WO2022270814A1 - Acier inoxydable austénitique et son procédé de fabrication - Google Patents

Acier inoxydable austénitique et son procédé de fabrication Download PDF

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WO2022270814A1
WO2022270814A1 PCT/KR2022/008454 KR2022008454W WO2022270814A1 WO 2022270814 A1 WO2022270814 A1 WO 2022270814A1 KR 2022008454 W KR2022008454 W KR 2022008454W WO 2022270814 A1 WO2022270814 A1 WO 2022270814A1
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stainless steel
austenitic stainless
less
bent portion
comparative example
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PCT/KR2022/008454
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English (en)
Korean (ko)
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김상석
박미남
조기훈
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주식회사 포스코
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Priority to CN202280043970.2A priority Critical patent/CN117529571A/zh
Priority to EP22828661.3A priority patent/EP4343013A1/fr
Priority to JP2023575582A priority patent/JP2024522170A/ja
Publication of WO2022270814A1 publication Critical patent/WO2022270814A1/fr

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    • 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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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 having no surface cracks and excellent surface roughness at a bent portion and a manufacturing method thereof.
  • austenitic stainless steels are used for various purposes such as transportation parts and construction parts due to their excellent formability, work hardenability and weldability.
  • 304 series stainless steel or 301 series stainless steel has a yield strength of only 200 to 350 MPa, there is a limit to its application to structures. Therefore, in order to obtain a higher yield strength in general-purpose 300 series stainless steel, it is a common method to undergo a temper rolling process.
  • the method through the temper rolling process has a problem in that the elongation of the material is extremely inferior together with the cost increase problem.
  • Patent Document 0001 a method of performing long-term heat treatment in the range of 600 to 700 ° C. for 48 hours or more in order to produce an average grain size of 10 ⁇ m or less was proposed.
  • the method proposed in Patent Document 0001 has a problem in that productivity is low and manufacturing cost is increased to be implemented in an actual production line.
  • Patent Document 0001 Japanese Laid-open Patent No. 2020-050940 A (Publication date: April 02, 2020)
  • An object of the present invention for solving the above-mentioned problems is to propose a super-fine manufacturing technology that realizes bending formability and sound surface properties of the bent part, so that there is no surface crack in the bent part and an austenitic stainless steel with excellent surface roughness and It is to provide a manufacturing method.
  • Austenitic stainless steel according to an embodiment of the present invention, by weight%, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Ni: 6 ⁇ 12%, Cr: 16 ⁇ 20%, N: 0.01-0.2%, Nb: 0.25% or less, including the remaining Fe and unavoidable impurities, the average grain size (d) value of the center of the thickness is 5 ⁇ m or less, and in the bent area after the 180 ° bending experiment The measured martensite area fraction may be 10% or less.
  • the austenitic stainless steel according to an embodiment of the present invention may have a surface roughness of Ra of 0.5 ⁇ m or less and Rz of 3 ⁇ m or less of the bent portion.
  • the austenitic stainless steel according to an embodiment of the present invention may have a pitting potential value of 250 mV or more by a 3.5% NaCl solution at 30 °C.
  • the step of hot rolling the slab containing the remaining Fe and unavoidable impurities the step of cold rolling at room temperature and expressed by the following formula (1) It may include a step of cold annealing so that the ⁇ value satisfies -10 or more and 10 or less.
  • [C], [Mn], [Ni], [N], [Nb] in Formula (1) means the weight% of each element
  • Temp means the cold annealing temperature (°C).
  • cold rolling may be performed without annealing after the hot rolling step.
  • an austenitic stainless steel having excellent surface roughness and no surface cracks in a bent portion is provided through an ultra-fine manufacturing technology that realizes bending formability and sound surface properties of the bent portion, and a method for manufacturing the same can do.
  • Figure 2 is a photograph showing the presence or absence of surface properties and surface cracks of the bent portion after the 180 ° bending experiment for Comparative Example 4.
  • Figure 3 is a photograph showing the surface roughness of the bent portion after the 180 ° bending experiment for Inventive Example 5.
  • Figure 4 is a photograph showing the surface roughness of the bent portion after the 180 ° bending experiment for Comparative Example 14.
  • FIG. 5 is a photograph of the microstructure of the center of the thickness of Example 5 through an Electron Backscatter Diffraction (EBSD).
  • EBSD Electron Backscatter Diffraction
  • FIG. 6 is a photograph of the microstructure of the center of the thickness of Inventive Example 14 through an Electron Backscatter Diffraction (EBSD).
  • EBSD Electron Backscatter Diffraction
  • Austenitic stainless steel according to an embodiment of the present invention, by weight%, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Ni: 6 ⁇ 12%, Cr: 16 ⁇ 20%, N: 0.01-0.2%, Nb: 0.25% or less, including the remaining Fe and unavoidable impurities, the average grain size (d) value of the center of the thickness is 5 ⁇ m or less, and in the bent area after the 180 ° bending experiment The measured martensite area fraction may be 10% or less.
  • Austenitic stainless steel according to an example of the present invention, by weight%, C: 0.005 ⁇ 0.03%, Si: 0.1 ⁇ 1%, Mn: 0.1 ⁇ 2%, Ni: 6 ⁇ 12%, Cr: 16 ⁇ 20 %, N: 0.01 to 0.2%, Nb: 0.25% or less, the remaining Fe and unavoidable impurities may be included.
  • the content of C (carbon) may be 0.005 to 0.03%.
  • C is an austenite phase stabilizing element.
