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WO2016103535A1 - Tôle d'acier de haute résistance galvanisée par immersion à chaud et son procédé de fabrication - Google Patents

Tôle d'acier de haute résistance galvanisée par immersion à chaud et son procédé de fabrication Download PDF

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Publication number
WO2016103535A1
WO2016103535A1 PCT/JP2015/003846 JP2015003846W WO2016103535A1 WO 2016103535 A1 WO2016103535 A1 WO 2016103535A1 JP 2015003846 W JP2015003846 W JP 2015003846W WO 2016103535 A1 WO2016103535 A1 WO 2016103535A1
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steel sheet
temperature
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Japanese (ja)
Inventor
典晃 ▲高▼坂
船川　義正
櫻井　理孝
康弘 西村
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JFE Steel Corp
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JFE Steel Corp
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Priority to KR1020177017047A priority Critical patent/KR101913530B1/ko
Priority to MX2017008295A priority patent/MX2017008295A/es
Priority to JP2015558271A priority patent/JP5958666B1/ja
Priority to CN201580069935.8A priority patent/CN107208205B/zh
Publication of WO2016103535A1 publication Critical patent/WO2016103535A1/fr
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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
    • C21D8/0247—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
    • 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
    • C22C18/00—Alloys based on zinc
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • 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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a high-strength hot-dip galvanized steel sheet having a high tensile strength (TS): 980 MPa or more and an excellent bendability, and a method for producing the same, which are useful for the use of automotive framework members.
  • TS tensile strength
  • the steel sheet composition is mass%, C: 0.05% or more and less than 0.12%, Si: 0.1% or less (excluding 0%), Mn: 2.0% or more and 3.5% or less, Ti, Nb and V At least one element selected from the group consisting of 0.01% to 0.2% in total, B: 0.0003% to 0.005%, P: 0.05% or less, S: 0.05% or less, Al: 0.1% or less, N: It satisfies 0.015% or less, the metal structure contains bainite and martensite, and may further contain a ferrite phase.
  • Martensite 15 to 50%, ferrite phase: 5% or less (0%) ), The remaining structure excluding bainite, martensite and ferrite phase: 3% or less (including 0%), and the average crystal grain size of bainite: 7 ⁇ m or less satisfying the tensile strength of 980 MPa or more It is said that a high yield ratio high strength steel sheet with excellent workability can be obtained.
  • the steel sheet composition is, in mass%, C: 0.075 to 0.300%, Si: 0.30 to 2.50%, Mn: 1.30 to 3.50%, P: 0.001 to 0.050%, S: 0.0001 to 0.0100%, Al: Tensile formed by forming an alloyed galvanized layer on the surface of a base steel plate containing 0.005 to 1.500%, N: 0.0001 to 0.0100%, O: 0.0001 to 0.0100%, the balance being iron and inevitable impurities It is a high-strength galvanized steel sheet with a maximum strength of 900 MPa or more. In the range of 1/8 to 3/8 thickness of the base steel sheet, the retained austenite is limited to 8% or less in volume fraction.
  • a plurality of measurement areas with a diameter of 1 ⁇ m or less are set, and the hardness distribution in the plurality of measurement areas is arranged in ascending order to obtain a hardness distribution. If the whole number is multiplied by 0.02 and this number includes a decimal number, the integer N0.02 obtained by rounding it up is obtained to determine the minimum hardness.
  • the composition of the steel sheet is mass%, C: 0.05 to 0.25%, Si: 0.5% or less (including 0%), Mn: 2.0 to 4%, P: 0.1% or less (not including 0%) ), S: 0.05% or less (not including 0%), Al: 0.01 to 0.1%, Ti, B: 0.0003 to 0.005%, and N: 0.01% or less (not including 0%), the balance being
  • a hot-dip galvanized steel sheet having a hot-dip galvanized layer on the surface of a base steel sheet made of iron and inevitable impurities, and the metal structure of the base steel sheet has a martensite phase, a bainite phase, and a ferrite phase, and the entire metal structure
  • the ratio of the martensite satisfies 50 area% or more, the bainite satisfies 15 to 50 area%, and the ferrite phase satisfies 5 area% or less (including 0 area%). It is said that a high-strength hot-dip galvanized
  • JP 2013-147736 Japanese Patent No. 5273324 JP 2013-227660
  • Patent Document 1 since the technique proposed in Patent Document 1 does not consider the surface structure, it is considered difficult to obtain good bendability.
