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WO2023022351A1 - Acier inoxydable austénitique et son procédé de fabrication - Google Patents

Acier inoxydable austénitique et son procédé de fabrication Download PDF

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Publication number
WO2023022351A1
WO2023022351A1 PCT/KR2022/008906 KR2022008906W WO2023022351A1 WO 2023022351 A1 WO2023022351 A1 WO 2023022351A1 KR 2022008906 W KR2022008906 W KR 2022008906W WO 2023022351 A1 WO2023022351 A1 WO 2023022351A1
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stainless steel
austenitic stainless
present
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Korean (ko)
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김상석
박미남
이재필
정일찬
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Posco Holdings Inc
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Posco Co Ltd
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Priority to JP2024506270A priority Critical patent/JP2024529999A/ja
Priority to EP22858593.1A priority patent/EP4361305A4/fr
Priority to US18/580,943 priority patent/US20240336989A1/en
Priority to CN202280055970.4A priority patent/CN117813413A/zh
Publication of WO2023022351A1 publication Critical patent/WO2023022351A1/fr
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • 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
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • 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 an austenitic stainless steel and a method for manufacturing the same, and more particularly, to ultra-fine-grained 304 series and 301 series austenitic stainless steel capable of realizing high strength and high ductility, and a method for manufacturing the same.
  • 304 series and 301 series general-purpose austenitic stainless steels are limited in their applicability to applications requiring high strength, such as structural materials, due to their low yield strength (200 to 350 MPa).
  • it is a common method to go through a temper rolling process, but it causes a cost increase problem.
  • the required properties of the 301 series 1/4H tempered materials require a yield strength of 500MPa or more, a tensile strength of 850MPa or more, and an elongation of 25% or more. Accordingly, in the present invention, high yield strength, tensile strength and excellent elongation are simultaneously achieved without temper rolling
  • a method for manufacturing ultra-fine 300 series stainless steel that can be realized has been proposed.
  • Ultra Fine Grain (UFG) materials have excellent strength-elongation balance, fatigue resistance, and etching processability.
  • UFG Ultra Fine Grain
  • SR Stress Relief
  • Patent Publication 2020-50940 it is proposed to perform heat treatment for a long time in the range of 600 to 700 ° C. for 48 hours or more in order to manufacture an average grain size of 10 ⁇ m or less for parts for nuclear power.
  • productivity is low to be implemented in an actual production line, and the manufacturing cost is increased due to a long heat treatment method.
  • the present invention 304 series, 301 series austenitic stainless steel sheet for the purpose of replacing tempered materials (especially 301 1/4H) for automobile exterior panels, building parts, automobile parts, etc. It is intended to provide an ultra-fine grain manufacturing technology that can be implemented.
  • the present invention focuses on low-cost component design and low-cost manufacturing technology to have high strength and high ductility in the thickness range to solve technical problems. wanted to solve it.
  • Ultra-fine grain realization technology in 300 series stainless steel generally transforms austenite phase into martensite phase through cold rolling, and implements ultra-fine grain through low-temperature annealing in a subsequent step.
  • the ultra-fine grain is implemented, it is not easy to express a material having excellent yield strength, tensile strength and elongation at the same time.
  • Ni content and Cr content are different within the range of 304 and 301 standards, and according to ASP (Austenitic Stability Parameter) value, the amount of martensite phase transformation according to cold working is different, and TRIP (Transformation Induced Plasticity) transformation behavior during tensile test This is different and the tensile curve characteristics change considerably.
  • ASP Austenitic Stability Parameter
  • Austenitic stainless steel in weight %, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Cu: 0.01 ⁇ 0.4, Mo: 0.01 ⁇ 0.2, Ni: 6 ⁇ 9%, Cr: 16 ⁇ 19%, N: 0.01 ⁇ 0.2%, including remaining Fe and unavoidable impurities, 551-462(C+N)-9.2Si-8.1Mn-13.7Cr- ASP (Austenitic Stability Parameter) value calculated as 29(Ni+Cu)-18.5Mo is 30 ⁇ 60, [100*N]/[Ni+Cu] value is more than 1.4, average grain size is less than 5 ⁇ m , The grain size fraction (%) of 5 ⁇ m or more is less than 10%.
  • the present invention satisfies the required characteristics (yield strength of 500 MPa or more, tensile strength of 850 MPa or more, and elongation of 25% or more) of the 301 series 1/4H tempered material having a thickness range of 0.4 to 2.0 mm, thereby replacing the 301 series 1/4H 300 It is possible to provide manufacturing technology for super-fine grain products.
