EP2554699B1 - Tôle d'acier présentant une résistance à la traction élevée et une meilleure ductilité et procédé de fabrication de cette dernière - Google Patents

Tôle d'acier présentant une résistance à la traction élevée et une meilleure ductilité et procédé de fabrication de cette dernière Download PDF

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Publication number
EP2554699B1
EP2554699B1 EP11762477.5A EP11762477A EP2554699B1 EP 2554699 B1 EP2554699 B1 EP 2554699B1 EP 11762477 A EP11762477 A EP 11762477A EP 2554699 B1 EP2554699 B1 EP 2554699B1
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Prior art keywords
steel sheet
steel
less
temperature
recrystallized
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EP11762477.5A
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German (de)
English (en)
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EP2554699A4 (fr
EP2554699A1 (fr
Inventor
Takashi Kobayashi
Yoshimasa Funakawa
Tetsuya Mega
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JFE Steel Corp
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JFE Steel Corp
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Classifications

    • 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
    • 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
    • C22C38/04—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
    • 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
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a high strength steel sheet used in industrial fields such as transport machinery, for example, automobiles.
  • the invention relates to a high strength steel sheet having excellent ductility with a tensile strength (TS) of 700 to 900 MPa, and a method for manufacturing the same.
  • TS tensile strength
  • patent document 1 discloses a process for manufacturing high strength hot rolled steel sheets for automobile parts having excellent formability, in which a steel slab that has a chemical composition represented by, in terms of % by weight, C: not more than 1.0%, Si: 0.01 to 2.50%, Mn: 10 to 30%, sol.
  • Al 0.001 to 0.10%, P: not more than 0.05%, S: not more than 0.05%, and iron and inevitable impurities: balance, is heated to 1100°C or above, thereafter continuously hot finish rolled in such a manner that the total reduction in rough rolling and finish rolling is not less than 90%, the finishing temperature is not less than 800°C and the final sheet thickness is 1.1 to 5.0 mm, subsequently cooled to not more than 650°C at a cooling rate of 10 to 100°C/s, and thereafter coiled.
  • Patent document 2 discloses high strength lightweight steel strips or steel sheets with excellent cold formability containing, in terms of % by mass, C: not more than 1.00%, Mn: 7.00 to 30.00%, Al: 1.00 to 10.00%, Si: above 2.50% to not more than 8.00%, Al + Si: above 3.50% to not more than 12.00% and B: above 0.00% to less than 0.01%, and optionally containing Ni: less than 8.00%, Cu: less than 3.00%, N: less than 0.60%, Nb: less than 0.30%, Ti: less than 0.30%, V: less than 0.30% and P: less than 0.01%.
  • Patent document 3 discloses Fe-C-Mn based austenitic hot rolled steel sheets which contain, in terms of % by weight, C: 0.5 to 0.7%, Mn: 17 to 24%, Si: not more than 3%, Al: not more than 0.050%, S: not more than 0.030%, P: not more than 0.08% and N: not more than 0.1%, optionally together with one or more elements selected from Cr: not more than 1%, Mo: not more than 0.40%, Ni: not more than 1%, Cu: not more than 5%, Ti: not more than 0.50%, Nb: not more than 0.50% and V: not more than 0.50%, the balance being represented by Fe and inevitable impurities, and in which the recrystallization fraction is greater than 75%, the surface fraction of precipitated carbides is less than 1.5% and the average austenite grain diameter is less than 18 ⁇ m, the steel sheets having TS of greater than 900 MPa and TS x El (El: break elongation) of greater than 45000 MPa
  • Patent document 4 discloses a method for manufacturing high manganese nonmagnetic steel having excellent local deformability, in which a steel ingot or a steel slab that contains C: 0.15 to 0.70 wt%, Si: 0.10 to 3.00 wt%, Mn: 12 to 30 wt%, Ti: 0.01 to 0.10 wt%, and Fe and inevitable impurities: balance, and has C and Mn contents satisfying 60 x C wt% + Mn wt% ⁇ 36 wt% and a cleanliness of not more than 0.03% with respect to the content of nonmetallic inclusions is heated to 1050 to 1250°C and thereafter hot rolled at a finishing temperature of 900°C.