  • Patent Document 3 considers reducing the strength difference in the plate width direction, but does not consider the structure of the surface layer, so it is difficult to obtain good bendability.
  • an object of the present invention is to provide a high-strength hot-dip galvanized steel sheet having a tensile strength of 980 MPa or more and good bendability and a method for producing the same.
  • the balance between strength and ductility can be improved, and the main component is an autotempered martensite phase in which carbide precipitates in the grains. It was found to be effective. Furthermore, it was found that when the ferrite phase was formed on the steel sheet surface, voids were generated at the interface between the ferrite phase and the bainite phase, martensite phase, or autotempered martensite phase, resulting in deterioration of bendability. . And in order to suppress the formation of the ferrite phase on the surface of the steel sheet, it is important to reduce the uneven distribution of elements in the steel sheet as much as possible. For this purpose, pre-heating considering the atmosphere and heating temperature is necessary before annealing. It was found that applying the process is effective.
  • Component composition is mass%, C: 0.09% to 0.20%, Si: less than 0.50%, Mn: 2.2% to 3.5%, P: 0.03% or less, S: 0.005% or less, Al: 0.08 %: N: 0.006% or less, B: 0.0002% or more and 0.0030% or less, the balance consists of Fe and unavoidable impurities, the structure is the area ratio, the ferrite phase is less than 10% (including 0%), The bainite phase is 50% or less (including 0%), the martensite phase is 50% or more (including 100%), and the autotempered martensite contained in the martensite phase is 85% or more (including 100%) There is a high-strength hot-dip galvanized steel sheet in which the ferrite phase from the surface layer to the plate thickness direction of 10.0 ⁇ m is 10% or less in area ratio, and the average particle size of carbide dispersed in the autotempered marten
  • Cr 0.001% to 0.6%
  • Ni 0.001% to 0.08%
  • V 0.001% to 0.3%
  • Mo 0.001% to 0.3%
  • the high-strength hot-dip galvanized steel sheet according to the above [1] or [2] containing one or more of W: 0.001% to 0.2% and Hf: 0.001% to 0.3%.
  • the residence time in the temperature range from the Ac 3 point to the maximum temperature is 10 seconds or more
  • the average cooling rate from the Ac 3 point to 550 ° C is 5 ° C / s or more
  • the cooling stop temperature is (Ms point + 20 ° C) Cooling at a temperature of 550 ° C or lower and annealing (Ms point + 20 ° C) for a residence time in the temperature range of 550 ° C or higher and 10 seconds or more and 90 seconds or less, followed by plating Method for manufacturing a high strength galvanized steel sheet subjected to physical.
  • the Ms point is a value obtained by the following equation (1).
  • the composition of the plating layer formed in the plating treatment is mass%, Fe: 5.0-20.0%, Al: 0.001% -1.0%, Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr [5] or [6] above, containing one or more of Co, Ca, Cu, Li, Ti, Be, Bi, and REM in a total of 0% to 3.5%, the balance being Zn and inevitable impurities
  • the high-strength hot-dip galvanized steel sheet is a hot-dip galvanized steel sheet having a tensile strength (TS) of 980 MPa or more, which has been subjected to a hot-dip galvanizing treatment (GI), and further after the hot-dip galvanizing treatment. Any of those subjected to alloying treatment (GA) is targeted.
  • TS tensile strength
  • a high-strength hot-dip galvanized steel sheet having a tensile strength of 980 MPa or more and good bendability can be obtained.
  • the high-strength hot-dip galvanized steel sheet of the present invention has a tensile strength of 980 MPa or more and is excellent in bendability, so that it can be suitably used for the use of structural members of automobiles, reducing the weight of automobile parts and its reliability. The effect is remarkable, such as improving the property.