  • Example 1 is an analysis of the TD (Transverse Direction) surface of the thickness center of the final cold-rolled product of Example 1 with a backscatter electron diffraction pattern analyzer (Electron BackScatter Diffraction, EBSD), and the crystal grains representing the crystal grain size of 5 ⁇ m or more are gray (gray) ), and is a diagram showing the fraction.
  • TD Transverse Direction
  • EBSD Backscatter electron diffraction pattern analyzer
  • Example 2 is a diagram showing the fraction of crystal grains representing a grain size of 5 ⁇ m or more by analyzing the TD plane of the thickness center of the final cold-rolled product of Example 3 with a backscatter electron diffraction pattern analyzer, and expressing them in gray .
  • FIG. 3 is a diagram showing the fraction of crystal grains representing a crystal grain size of 5 ⁇ m or more by analyzing the TD plane of the thickness center of the final cold-rolled product of Comparative Example 1 with a backscatter electron diffraction pattern analyzer, and expressing them in gray .
  • FIG. 4 is a diagram showing the fraction of crystal grains representing a crystal grain size of 5 ⁇ m or more by analyzing the TD plane of the thickness center of the final cold-rolled product of Comparative Example 2 with a backscatter electron diffraction pattern analyzer, and expressing them in gray .
  • Example 5 is a graph showing a stress-strain curve of Example 1.
  • Austenitic stainless steel in weight %, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Cu: 0.01 ⁇ 0.4, Mo: 0.01 ⁇ 0.2, Ni: 6 ⁇ 9%, Cr: 16 ⁇ 19%, N: 0.01 ⁇ 0.2%, including remaining Fe and unavoidable impurities, 551-462(C+N)-9.2Si-8.1Mn-13.7Cr- ASP (Austenitic Stability Parameter) value calculated as 29(Ni+Cu)-18.5Mo is 30 ⁇ 60, [100*N]/[Ni+Cu] value is more than 1.4, average grain size is less than 5 ⁇ m , The grain size fraction (%) of 5 ⁇ m or more is less than 10%.
  • Austenitic stainless steel in weight %, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Cu: 0.01 ⁇ 0.4, Mo: 0.01 ⁇ 0.2, Ni: 6 ⁇ 9%, Cr: 16 ⁇ 19%, N: 0.01 ⁇ 0.2%, including remaining Fe and unavoidable impurities, 551-462(C+N)-9.2Si-8.1Mn-13.7Cr- ASP (Austenitic Stability Parameter) value calculated as 29(Ni+Cu)-18.5Mo is 30 ⁇ 60, [100*N]/[Ni+Cu] value is more than 1.4, average grain size is less than 5 ⁇ m , The grain size fraction (%) of 5 ⁇ m or more is less than 10%.
  • the content of C (carbon) is 0.005 to 0.03% by weight.
  • C is an austenite phase stabilizing element.
  • C is added in an amount of 0.005% by weight or more.
  • the C content is limited to 0.03% by weight or less.
  • the content of Si (silicon) is 0.1 to 1% by weight.
  • Si is a component added as a deoxidizer during steelmaking, and when performing a bright annealing process, Si oxide is formed in the passivation film to improve corrosion resistance of the steel.
  • Si is added in an amount of 0.1% by weight or more.
  • the Si content is limited to 1.0% by weight or less in the present invention.
  • the content of Mn (manganese) is 0.1 to 2.0% by weight.
  • Mn is an austenite phase stabilizing element.
  • Mn is added in an amount of 0.1% by weight or more in the present invention.
  • the Mn content is limited to 2.0% by weight or less in the present invention.
  • Ni nickel
  • Ni is an austenite phase stabilizing element and has an effect of softening steel materials. Considering this, Ni is added in an amount of 6.0% by weight or more in the present invention. However, if the Ni content is excessive, there is a problem in that the cost increases, so the Ni content is limited to 9.0% by weight or less in the present invention.
  • the content of Cr (chromium) is 16.0 to 19.0% by weight.
  • Cr is a major element for improving the corrosion resistance of stainless steel.
  • Cr is added in an amount of 16.0% by weight or more.
  • the Cr content is limited to 19.0% by weight or less in the present invention.
  • the content of N (nitrogen) is 0.01 to 0.2% by weight.
  • N is an austenite phase stabilizing element and improves the strength of steel materials.
  • N may be added in an amount of 0.01% or more.