  • US 3 170 824 discloses a high manganese-nickel steel having good yield and tensile strengths as well as a good metal toughness.
  • the austenitic high manganese steel sheets disclosed in patent documents 1 to 4 have a problem in that a so-called plasticity instability phenomenon in which a work hardening behavior is destabilized in a highly distorted region is apt to occur so that press-forming the steel sheet tends to result in sudden breakage without giving rise to necking.
  • the present inventors carried out studies in order to achieve the above object, thus finding the following.
  • the present invention has been made on the basis of the above finding.
  • the invention provides a high strength steel sheet having excellent ductility which has a chemical composition according to claim 1.
  • the high strength steel sheet according to the present invention may be manufactured by reheating a steel slab having the above chemical composition to a heating temperature of 1100 to 1300°C, then hot rolling the steel slab to a hot rolled steel sheet at a finishing temperature of not less than 800°C, cooling the hot rolled steel sheet to at least 600°C in such a manner that the cooling rate is not less than 20°C/s in the temperature range of 800°C or less, and coiling the steel sheet at a coiling temperature of not more than 600°C.
  • scales may be removed and the steel sheet may be thereafter annealed at an annealing temperature of 750 to 1050°C and cooled in such a manner that the cooling rate in the range of temperatures from the annealing temperature to at least 450°C is not less than 10°C/s.
  • scales may be removed after coiling, and the steel may be thereafter cold rolled, annealed at an annealing temperature of 750 to 1050°C and cooled in such a manner that the cooling rate in the range of temperatures from the annealing temperature to at least 450°C is not less than 10°C/s.
  • the high strength steel sheet according to the invention is a steel sheet that has been hot rolled (hereinafter, steel sheet as hot rolled), a steel sheet resulting from annealing of the steel sheet as hot rolled, or a steel sheet resulting from cold rolling and subsequent annealing of the steel sheet as hot rolled.
  • the present invention allows for the manufacturing of high strength steel sheets having excellent ductility which can avoid sudden breakage during press forming and have TS of 700 to 900 MPa.
  • the inventive high strength steel sheet has an excellent balance between strength and ductility and thus can be used for the fabrication of parts which are difficult to be formed.
  • the high strength steel sheet of the invention is highly suited for the weight reduction of automobile bodies.
  • the high strength steel sheet having excellent ductility according to the present invention, and a method for manufacturing such steel sheets will be described in detail hereinbelow.
  • the percentages "%” indicating the contents of components mean “% by mass” unless otherwise mentioned.
  • Carbon is an essential element for the stabilization of austenite phase and plays a major role in increasing the tensile strength of steel. If the C content is less than 0.5%, the stabilization of austenite phase is insufficient and excellent ductility cannot be obtained. On the other hand, a C content in excess of 1.5% causes the precipitation of carbides which lowers ductility. Thus, the C content is 0.5 to 1.5%, and preferably 0.5 to 1.0%.
  • Silicon is an element that can be added for the purpose of deoxidation of steel.
  • adding an excessive amount of silicon which brings about a Si content in the steel exceeding 0.1% results in a saturation of the deoxidation effect as well as an increase in the amounts of internal defects and surface defects due to the increase of inclusions formed.
  • the Si content is not more than 0.1%.
  • the Si content is preferably 0.01 to 0.1%.
  • the Mn content is 10 to 25%, and preferably 15 to 25%.
  • the present inventors have studied the relationship between the stabilization of austenite phase and material properties, in particular the TS x El balance.
  • the present inventors have found that the TS x El balance becomes particularly excellent when the C and Mn contents are within the inventive ranges and when the C content and the Mn content satisfy Expression (1).
  • the P content exceeds 0.1%, steel toughness is lowered.