  • the preferred range of the yield ratio is 0.67 or more, more preferably 0.70 or more.
  • the tensile strength is preferably 1300 MPa or less from the viewpoint of achieving good ductility.
  • C 0.09% or more and 0.20% or less C has a hardenability that increases the hardness of martensite and suppresses ferrite transformation.
  • the C content needs to be 0.09% or more.
  • the C content exceeds 0.20%, the martensite transformation point is excessively lowered, and the target autotempered martensite is hardly generated. Therefore, the C content is 0.09% or more and 0.20% or less.
  • it is 0.10% or more and 0.16% or less.
  • Si Less than 0.50% Si is an element that contributes to high strength by solid solution strengthening. On the other hand, Si raises the transformation temperature from the ferrite phase to the austenite phase (transformation point (Ac 3 point)), making it difficult to remove the ferrite phase during annealing (that is, transformation from the ferrite phase to the austenite phase). Suppression). Moreover, since Si reduces the wettability between the plating and the steel sheet surface, it causes defects such as non-plating. In the present invention, the Si content is acceptable if it is in the range of less than 0.50%. Preferably it is less than 0.30%. Since 0.01% may inevitably be mixed in production, the lower limit is preferably 0.01%.
  • Mn 2.2% to 3.5% Mn contributes to high strength by solid solution strengthening, and also lowers the Ac 3 transformation point to make it easier to remove the ferrite phase during annealing (ie, suppressing transformation from the ferrite phase to the austenite phase) and cooling. Has the effect of suppressing the start of ferrite transformation. From this viewpoint, the Mn content is 2.2% or more. On the other hand, if the Mn content exceeds 3.5%, the Ms point is excessively lowered and it becomes difficult to generate autotempered martensite. Therefore, the upper limit of Mn is set to 3.5%. A preferable range of the Mn content is 2.3% or more and 3.1% or less.
  • P 0.03% or less
  • P is an element that has an adverse effect on bendability because it segregates at grain boundaries and becomes the starting point of cracking during bending. Therefore, it is preferable to reduce P as much as possible.
  • the P content is set to 0.03% or less. Preferably it is 0.02% or less.
  • the P content is preferably reduced as much as possible, but 0.002% may inevitably be mixed in production, so the lower limit is preferably 0.002%.
  • S 0.005% or less
  • S exists as an inclusion such as MnS in steel. This inclusion becomes wedge-shaped by hot rolling and cold rolling. In such a form, S tends to be a starting point for void formation and adversely affects impact resistance. Therefore, in the present invention, it is preferable to reduce the S content as much as possible, and it is 0.005% or less. Preferably it is 0.003% or less.
  • the S content is preferably reduced as much as possible, but 0.0002% may inevitably be mixed in production, so the lower limit is preferably 0.0002%.
  • Al 0.08% or less
  • the Al content is 0.08% or less.
  • the Al content is 0.08% or less.
  • it is 0.07% or less.
  • N 0.006% or less N binds to B, which is a hardenable element, and thereby loses the hardenability effect of B. Therefore, the N content is preferably reduced as much as possible, and the upper limit is set to 0.006%. Preferably it is 0.005% or less. The N content is preferably reduced as much as possible, but 0.001% may be inevitably mixed in production, so the lower limit is preferably 0.001%.
  • B 0.0002% or more and 0.0030% or less B segregates at the grain boundaries of austenite before transformation and has the effect of significantly delaying the nucleation of the ferrite phase, and has the effect of suppressing the formation of the ferrite phase. In order to acquire this effect, it is necessary to contain B 0.0002% or more. On the other hand, if the B content exceeds 0.0030%, not only the hardenability effect is saturated, but also the ductility is adversely affected. From the above, the B content is 0.0002% or more and 0.0030% or less. Desirably, it is 0.0003% or more and 0.0020% or less.
  • Ti and Nb 0.001% or more and 0.1% or less
  • 1 type or 2 types included Ti and Nb combine with N and have an effect of stably expressing the hardenability effect by B.
