therefore, can be added as necessary.
  • the effect is obtained when B is 0.0003% or more. However, if 0.0050% is exceeded, the formability is degraded. Furthermore, an increase in cost is brought about. Therefore, in the case where B is added, B is specified to be 0.0003% or more, and 0.0050% or less.
  • Tin can be added from the viewpoint of suppressing nitriding and oxidation of a steel sheet surface or decarbonization of several ten micrometers of region of a steel sheet surface layer generated through oxidation. Suppression of such nitriding and oxidation prevents reduction in the amount of generation of martensite on the steel sheet surface and improves the fatigue resistance and the aging resistance. From the viewpoint of suppression of nitriding and oxidation, in the case where Sn is added, it is desirable that the content thereof is specified to be 0.002% or more, and it is desirable that the content thereof is specified to be 0.2% or less because if 0.2% is exceeded, reduction in toughness is brought about.
  • the area ratios of ferrite, bainitic ferrite, pearlite, and martensitic phases refer to proportions of the areas of the individual phases constituting an observation area.
  • the alloying treatment of zinc coating is performed in a temperature range of 500°C to 600°C under the condition satisfying the following formula, 0.45 ⁇ exp 200 / 400 - T ⁇ ln t ⁇ 1.0
  • T average keeping temperature (°C) in a temperature range of 500°C to 600°C
  • t keeping time (s) in a temperature range of 500°C to 600°C
  • exp(X) and ln(X) represent an exponential function and natural logarithm, respectively, of X.
  • a steel having the above-described component composition is melted, is made into a slab through roughing or continuous casting, and is made into a hot rolled sheet through hot rolling by a known method.
  • hot rolling it is preferable that the slab is heated to 1,100°C to 1,300°C, hot rolling is performed at a final finishing temperature of 850°C or higher, and steel sheet is coiled at 400°C to 650°C.
  • the coiling temperature exceeds 650°C, carbides in the hot-rolled sheet may become coarse, and required strength cannot be obtained in some cases because such coarse carbides are not melted completely during soaking in annealing.
  • a pickling treatment is performed by a known method.
  • the pickled hot rolled sheet or the cold rolled steel sheet is subjected to annealing described below and, then, cooling and galvanization are performed.
  • Heating to temperature range of 650°C or higher at average heating rate of 5°C/s or more If the average heating rate in heating to the temperature range of 650°C or higher is less than 5°C/s, a fine uniformly dispersed austenite phase is not generated during annealing, the area ratio of martensitic phase in the final microstructure increases and it is difficult to ensure good stretch flangeability. Furthermore, a furnace longer than a usual furnace is necessary and, thereby, an increase in cost associated with large energy consumption and reduction in production efficiency are brought about. It is preferable that a direct fired furnace (DFF) is used as a furnace. This is because an internal oxide layer is formed through rapid heating by the DFF and, thereby, concentration of oxides of Si, Mn, and the like on the outermost layer of the steel sheet is prevented so as to ensure good wettability of the coating.
  • DFF direct fired furnace
  • alloying of the coating layer is not facilitated, and it is difficult to obtain a galvannealed steel sheet. Meanwhile, in the temperature range exceeding 600°C, most of the secondary phase is converted to pearlite, so that a desired area ratio of martensitic phase is not obtained and the balance between the strength and the elongation is reduced. Alloying of the coating layer can be performed in the scope of the present invention, in which the temperature is in the range of 500°C to 600°C and the above-described condition of exp[200/(400 - T)] ⁇ ln(t) is satisfied, without problems.
  • the keeping temperature is not necessary constant insofar as the temperature is in the above-described range. Furthermore, even in the case where the cooling rate is changed during cooling, the gist of the present invention is not impaired insofar as the rate is in the specified range.
  • the steel sheet may be subjected to a heat treatment by any equipment insofar as only the heat history is satisfied.
  • the steel sheet according to the present invention is subjected to temper rolling after the heat treatment for the purpose of shape correction.
  • a steel is produced through usual steps of steel making, casting, and hot rolling. However, for example, the steel may be produced through thin wall casting or the like, where a part of or whole hot rolling step is omitted.
  • Fig. 1 and Fig. 2 are diagrams showing the organized relationships between TS and the annealing temperature (T 1 ) and between EL and the annealing temperature (T 1 ) with respect to Nos. 15, 16, and 17 of Steel A, which are invention examples, (Table 2 and Table 5) and Nos. 18, 19, and 20 of Steel H, which are comparative examples, (Table 2 and Table 5) in Examples described later.
  • Table 2 and Table 5 are diagrams showing the organized relationships between TS and the annealing temperature (T 1 ) and between EL and the annealing temperature (T 1 ) with respect to Nos. 15, 16, and 17 of Steel A, which are invention examples, (Table 2 and Table 5) and Nos. 18, 19, and 20 of Steel H, which are comparative examples, (Table 2 and Table 5) in Examples described later.