  • the P content is not more than 0.1%, and preferably not more than 0.05%.
  • the S content exceeds 0.05%, hot processability of steel is lowered.
  • the S content is not more than 0.05%, preferably not more than 0.02%, and more preferably not more than 0.01%.
  • Aluminum is an element that can be added for the purpose of deoxidation of steel. However, adding an excessive amount of aluminum which brings about an Al content in the steel exceeding 0.1% results in a saturation of the deoxidation effect as well as an increase in the amounts of internal defects and surface defects due to the increase of inclusions formed. Thus, the Al content is not more than 0.1%. In order to obtain the deoxidation effect sufficiently, the Al content is preferably 0.01 to 0.1%.
  • Nickel is the most important element in the present invention. Nickel has an effect of increasing the stacking fault energy of steel so as to stably produce the twinning induced plasticity effect, thus increasing ductility. In particular, this element is effective for suppressing the occurrence of plasticity instability in a highly distorted region as well as for increasing 1-E1 of austenitic high manganese steel sheets. In order to obtain these effects sufficiently, it is necessary that the Ni content be not less than 3.0%. Adding nickel to a Ni content in excess of 8.0% results in a saturation of these effects and an increase in production costs. Thus, the Ni content is 3.0 to 8.0%, and preferably 3.0 to 6.0%.
  • Molybdenum retards the recrystallization of steel and produces an austenite grain refinement effect, thereby contributing to the increase in tensile strength of steel.
  • the Mo content is preferably not less than 0.01%. If the Mo content exceeds 0.1%, however, the tensile strength TS becomes excessively high in excess of 900 MPa and the ductility is markedly deteriorated. Thus, the Mo content is not more than 0.1%, and preferably not more than 0.05%.
  • the N content exceeds 0.01%, steel ductility is lowered.
  • the N content is not more than 0.01%, and preferably not more than 0.005%.
  • the balance is represented by Fe and inevitable impurities.
  • the high strength steel sheet of the invention has a microstructure formed of recrystallized austenite grains with an average grain diameter of 5 to 30 ⁇ m or further has another microstructure at an area ratio of not more than 1%.
  • the microstructure needs to be an austenite single phase in order to achieve high ductility utilizing the twinning induced plasticity of the austenite phase.
  • the austenite grains need to be recrystallized grains in which the internal strain energy has been sufficiently released.
  • the average grain diameter of the austenite grains in the inventive high strength steel sheet is not less than 5 ⁇ m, and preferably not less than 10 ⁇ m. If the average grain diameter is in excess of 30 ⁇ m, it becomes difficult to obtain desired TS. Thus, the average grain diameter of the recrystallized austenite grains is not more than 30 ⁇ m.
  • microstructures other than the recrystallized austenite grains such as iron carbides and martensite phases are sometimes formed depending on the cooling rate after hot rolling or the cooling rate after annealing.
  • the formation of such other microstructures be suppressed minimally.
  • the object of the invention is not deteriorated as long as the area ratio of such other microstructures relative to all the microstructures is about 1% or less.
  • the inventive high strength steel sheet has a microstructure formed of recrystallized austenite grains with an average grain diameter of 5 to 30 ⁇ m or further has another microstructure such as iron carbide or martensite phase at an area ratio of not more than 1%.
  • the high strength steel sheet of the invention includes a microstructure in which recrystallized austenite grains have an average grain diameter of 5 to 30 ⁇ m and the recrystallized austenite grains have an area ratio of not less than 99% relative to all the microstructures in the steel sheet.
  • the average grain diameter of the recrystallized austenite grains was determined by taking SEM images of a microstructure that was located at 1/4 of the sheet thickness in a cross section parallel to the rolling direction of the steel sheet at a 1000x to 5000x magnification for several fields of view, and analyzing the images while performing phase identification by EBSD analysis. Whether the grains were recrystallized grains was judged based on whether or not the aspect ratio of the crystal grain shape was less than 2, and the judgment was verified while considering the estimated amount of strain in the grains obtained by EBSD analysis.