  • Ti and Nb are precipitated as fine carbides in a small amount, they are effective in increasing the strength.
  • Ti and Nb are produced as coarse carbides when contained in large amounts.
  • Coarse carbides serve as nucleation sites for the ferrite phase and facilitate the formation of the ferrite phase. From such a viewpoint, the contents of Ti and Nb are both 0.001% or more and 0.1% or less when they are contained.
  • Ti and Nb are 0.005% or more and 0.06% or less in total.
  • Cr 0.001% to 0.6%
  • Ni 0.001% to 0.08%
  • V 0.001% to 0.3%
  • Mo 0.001% to 0.3%
  • W 0.001% to 0.2%
  • Hf 0.001% or more Contains one or more of 0.3% or less Cr, Ni, V, Mo, W and Hf have an effect of delaying the start of ferrite transformation, and in addition to the effect of hardenability by B, it becomes easy to stably obtain a desired steel sheet structure.
  • the Cr content exceeds 0.6%
  • the plating property is adversely affected.
  • Ni, V, Mo, W and Hf exceed the above range, the hardenability effect is saturated.
  • REM lanthanoid element with atomic number 57 to 71
  • Mg and Ca spheroidize cementite precipitated in martensite and bainite and reduce stress concentration around the cementite.
  • the content of one or more of REM, Mg, and Ca exceeds 0.01% in total, the effect of changing the shape of cementite is saturated and the workability is adversely affected.
  • one or more of REM, Mg, and Ca is made 0.0002% or more and 0.01% or less in total.
  • one or more of REM, Mg, and Ca is 0.0005% or more and 0.005% or less in total.
  • Area ratio of ferrite phase less than 10% (including 0%)
  • the ferrite phase is a soft structure, and voids are easily generated at the interface with a high-hardness metal structure, which adversely affects bendability. Therefore, the area ratio of the ferrite phase should be reduced as much as possible. Therefore, the area ratio of the ferrite phase is less than 10% (including 0%). Preferably it is 5% or less.
  • the bainite phase has a lower hardness than the martensite phase that is not autotempered martensite, and even if the bainite phase is included, the bendability is not impaired.
  • the bainite phase exceeds 50%, the tensile strength is less than 980 MPa, so the bainite phase needs to be 50% or less. Preferably it is 40% or less.
  • the lower limit is preferably 10%.
  • Area ratio of martensite phase 50% or more (including 100%), area ratio of autotempered martensite contained in martensite phase: 85% or more (including 100%)
  • the lower limit of the area ratio of the martensite phase is 50%.
  • the hardness of the as-quenched martensite phase, in which no carbide is observed in the grains, is remarkably high and the bendability is poor. If a ferrite phase or a bainite phase is present around the martensite phase, a stress gradient is generated and the yield ratio is lowered. In order to prevent these, a tempering heating step (reheating after plating) is necessary.
  • the present invention is characterized in that a tempering heating step is not required. That is, it is characterized by utilizing an auto-tempered martensite phase that does not require a tempering heating step (reheating after applying a plating layer).
  • the autotempered martensite phase is a structure in which carbides are observed in the grains.
  • the area ratio of the autotempered martensite phase contained in the martensite phase (the ratio of the area ratio of the autotempered martensite phase to the area ratio of all martensite phases) 85% or more is necessary. 90% or more is a more preferable range.
  • the area ratio is 10% or less
  • the structure of the surface layer is important.
  • the structure is mainly composed of a high-hardness autotempered martensite phase and a bainite phase (in the case where the area ratio of the bainite phase is low, the autotempered martensite phase is the main component). Then, voids are easily generated at the interface between the autotempered martensite phase and the bainite phase and the ferrite phase. As a result, bendability deteriorates. Therefore, it is necessary to reduce the area ratio of the ferrite phase in the surface layer as much as possible.
  • the ferrite phase of the surface layer should be 10% or less in terms of area ratio.
  • the depth from the surface to the plate thickness direction of 10.0 ⁇ m is as follows.
  • the interface between the plating phase and the ground iron becomes unclear, so that it is difficult to define the interface itself.