  • Table 2 and Table 5 are diagrams showing the organized relationships between TS and the annealing temperature (T 1 ) and between EL and the annealing temperature (T 1 ) with respect to Nos
  • Fig. 3 and Fig. 4 are diagrams showing the organized relationships between TS and the average keeping time (T 2 ) in cooling after annealing and between EL and the average keeping time (T 2 ) with respect to Nos. 21, 22, and 23 of Steel A, which are invention examples, (Table 2 and Table 5) and Nos. 24, 25, and 26 of Steel H, which are comparative examples, (Table 2 and Table 5) in Examples described later.
  • Table 2 and Table 5 are invention examples, (Table 2 and Table 5) and Nos. 24, 25, and 26 of Steel H, which are comparative examples, (Table 2 and Table 5) in Examples described later.
  • FIG. 3 and Fig. 4 regarding Steel A of the invention example, variations in TS and EL associated with changes in average keeping time are small, whereas variations in TS and EL are large regarding Steel H of the comparative example.
  • the resulting slab was heated to 1,200°C, hot rolling to a sheet thickness of 3.2 mm was performed at a finish temperature of 870°C to 920°C, and coiling was performed at 520°C. Subsequently, the resulting hot-rolled sheet was pickled. A part of the resulting hot-rolled sheets were served as pickled hot-rolled steel sheets, and a part of the hot-rolled sheets were subjected to cold rolling, so as to produce cold-rolled steel sheets.
  • the hot-rolled steel sheet (after pickling) and the cold-rolled steel sheet obtained as described above were subjected to an annealing treatment and a galvanizing treatment with a continuous galvanization line under the production condition shown in Tables 2 to 4. Furthermore, an alloying treatment of the plating layer was performed, so as to obtain a galvannealed steel sheet.
  • the amount of deposition of coating was specified to be 30 to 50 g/m 2 on one surface basis.
  • galvanized steel sheets, which were not subjected to an alloying treatment after being galvanized were also produced.
  • the area ratios of ferrite, bainitic ferrite, pearlite, and martensitic phases were determined by polishing a sheet thickness cross-section parallel to a rolling direction of the steel sheet, followed by corroding with 3% nital, and observing 10 visual fields with a scanning electron microscope (SEM) under a magnification of 2,000 times through the use of Image-Pro of Media Cybernetics, Inc. At that time, it was difficult to distinguish martensite and retained austenite.
  • SEM scanning electron microscope
  • the resulting galvanized steel sheet was subjected to a tempering treatment at 200°C for 2 hours, the microstructure of a sheet thickness cross-section parallel to the rolling direction of the steel sheet was observed by the above-described method, and the aria ratio of tempered martensitic phase determined by the above-described method was taken as the aria ratio of martensitic phase. Furthermore, the volume ratio of retained austenite phase was determined on the basis of integrated intensity of ferrite and austenite peaks of a face at one-quarter sheet thickness, where the steel sheet was polished up to the one-quarter face in the sheet thickness direction.
  • X-ray diffractometer using Co-Ka was used, the intensity ratios were determined with respect to all combinations of integrated intensities of peaks of ⁇ 111 ⁇ , ⁇ 200 ⁇ , ⁇ 220 ⁇ , and ⁇ 311 ⁇ faces of retained austenite phase and ⁇ 110], ⁇ 200 ⁇ , and ⁇ 211 ⁇ faces of ferrite phase, and the average value of them was taken as the volume ratio of retained austenite phase.
  • a tensile test was performed on the basis of JIS Z2241 by using JIS No. 5 test piece, where sample was taken in such a way that a tensile direction becomes in the direction orthogonal to the rolling direction of the steel sheet, and the tensile strength (TS) and the total elongation (EL) were measured.
  • TS tensile strength
  • EL total elongation
  • the hole expansion property (stretch flangeability) was measured.
  • the hole expansion property (stretch flangeability) was measured on the basis of the Japan Iron and Steel Federation Standard JFST1001.
  • JFST1001 Japan Iron and Steel Federation Standard
  • Every high strength galvanized steel sheet according to the present invention has TS of 540 MPa or more and has ⁇ of 70% or more so as to exhibit excellent stretch flangeability. Furthermore, TS ⁇ EL ⁇ 19,000 MPa ⁇ % is satisfied and the balance between the strength and the elongation is high. Therefore, it is clear that a high strength galvanized steel sheet having excellent formability is obtained. Moreover, the values of ⁇ TS and ⁇ EL are small and, therefore, it is clear that a high strength galvanized steel sheet having excellent stability of mechanical properties is obtained. On the other hand, regarding comparative examples, at least one of the elongation and the stretch flangeability is poor, or the stability of mechanical properties is not favorable.
  • the high strength galvanized steel sheet according to the present invention has a tensile strength TS of 540 MPa or more, exhibits high elongation and high stretch flangeability, and has excellent stability of mechanical properties.
  • TS tensile strength
  • the high strength galvanized steel sheet according to the present invention is applied to, for example, an automobile structural member, enhancement of fuel economy due to weight reduction of a car body can be facilitated. Therefore, an industrial utility value is very large.
EP11734786.4A 2010-01-22 2011-01-18 Verfahren zur herstellung eines hochfestes feuerverzinktes stahlblech mit hervorragender materialstabilität und verarbeitbarkeit Active EP2527482B1 (de)