  • inventive steel sheets Preferred conditions for manufacturing the inventive steel sheets will be described below. However, the methods for manufacturing the inventive high strength steel sheets are not limited to those methods described below.
  • Heating temperature for steel slab 1100 to 1300°C
  • the heating temperature for a steel slab exceeds 1300°C, hot processability is lowered and an increased amount of energy is incurred to perform heating. On the other hand, heating at a temperature less than 1100°C results in an increase in the load incurred during hot rolling.
  • the heating temperature for a steel slab is 1100 to 1300°C, and preferably 1150 to 1250°C.
  • a steel slab that has been cooled to room temperature may be reheated or a steel slab that is being cooled after casting and still has a high temperature may be heated supplementarily or kept at such a high temperature.
  • Finishing hot rolling temperature not less than 800°C
  • finishing hot rolling temperature is less than 800°C, recrystallization and grain growth do not proceed sufficiently and grains tend to remain unrecrystallized in the resultant hot rolled steel sheet. Further, such a low finishing hot rolling temperature causes an increase in the rolling load in the case where the steel sheet is cold rolled afterward.
  • the finishing hot rolling temperature is not less than 800°C, and preferably not less than 850°C.
  • a finishing temperature exceeding 1050°C tends to cause the crystal grains to become excessively coarse, often resulting in decreases in strength and ductility.
  • the finishing temperature is desirably not more than 1050°C.
  • the steel sheet that is being rolled may be supplementarily heated using a heating device such as an edge heater or a bar heater.
  • Cooling rate after hot rolling not less than 20°C/s for temperatures in the range of 800°C or less
  • cooling after hot rolling is performed at a cooling rate of less than 20°C/s for temperatures of 800°C or less, iron carbides are precipitated during cooling so as to decrease ductility.
  • the hot rolled steel sheet be cooled to at least 600°C in such a manner that the steel sheet is cooled at a cooling rate of not less than 20°C/s in the temperature range of 800°C or less.
  • the rate of cooling after hot rolling is more than 100°C/s, recrystallization does not complete at times.
  • the rate of cooling after hot rolling is preferably not more than 100°C/s.
  • finishing temperature is above 800°C
  • natural cooling air cooling
  • the steel sheet is cooled to at least 600°C in such a manner that the steel sheet is cooled at a cooling rate of not less than 20°C/s in the temperature range of 800°C or less.
  • Coiling temperature not more than 600°C
  • the coiling temperature is in excess of 600°C, iron carbides are formed during gradual cooling after coiling, thereby decreasing ductility.
  • the coiling temperature is not more than 600°C, and preferably not more than 550°C.
  • the steel sheet as hot rolled that is manufactured as described above may be directly used as the inventive high strength steel sheet.
  • the steel sheet as hot rolled is descaled or after the steel sheet as hot rolled is descaled and thereafter cold rolled, the steel sheet may be further annealed under the following annealing conditions.
  • the removal of scales may be carried out by a common procedure such as pickling.
  • Annealing conditions annealing temperature: 750 to 1050°C, cooling rate in the range of temperatures from the annealing temperature to at least 450°C: not less than 10°C/s
  • the steel sheet as hot rolled may be annealed at an annealing temperature of 750 to 1050°C in order to promote grain growth. Annealing is more preferably carried out at an annealing temperature of 800 to 1000°C.
  • the steel sheet as hot rolled is cold rolled into a desired steel sheet thickness and such a steel sheet is annealed
  • the annealing temperature is less than 750°C, recrystallization does not complete and sufficient ductility cannot be obtained.
  • an annealing temperature exceeding 1050°C may cause the crystal grains to become excessively coarse, often resulting in decreases in strength and ductility.
  • annealing is performed at an annealing temperature of 800 to 1000°C.