  • the bendability is greatly influenced by the structure of the steel sheet surface layer, and it is necessary to control the ferrite area ratio within the above range. Therefore, the depth is 10.0 ⁇ m from the surface.
  • control in the annealing process is important to control the ferrite phase from the surface to the plate thickness direction of 10.0 ⁇ m.
  • the average particle size of the carbide dispersed in the autotempered martensite grains is 200 nm or less.
  • the carbides in the autotempered martensite grains are preferably fine, and the fine particles in the autotempered martensite grains are fine. It is preferable to disperse the carbide.
  • the dispersion in this case is a state in which cementite is precipitated. Steel with excellent strength and ductility can be obtained by the precipitation of fine carbides in the autotempered martensite grains.
  • the carbide at this time is Fe-based carbide (cementite or ⁇ carbide). If the average particle size is 200 nm or less, the tensile strength of 980 MPa or more required in the present invention can be easily obtained.
  • the upper limit of the average particle size of the carbide dispersed in the autotempered martensite grains is 200 nm. Preferably it is 100 nm or less.
  • the lower limit of the average particle diameter of the carbide is preferably 10 nm or more in consideration of the case where the Ms point is low.
  • tissue can be obtained by controlling preheating process conditions and annealing conditions among the manufacturing methods mentioned later. In particular, by setting the residence time in the temperature range of (Ms point + 20 ° C) to less than 550 ° C to 10 seconds to 90 seconds, autotempered martensite contained in the martensite phase is 85% or more in area ratio ( 100% included). Moreover, the said structure
  • the high-strength hot-dip galvanized steel sheet of the present invention heats a steel material (steel slab) having the above-described composition at a temperature of 1100 ° C. or higher and 1350 ° C. or lower, and then performs hot rolling to a finish rolling temperature of 800 ° C. or higher.
  • the residence time in the temperature range from the point to the maximum temperature is 10 seconds or more
  • the average cooling rate from the Ac 3 point to 550 ° C is 5 ° C / s or more
  • the cooling stop temperature is (Ms point + 20 ° C) or more 550
  • Cooling is performed at a temperature lower than °C
  • an annealing treatment is performed so that the residence time in the temperature range from (Ms point + 20 °C) to less than 550 °C is 10 seconds to 90 seconds.
  • It can be prepared by subjecting the Kki process. That is, a steel material (steel slab) having the above-described composition is heated at a temperature of 1100 ° C. or higher and 1350 ° C.
  • a hot-rolling step, a cold-rolling step of cold rolling the hot-rolled steel plate obtained in the hot-rolling step, and a cold-rolled steel plate obtained in the cold-rolling step are at least Ac 3 points at a dew point of -20 ° C or lower.
  • Preheat treatment that heats to the highest temperature and stays in the temperature range from the Ac 3 point to the highest temperature for 30 seconds or more, and cools at an average cooling rate from the Ac 3 point to 550 ° C at 3 ° C / s or more.
  • the Ac 3 point is a value obtained from a transformation expansion curve obtained at an average heating rate of 3 ° C./s using a thermal expansion measuring device.
  • the method for melting steel is not particularly limited, and a known melting method such as a converter or an electric furnace can be employed. Further, secondary refining may be performed in a vacuum degassing furnace. Thereafter, the slab (steel material) is preferably formed by a continuous casting method from the viewpoint of productivity and quality, but the slab may be formed by a known casting method such as an ingot-bundling rolling method or a thin slab continuous casting method. .
  • Heating temperature of steel material 1100 ° C. or higher and 1350 ° C. or lower
  • the heating temperature is set to 1100 ° C or higher and 1350 ° C or lower. Preferably they are 1150 degreeC or more and 1300 degrees C or less.
  • the steel material when hot rolling the steel material, if the steel material after casting is in the temperature range of 1100 ° C or higher and 1350 ° C or lower, or if the carbide of the steel material is dissolved, the steel material is heated. Direct rolling may be performed without any problem.
  • the rough rolling conditions are not particularly limited.
  • Finishing rolling temperature 800 ° C or more
  • the finish rolling temperature is 800 ° C. or higher.