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JP2010262087A JP5786317B2 (ja) 2010-01-22 2010-11-25 材質安定性と加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
PCT/JP2011/051151 WO2011090180A1 (ja) 2010-01-22 2011-01-18 材質安定性と加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法

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EP2402470A1 (de) * 2009-02-25 2012-01-04 JFE Steel Corporation Hochfeste feuerverzinkte stahlplatte mit hervorragender bearbeitbarkeit und verfahren zu ihrer herstellung
CN104350170A (zh) * 2012-06-01 2015-02-11 杰富意钢铁株式会社 伸长率和延伸凸缘性优良的低屈服比高强度冷轧钢板及其制造方法
EP2762583A4 (de) * 2011-09-30 2015-12-02 Nippon Steel & Sumitomo Metal Corp Hochfestes feuerverzinktes stahlblech mit hervorragender beständigkeit gegen verzögerte fraktur und herstellungsverfahren dafür
EP2527484A4 (de) * 2010-01-22 2016-02-17 Jfe Steel Corp Hochfestes feuerverzinktes stahlblech mit hervorragender verarbeitbarkeit und punktschweissbarkeit sowie verfahren zu seiner herstellung
EP2886674A4 (de) * 2012-08-15 2016-11-30 Nippon Steel & Sumitomo Metal Corp Stahlblech zur verwendung in einer heisspressung, herstellungsverfahren dafür und mithilfe des stahlblechs heissgepresstes element

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JP5862002B2 (ja) * 2010-09-30 2016-02-16 Ｊｆｅスチール株式会社 疲労特性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP5246283B2 (ja) * 2011-02-28 2013-07-24 Ｊｆｅスチール株式会社 伸びと伸びフランジ性に優れた低降伏比高強度冷延鋼板およびその製造方法
JP5793971B2 (ja) * 2011-06-01 2015-10-14 Ｊｆｅスチール株式会社 材質安定性、加工性およびめっき外観に優れた高強度溶融亜鉛めっき鋼板の製造方法
JP5267638B2 (ja) * 2011-11-17 2013-08-21 Ｊｆｅスチール株式会社 高強度溶融亜鉛めっき鋼板または高強度合金化溶融亜鉛めっき鋼板用熱延鋼板およびその製造方法
TWI454582B (zh) * 2012-06-13 2014-10-01 Jfe Steel Corp 延伸及延伸凸緣性優異之低降伏比高強度冷延鋼板及其製造方法

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Publication number Priority date Publication date Assignee Title
EP2402470A1 (de) * 2009-02-25 2012-01-04 JFE Steel Corporation Hochfeste feuerverzinkte stahlplatte mit hervorragender bearbeitbarkeit und verfahren zu ihrer herstellung
EP2402470A4 (de) * 2009-02-25 2017-04-26 JFE Steel Corporation Hochfeste feuerverzinkte stahlplatte mit hervorragender bearbeitbarkeit und verfahren zu ihrer herstellung
EP2527484A4 (de) * 2010-01-22 2016-02-17 Jfe Steel Corp Hochfestes feuerverzinktes stahlblech mit hervorragender verarbeitbarkeit und punktschweissbarkeit sowie verfahren zu seiner herstellung
EP2762583A4 (de) * 2011-09-30 2015-12-02 Nippon Steel & Sumitomo Metal Corp Hochfestes feuerverzinktes stahlblech mit hervorragender beständigkeit gegen verzögerte fraktur und herstellungsverfahren dafür
CN104350170A (zh) * 2012-06-01 2015-02-11 杰富意钢铁株式会社 伸长率和延伸凸缘性优良的低屈服比高强度冷轧钢板及其制造方法
CN104350170B (zh) * 2012-06-01 2018-03-06 杰富意钢铁株式会社 伸长率和延伸凸缘性优良的低屈服比高强度冷轧钢板及其制造方法
EP2886674A4 (de) * 2012-08-15 2016-11-30 Nippon Steel & Sumitomo Metal Corp Stahlblech zur verwendung in einer heisspressung, herstellungsverfahren dafür und mithilfe des stahlblechs heissgepresstes element
US10570470B2 (en) 2012-08-15 2020-02-25 Nippon Steel Corporation Steel sheet for hot stamping, method of manufacturing the same, and hot stamped steel sheet member

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TW201139731A (en) 2011-11-16
EP2527482A4 (de) 2017-04-05
WO2011090180A1 (ja) 2011-07-28
EP2527482B1 (de) 2019-12-25
JP2011168877A (ja) 2011-09-01
TWI433961B (zh) 2014-04-11
JP5786317B2 (ja) 2015-09-30

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