  • the N content is limited to 0.2% by weight or less.
  • the content of Cu (copper) is 0.01 to 0.4% by weight.
  • Cu is an austenite phase stabilizing element and may be added in an amount of 0.01% or more. However, if the Cu content is excessive, the corrosion resistance of the steel is lowered and the cost increases, so the Cu content is limited to 0.4% by weight or less in the present invention.
  • the content of Mo (molybdenum) is 0.01 to 0.2% by weight.
  • Mo has an effect of improving corrosion resistance and workability, it may be added in an amount of 0.01% or more. However, if the Mo content is excessive, there is a problem that the cost will increase, so the Mo content is limited to 0.2% by weight or less in the present invention.
  • the remaining component of the present invention is iron (Fe).
  • Fe iron
  • ASP Austenitic Stability Parameter
  • the [100 * N] / [Ni + Cu] value is 1.4 or more, and when it exceeds 1.4, the amount of dissolved nitrogen contributing to the yield strength is low, and the yield strength intended in the present invention is not satisfied.
  • the average grain size is less than 5 ⁇ m, the grain size fraction (%) of 5 ⁇ m or more is less than 10%, and outside the above range, the yield strength and tensile strength aimed at in the present invention are not satisfied.
  • the austenitic stainless steel may have a tensile strength of 850 MPa or more.
  • the austenitic stainless steel may have a yield strength of 500 MPa or more.
  • the austenitic stainless steel may have an elongation of 25% or more.
  • the average grain size is 5um or more, and the grain fraction of 5um or more is 10% or more, so that the yield strength and tensile strength aimed at in the present invention are not satisfied.
  • the cold reduction (%) value is less than 60%, the average grain size is 5um or more, and the grain fraction of 5um or more is 10% or more, so the yield strength intended in the present invention is not satisfied.
  • Table 1 shows the components of carbon, silicon, manganese, nickel, chromium, copper, and nitrogen in Examples and Comparative Examples of austenitic stainless steel, and the main component parameters ASP (Astenite Stability Parameter) value, [100 * N] / [ Ni + Cu] value, cold rolling rate (%) value, cold rolling annealing temperature (°C) [within 5 minutes of annealing time] value.
  • ASP Astenite Stability Parameter
  • Examples 1 to 6 all have ASP (Austenitic Stability Parameter) values calculated as 551-462 (C + N) -9.2Si-8.1Mn-13.7Cr-29 (Ni + Cu) -18.5Mo in the range of 30 to 60 While having, the [100 * N] / [Ni + Cu] value is 1.4 or more, the cold rolling ratio (%) value is 60% or more, and the cold annealing temperature (°C) value is in the range of 800 to 850.
  • ASP Austenitic Stability Parameter
  • the ASP (Austenitic Stability Parameter) value is outside the range of 30 to 60, the [100 * N] / [Ni + Cu] value is less than 1.4, or the cold rolling ratio (%) value is less than 60% Or, it indicates a case where the cold rolling annealing temperature (°C) value is out of the range of 800 to 850.
  • Table 2 shows the average grain size, crystal grain fraction (%) of 5 ⁇ m or less, and JIS13B tensile test piece analyzed by Electron BackScatter Diffraction (EBSD) on the TD (Transverse Direction) plane of the thickness center of the final cold-rolled product.
  • EBSD Electron BackScatter Diffraction
  • Examples 1 to 6 have an average grain size of less than 5 ⁇ m, and a crystal grain fraction (%) of 5 ⁇ m or more is less than 10%, and the ASP (Austenitic Stability Parameter) value is in the range of 30 to 60 and [100*N]/[Ni+Cu] value of 1.4 or more, finally required characteristics of 301 series 1/4H tempered material (yield strength of 500MPa or more, tensile strength of 850MPa or more, elongation of 25% or more) satisfies
  • Comparative Example 1 the cold-rolled annealing temperature value is outside the range of the present invention, the average grain size is 5um or more, and the grain fraction of 5um or more is 10% or more, so the yield strength and tensile strength aimed at in the present invention are not satisfied.
  • Comparative Example 2 Comparative Example 3, and Comparative Example 4, the ASP (Austenitic Stability Parameter) value was out of the range of the present invention, and TRIP (Transformation Induced Plasticity) transformation of the material did not occur well (work hardening did not occur well) during the tensile test. not) does not satisfy the tensile strength intended in the present invention.