  • the finish rolling temperature is preferably 950 ° C. or less from the viewpoint of suppressing the occurrence of scale defects.
  • Winding temperature 560 ° C or less
  • the winding temperature needs to be 560 ° C. or less.
  • the coiling temperature is 350 ° C. or higher due to production line restrictions.
  • Cold rolling In order to obtain a desired plate thickness, it is necessary to perform cold rolling. Although there is no restriction
  • Preheating treatment cooled at 3 ° C / s or more since a ferrite phase is partially formed when decarburized, cracks occur at the boundary between ferrite and martensite, resulting in a decrease in bendability. To do. Therefore, it is necessary to set the dew point to ⁇ 20 ° C. or lower in the preheating step. Preferably it is -30 degrees C or less. However, the dew point is preferably ⁇ 50 ° C. or higher due to equipment restrictions.
  • the purpose of the preheating step is to suppress the uneven distribution of elements inside the steel plate. By suppressing the uneven distribution of elements inside the steel sheet, it is possible to form a uniform structure while suppressing the formation of ferrite phases in the steel sheet surface layer.
  • the residence time in the temperature range from the Ac 3 point to the maximum temperature must be 30 seconds or more.
  • the residence time in the temperature range from the Ac 3 point + 20 ° C. to the maximum temperature is 50 seconds or more. If the cumulative holding time does not reach 30 seconds by one heating, it is sufficient to perform two or more heating, that is, two or more sheets passing through the continuous annealing line. Further, from the viewpoint of productivity, the residence time is preferably 300 seconds or less.
  • the maximum temperature is at least the Ac 3 point, and preferably the maximum temperature is at the Ac 3 point to the Ac 3 point + 50 ° C or less. is there.
  • the cooling process it is necessary to suppress the distribution of elements accompanying the ferrite transformation. Therefore, it is necessary to cool in a range where the ferrite transformation is not started. Therefore, since in the present invention steel can be completed cooling without starting the ferrite transformation when the average cooling rate from Ac 3 point to 550 ° C. is 3 ° C. / s or higher, from the Ac 3 point to 550 ° C.
  • the average cooling rate is 3 ° C / s or more.
  • the average cooling rate is preferably 50 ° C./s or less because of equipment restrictions.
  • the average cooling rate from Ac 3 point to 550 ° C. Cooling is performed at 5 ° C / s or more and the cooling stop temperature is (Ms point + 20 ° C) or more and less than 550 ° C, and the residence time in the temperature range (Ms point + 20 ° C) or more and less than 550 ° C is 10 seconds or more and 90 seconds or less
  • Anustenite single phase is important in annealing processes where the dew point of -30 ° C or lower is heated to the Ac 3 point or higher and the maximum temperature reached, and the residence time in the temperature range from the Ac 3 point to the maximum temperature is 10 seconds or longer.
  • the dew point needs to be ⁇ 30 ° C. or lower in order to suppress changes in the structure of the surface layer. Preferably it is -35 degrees C or less. Note that the dew point is preferably ⁇ 50 ° C. or higher due to equipment restrictions of the annealing furnace.
  • the element distribution inside the steel plate is close to uniform, so in this annealing process, a uniform structure can be obtained if the residence time in the temperature range from the Ac 3 point to the maximum temperature is 10 seconds or more. It is also important to bring the transformation from the ferrite phase to the austenite phase close to completion.
  • the total amount of heat energy given to the steel sheet at the transformation completion temperature (Ac 3 points) from the ferrite phase to the austenite phase becomes important.
  • the number of Ac is 3 or more
  • ferrite grains having a nano-order particle size remain due to the influence of element distribution.
  • the residence time is preferably 50 seconds or less.
  • the maximum temperature in order to control the residence time of the temperature range of from Ac 3 point to a maximum ultimate temperature must be Ac 3 points or more, preferably the maximum temperature is Ac 3 point or more Ac 3 point + 50 It is below °C.
  • the average cooling rate is preferably 50 ° C./s or less because of equipment restrictions.