  • the cold rolling reduction is not particularly limited as long as a desired sheet thickness is obtained. However, the cold rolling reduction is desirably about 50 to 70% from the viewpoint of production efficiency.
  • cooling in such a manner that the cooling rate in the range of temperatures from the annealing temperature to at least 450°C is less than 10°C/s results in the formation of iron carbides and a consequent decrease in ductility.
  • the steel be cooled in such a manner that the cooling rate in the range of temperatures from the annealing temperature to at least 450°C is not less than 10°C/s.
  • the steel according to the invention may be produced by melting with a converter or an electric furnace.
  • the molten steel is formed into a slab by ingot making followed by slabbing, or by continuous casting. It is preferable to perform any of various preliminary treatments, secondary refining, slab surface conditioning and others in accordance with need.
  • annealing is preferably carried out with a continuous annealing facility.
  • the steel sheet as hot rolled or the annealed steel sheet may be subjected to any of various plating treatments without deteriorating the advantageous effects of the invention.
  • the steel sheet as hot rolled, the annealed steel sheet or the plated steel sheet may be temper rolled in order to correct the shape or control the surface roughness.
  • the inventive steel sheet may be subjected to any of various surface treatments such as painting and coating.
  • Steel slabs of steels A to K that had chemical compositions described in Table 1 were each hot rolled into a hot rolled steel sheet with a sheet thickness of 3 mm under hot rolling conditions described in Table 2. After scales were removed by pickling, some of the steel sheets were further annealed under annealing conditions described in Table 2, or were cold rolled at a cold rolling reduction described in Table 2 and thereafter annealed under annealing conditions described in Table 2. Thus, steel sheets as hot rolled, as well as hot rolled and annealed steel sheets and cold rolled and annealed steel sheets Nos. 1 to 20 were prepared.
  • the prepared steel sheets were analyzed in order to examine the microstructures by the aforementioned method, thus determining the phase configuration and the average grain diameter of recrystallized austenite grains.
  • the phase configuration indicates recrystallized austenite grains and another type of microstructure that was observed at an area ratio exceeding 1%, and also indicates recrystallized austenite grains alone when the area ratio of other microstructures was 1% or less.
  • a 13B test piece specified in JIS Z2201 was sampled along the rolling direction and was subjected to tensile test in accordance with the method described in JIS Z2241, thereby determining TS, El, 1-EL and TS x El.
  • the steel sheet was evaluated to be a high strength steel sheet having excellent ductility when TS x El thereof was 60 GPa ⁇ % or more,.
  • EX. 10 Recrystallized ⁇ 31 691 90.5 10.9 62.5 COMP.
  • EX. 11 Recrystallized ⁇ + unrecrystallized ⁇ 3 962 52.5 2.8 50.5 COMP.
  • EX. 12 Recrystallized ⁇ + iron carbide 13 835 64.3 5.1 53.7 COMP.
  • EX. 13 Recrystallized ⁇ 7 877 68.7 6.6 60.2 INV.
  • EX. 15 Recrystallized ⁇ 14 776 89.5 10.3 69.5 INV.
  • EX. 16 Recrystallized ⁇ 13 824 73.8 7.6 60.8 INV.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (4)

  1. Tôle d'acier de haute résistance ayant une excellente ductilité présentant une composition chimique représentée par, en termes de % en masse, C : de 0,5 à 1,5 %, Si : pas plus de 0,1 %, Mn : de 10 à 25 %, P : pas plus de 0,1 %, S : pas plus de 0,05 %, Al : pas plus de 0,1 %, Ni : de 3,0 à 8,0 %, Mo : pas plus de 0,1 %, N : pas plus de 0,01 %, et Fe et des impuretés inévitables : le reste, et présentant une microstructure comprenant une phase unique d'austénite recristallisée de 99 % ou plus d'austénite recristallisée formée de grains d'austénite recristallisée avec un diamètre moyen de grain de 5 à 30 µm et où le rapport des surfaces d'une autre microstructure n'est pas supérieur à 1 %.