  • ASP Austenitic Stability Parameter
  • Comparative Example 8 and Comparative Example 9 the ASP (Austenitic Stability Parameter) value and [100 * N] / [Ni + Cu] value were out of the scope of the present invention, and the average grain size was 5um or more, and the crystal grain fraction of 5um or more was 10 % or more, it does not satisfy the yield strength and tensile strength aimed at in the present invention.
  • the cold reduction (%) value was outside the range of the present invention, the average grain size was 5um or more, and the grain fraction of 5um or more was 10% or more, so that the yield strength aimed at in the present invention not satisfied
  • FIG. 5 to 8 are graphs showing stress-strain curves of Examples and Comparative Examples, FIG. 5 is a graph for Example 1, FIG. 6 is a graph for Comparative Example 1, and FIG. is a graph for Comparative Example 2, and FIG. 8 is a graph for Comparative Example 5. 5 to 8, it can be confirmed that the austenitic stainless steel according to one embodiment of the present invention has a relatively high stress change rate according to the degree of deformation, and thus can simultaneously satisfy high strength and high elongation compared to the comparative example. .
  • the present invention can replace 301 series 1/4H by satisfying the required properties (yield strength of 500 MPa or more, tensile strength of 850 MPa or more, elongation of 25% or more) of 301 series 1/4H tempered materials having a thickness range of 0.4 to 2.0 mm. It is possible to provide ultra-fine-grain stainless steel with industrial applicability.

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  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne un acier inoxydable austénitique comprenant, en % en poids, de 0,005 à 0,03 % de C, de 0,1 à 1 % de Si, de 0,1 à 2 % de Mn, de 0,01 à 0,4 % de Cu, de 0,01 à 0,2 % de Mo, de 6 à 9 % de Ni, de 16 à 19 % de Cr, de 0,01 à 0,2 % de N, et le reste étant du Fe et des impuretés inévitables, une valeur de paramètre de stabilité austénitique (ASP), telle que calculée par 551-462(C+N)-9,2Si-8,1Mn-13,7Cr-29 (Ni+Cu)-18,5Mo, étant de 30 à 60, une valeur [100*N]/[Ni+Cu] étant supérieure ou égale à 1,4, la taille moyenne des grains cristallins étant inférieure à 5 µm et la fraction (%) de grains cristallins ayant une taille supérieure ou égale à 5 µm étant inférieure à 10 %. La présente invention concerne un procédé de fabrication d'acier inoxydable austénitique, le procédé comprenant les étapes consistant à : fabriquer une brame par coulée continue d'acier inoxydable austénitique, l'acier inoxydable austénitique comprenant, en % en poids, de 0,005 à 0,03 % de C, de 0,1 à 1 % de Si, de 0,1 à 2 % de Mn, de 0,01 à 0,4 % de Cu, de 0,01 à 0,2 % de Mo, de 6 à 9 % de Ni, de 16 à 19 % de Cr, de 0,01 à 0,2 % de N, et le reste étant du Fe et des impuretés inévitables, une valeur de paramètre de stabilité austénitique (ASP), telle que calculée par 551-462(C+N)-9,2Si-8,1Mn-13,7 Cr-29(Ni+Cu)-18,5Mo, étant de 30 à 60, une valeur [100* ]/[Ni+Cu] étant supérieure ou égale à 1,4, la taille moyenne des grains cristallins étant inférieure à 5 µm et la fraction (%) de grains cristallins ayant une taille supérieure ou égale à 5 µm étant inférieure à 10 % ; laminer à chaud, recuire et décaper la brame, puis la laminer à froid à un taux de réduction à froid supérieur ou égal à 60 % ; ainsi que recuire à une température de recuit dans la plage de 800 à 850° C.
PCT/KR2022/008906 2021-08-18 2022-06-23 Acier inoxydable austénitique et son procédé de fabrication Ceased WO2023022351A1 (fr)

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JP2024506270A JP2024529999A (ja) 2021-08-18 2022-06-23 オーステナイト系ステンレス鋼及びその製造方法
EP22858593.1A EP4361305A4 (fr) 2021-08-18 2022-06-23 Acier inoxydable austénitique et son procédé de fabrication
US18/580,943 US20240336989A1 (en) 2021-08-18 2022-06-23 Austenitic stainless steel and method for manufacturing same
CN202280055970.4A CN117813413A (zh) 2021-08-18 2022-06-23 奥氏体系不锈钢及其制造方法

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EP4361305A1 (fr) 2024-05-01
US20240336989A1 (en) 2024-10-10

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