  • the softening of the austenite phase is preferably maintained at a high temperature for a long time.
  • an undesired structure such as a ferrite phase or a bainite phase is formed, it is necessary to hold at the most effective temperature and time.
  • the following formula (1) is the martensitic transformation start temperature (Ms point) considering the local region of the untransformed austenite phase.
  • [% C] and [% Mn] are C content and Mn content, respectively.
  • V f is the area ratio of the ferrite phase.
  • Coefficients related to [% C] and [% Mn] represent the slope at which the Ms point decreases due to the amount of C or Mn elements concentrated in the austenite phase due to the formation of the ferrite phase.
  • the austenite phase is not softened efficiently in the temperature range below Ms + 20 ° C calculated from the above equation (1).
  • the cooling stop temperature after forced cooling is (Ms point + 20 ° C) or more and less than 550 ° C.
  • the residence time in this temperature range is 10 seconds or more in order to soften the austenite phase.
  • the residence time exceeds 90 seconds, the bainite phase is excessively generated.
  • the residence time in the temperature range of (Ms point + 20 ° C) or higher and lower than 550 ° C is 10 seconds or longer and 90 seconds or shorter.
  • the relationship between the cooling stop temperature and the ferrite area ratio is investigated in advance in the laboratory, and the Ms point is calculated from the ferrite area ratio. Further, since autotempered martensite causes martensitic transformation at a high temperature and generates carbides in the cooling process, the Ms point is desirably as high as possible, and the Ms point is preferably 350 ° C. or higher.
  • the high-strength hot-dip galvanized steel sheet of the present invention is manufactured.
  • the high-strength hot-dip galvanized steel sheet of the present invention does not affect the material depending on the plating treatment or the composition of the plating bath, so the plating treatment may be either hot-dip galvanizing treatment or alloyed hot-dip galvanizing treatment. Is also applicable.
  • the plating bath composition is Fe: 5.0-20.0%, Al: 0.001% -1.0%, Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, It is preferable that one or more of Be, Bi, and REM is contained in a total of 0% to 3.5%, with the balance being Zn and inevitable impurities.
  • the high-strength hot-dip galvanized steel sheet of the present invention is mass%, Fe: 5.0-20.0%, Al: 0.001% -1.0%, Pb, Sb, Si Contains 1% or more of Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, REM in total of 0% to 3.5%, the balance being Zn and inevitable impurities It will have the plating layer which consists of.
  • a high-strength galvanized steel sheet manufactured by electrogalvanizing treatment satisfies the component composition and structure of the present invention, so that the tensile strength is 980 MPa or more (preferably 980 MPa or more and 1300 MPa or less) and good. There is an effect that it has a good bendability.
  • a steel material with a thickness of 250 mm having the composition shown in Table 1 is used as a hot-rolled steel sheet under the hot-rolling conditions shown in Table 2 (Table 2-1 and Table 2-2 are combined into Table 2). Cold rolling with a hot rolling ratio of 30% to 80% was performed. Next, a preheating step was performed under the conditions shown in Table 2, and hot dip galvanized steel sheets (“GI material” and “GA material”) were manufactured in the continuous annealing hot dip galvanizing line under the conditions shown in Table 2. The Ac 3 point was obtained from the transformation expansion curve obtained at an average heating rate of 3 ° C./s using a thermal expansion measuring device.
  • the temperature of the plating bath immersed in the continuous annealing hot dip galvanizing line (plating composition: Zn-0.13% by mass Al) is 460 ° C, and the coating weight is 45 to 65g / m 2 per side for both GI and GA materials.
  • the amount of Fe contained in the plating layer was in the range of 6 to 14%.
  • Specimens were collected from the hot dip galvanized steel sheet obtained as described above, and the structure was observed by the following method to evaluate the performance.
  • the area ratio of each phase was evaluated by the following method. A section parallel to the rolling direction was cut from the steel plate so that the observation surface was observed, and the central portion of the plate thickness was corroded with 1% nital, and was magnified 2000 times with a scanning electron microscope and photographed for 10 fields of view.