  2. Procédé de fabrication d'une tôle d'acier de haute résistance présentant une excellente ductilité, comprenant le recuit d'une brame d'acier présentant la composition chimique selon la revendication 1 à une température de recuit de 1 100 à 1 300°C, le laminage à chaud de la brame d'acier jusqu'à l'obtention d'une tôle d'acier laminée à chaud à une température de finition non inférieure à 800°C, le refroidissement de la tôle d'acier laminée à chaud à au moins 600°C d'une manière telle que la vitesse de refroidissement ne soit pas inférieure à 20°C/s dans la plage des températures de 800°C ou moins, et le bobinage de la tôle d'acier à une température de bobinage non supérieure à 600°C.
  3. Procédé de fabrication d'une tôle d'acier de haute résistance présentant une excellente ductilité selon la revendication 2, comprenant en outre l'élimination de la calamine après le bobinage, le recuit de l'acier à une température de recuit de 750 à 1 050°C, et le refroidissement de l'acier d'une manière telle que la vitesse de refroidissement située dans la plage des températures allant de la température de recuit jusqu'à au moins 450°C ne soit pas inférieure à 10°C/s.
  4. Procédé de fabrication d'une tôle d'acier de haute résistance présentant une excellente ductilité selon la revendication 2, comprenant en outre l'élimination de la calamine après le bobinage, le laminage à froid de l'acier, le recuit de l'acier laminé à froid à une température de recuit de 750 à 1 050°C, et le refroidissement de l'acier d'une manière telle que la vitesse de refroidissement située dans la plage des températures allant de la température de recuit jusqu'à au moins 450°C ne soit pas inférieure à 10°C/s.
EP11762477.5A 2010-03-30 2011-02-25 Tôle d'acier présentant une résistance à la traction élevée et une meilleure ductilité et procédé de fabrication de cette dernière Not-in-force EP2554699B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2010077305A JP5003785B2 (ja) 2010-03-30 2010-03-30 延性に優れた高張力鋼板およびその製造方法
PCT/JP2011/055007 WO2011122237A1 (fr) 2010-03-30 2011-02-25 Tôle d'acier présentant une résistance à la traction élevée et une meilleure ductilité et procédé de fabrication de cette dernière

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EP2554699A1 EP2554699A1 (fr) 2013-02-06
EP2554699A4 EP2554699A4 (fr) 2015-07-08
EP2554699B1 true EP2554699B1 (fr) 2016-08-10

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EP (1) EP2554699B1 (fr)
JP (1) JP5003785B2 (fr)
KR (1) KR101287331B1 (fr)
CN (1) CN102822371B (fr)
WO (1) WO2011122237A1 (fr)

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US11959157B2 (en) 2018-08-03 2024-04-16 Jfe Steel Corporation High-Mn steel and method of producing same

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US20140261918A1 (en) * 2013-03-15 2014-09-18 Exxonmobil Research And Engineering Company Enhanced wear resistant steel and methods of making the same
KR101665801B1 (ko) 2014-12-23 2016-10-13 주식회사 포스코 도금 품질이 우수한 오스테나이트계 고강도 고망간 용융 알루미늄 도금강판 및 그의 제조방법
KR101665807B1 (ko) 2014-12-23 2016-10-13 주식회사 포스코 도금성이 우수한 오스테나이트계 고강도 고망간 용융 알루미늄 도금강판 및 그의 제조방법
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JP6590117B1 (ja) * 2017-12-07 2019-10-16 Ｊｆｅスチール株式会社 高Ｍｎ鋼およびその製造方法
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JP2011208226A (ja) 2011-10-20
JP5003785B2 (ja) 2012-08-15
EP2554699A4 (fr) 2015-07-08
KR101287331B1 (ko) 2013-07-23
CN102822371B (zh) 2015-05-20
EP2554699A1 (fr) 2013-02-06
CN102822371A (zh) 2012-12-12
KR20120113789A (ko) 2012-10-15

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