  • the ferrite phase is a structure having a form in which corrosion marks and cementite are not observed in the grains
  • the bainite phase is a structure in which large carbides are recognized in the grains compared to the corrosion marks and autotempered martensite.
  • the martensite phase has a structure in which no carbide is observed in the grains and is observed with white contrast
  • the autotempered martensite is a structure in which carbide is observed in the grains with white contrast.
  • FIG. 1 A typical example of an organization is shown in FIG.
  • the bainite phase, the bainite phase, and the martensite phase were separated from each other by image analysis, and each structure was determined by the area ratio with respect to the observation field.
  • To measure the particle size of the carbide dispersed in the autotempered martensite grain we photographed with a transmission electron microscope at a magnification of 135,000 times or more, obtained the area of each carbide by image analysis, and equivalent circle diameter equivalent to that area The average value of equivalent circle diameters for 300 or more carbides was determined as the average particle diameter of the carbides.
  • the structure of the surface of the steel sheet is the surface area of the ferrite phase from the surface layer to 10.0 ⁇ m, after the plated layer is peeled off by pickling the plated steel sheet, then magnified 2000 times with a scanning electron microscope and taken for 10 fields of view. The rate was determined.

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Abstract

La présente invention concerne une tôle d'acier de haute résistance galvanisée par immersion à chaud dont la résistance à la traction est supérieure ou égale à 980 MPa et qui possède d'excellentes propriétés de flexion, et un procédé de fabrication correspondant. Les teneurs contenues dans la tôle d'acier sont, en % en masse, C : de 0,09 à 0,20 %, Si : inférieure à 0,50 %, Mn : de 2,2 à 3,5 %, P : inférieure ou égale à 0,03 %, S : inférieure ou égale à 0,005 %, Al : inférieure ou égale à 0,08 %, N : inférieure ou égale à 0,006 %, et B : de 0,0002 à 0,0030 %, le complément étant du Fe et d'inévitables impuretés. En rapport surfacique, la phase ferrite de la composition est inférieure à 10 % (y compris 0 %), la phase bainite est inférieure ou égale à 50 % (y compris 0 %), la phase martensite est supérieure ou égale à 50 % (incluant 100 %), et la martensite auto-trempée contenue dans ladite phase martensite est supérieure ou égale à 85 % (y compris 100 %). La phase ferrite jusqu'à 10 μm à partir de la surface dans la direction de l'épaisseur de la plaque représente une valeur inférieure ou égale à 10 % en rapport surfacique. Le diamètre moyen des particules de carbure dispersées au sein des particules de martensite auto-trempée mentionnée ci-dessus est inférieur ou égal à 200 nm.
PCT/JP2015/003846 2014-12-22 2015-07-30 Tôle d'acier de haute résistance galvanisée par immersion à chaud et son procédé de fabrication Ceased WO2016103535A1 (fr)

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JP7389322B2 (ja) 2019-08-20 2023-11-30 日本製鉄株式会社 薄鋼板及びその製造方法
JP2021031703A (ja) * 2019-08-20 2021-03-01 日本製鉄株式会社 薄鋼板及びその製造方法
JP2023505693A (ja) * 2019-12-13 2023-02-10 アルセロールミタル 熱処理された冷間圧延鋼板及びその製造方法
JP2023506477A (ja) * 2019-12-13 2023-02-16 アルセロールミタル 熱処理された冷間圧延鋼板及びその製造方法
JP2024138480A (ja) * 2019-12-13 2024-10-08 アルセロールミタル 熱処理された冷間圧延鋼板及びその製造方法
JP2024153872A (ja) * 2019-12-13 2024-10-29 アルセロールミタル 熱処理された冷間圧延鋼板及びその製造方法
JP2023508240A (ja) * 2020-03-02 2023-03-01 アルセロールミタル 高強度冷間圧延合金化溶融亜鉛めっき鋼板及びその製造方法
JP7488351B2 (ja) 2020-03-02 2024-05-21 アルセロールミタル 高強度冷間圧延合金化溶融亜鉛めっき鋼板及びその製造方法

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CN107208205A (zh) 2017-09-26
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