  • C may be added by 0.005% or more.
  • the upper limit of the C content may be limited to 0.03%.
  • the content of Si may be 0.1 to 1.0%.
  • Si is a component added as a deoxidizer in the steelmaking step, and has the effect of improving the corrosion resistance of the steel by forming Si oxide in the passivation film when going through the bright annealing process. Considering this, Si may be added in an amount of 0.1% or more. However, when the content of Si is excessive, a problem of lowering the ductility of the steel may occur. In consideration of this, the upper limit of the Si content may be limited to 1.0%.
  • the content of Mn (manganese) may be 0.1 to 2.0%.
  • Mn is an austenite phase stabilizing element. Considering this, Mn may be added in an amount of 0.1% or more. However, when the content of Mn is excessive, a problem of lowering corrosion resistance may occur. In consideration of this, the upper limit of the Mn content may be limited to 2.0%.
  • Ni nickel
  • the content of Ni (nickel) may be 6.0 to 12.0%.
  • Ni is an austenite phase stabilizing element and has an effect of softening steel materials. Considering this, 6.0% or more of Ni may be added. However, when the Ni content is excessive, a problem of cost increase may occur. In consideration of this, the upper limit of the Ni content may be limited to 12.0%.
  • the content of Cr (chromium) may be 16.0 to 20.0%.
  • Cr is a major element for improving the corrosion resistance of stainless steel. In consideration of this, 16.0% or more of Cr may be added. However, when the content of Cr is excessive, the steel material is hardened, and a problem of suppressing strain-induced martensitic transformation during cold rolling may occur. In consideration of this, the upper limit of the Cr content may be limited to 20.0%.
  • the content of N may be 0.01 to 0.2%.
  • 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 upper limit of the N content may be limited to 0.2%.
  • the content of Nb may be 0.25% or less.
  • Nb has the effect of inhibiting crystal grain growth by forming Nb-based z-phase precipitates when added.
  • the upper limit of the Nb content may be limited to 0.25%.
  • the remaining component is iron (Fe).
  • Fe iron
  • the average grain size (d) value of the center of the thickness is 5 ⁇ m or less, and martensite measured at the bent portion after the 180 ° bending experiment
  • the area fraction may be 10% or less.
  • an ultra-fine microstructure is realized, and at the same time, the martensite area fraction measured at the bending part is lowered to improve the surface properties.
  • An excellent austenitic stainless steel can be provided.
  • the austenitic stainless steel according to an embodiment of the present invention may have a center line average roughness (Ra) of 0.5 ⁇ m or less and a 10-point average roughness (Rz) of 3 ⁇ m or less after a 180° bending test.
  • the 180 ° bending experiment may be performed by making the R value of the curvature of the bending part equal to the thickness of the material and performing the bending once.
  • the pitting potential is a critical potential at which corrosion occurs in the form of a hole in a passivated metal material, and pitting occurs when the austenitic stainless steel according to an embodiment of the present invention is immersed in a NaCl solution and a potential is applied.
  • the result of measuring the pitting potential may be 250 mV or more.
  • the temperature of the NaCl solution is 30 °C, the concentration may be 3.5%.
  • [C], [Mn], [Ni], [N], [Nb] in Formula (1) means the weight% of each element
  • Temp means the cold annealing temperature (°C).
  • the slab having the alloy composition may be manufactured as a hot-rolled material through a hot-rolling process. Thereafter, the hot-rolled material may be manufactured into a cold-rolled material by cold rolling at room temperature.
  • the prepared cold rolled material may be cold rolled annealed.
  • Cold rolling annealing may be performed in the range of 700 to 850 ° C. in order to satisfy the ⁇ value represented by Equation (1) above -10 and below 10.
  • the temperature of cold rolling annealing is less than 700 ° C., recrystallization is not sufficient and the elongation is lowered.
  • the temperature of cold rolling annealing exceeds 850 °C, the particles become coarse and it is difficult to form ultra-fine particles of 5 ⁇ m or less, resulting in surface cracks in the bent portion of austenitic stainless steel and poor surface roughness. Problems can arise.
  • annealing was performed at 1000 to 1150 ° C. or cold rolling was performed at room temperature with a total sheet thickness reduction rate of 40% or more without performing annealing. Then, by annealing in the range of 700 to 850 °C to prepare a cold-rolled annealed material.
  • Equation (1) of the prepared cold rolled annealed material are shown in Table 1 below.
  • [C], [Mn], [Ni], [N], [Nb] means the weight% of each element
  • Temp means the cold rolling annealing temperature (°C).
  • the prepared cold-rolled annealed material was produced as a specimen having a thickness of 0.1 to 3.0 mm. Thereafter, the average grain size (d) of the thickness center, pitting potential, martensite area fraction of the bending part, cracks of the bending part, property of the bending part, center line average roughness (Ra) of the bending part, and 10-point average roughness (Rz) of the bending part with respect to the specimen ) After measuring, it is shown in Table 2 below.
  • the average grain size (d) was measured by analyzing the orientation of the center of the thickness using an Electron Backscatter Diffraction (EBSD) model name e-Flash FS.
  • EBSD Electron Backscatter Diffraction
  • the pitting potential means a potential value at which pitting occurs by immersing in a NaCl solution and applying a potential.
  • a NaCl solution a solution having a temperature of 30°C and a concentration of 3.5% was used.
  • the area fraction (%) of martensite in the bent part means the area fraction (%) of martensite in the bent part after the 180 ° bending experiment.
  • the martensite area fraction (%) was measured using a ferrite content meter having a model name of FMP30.
  • the cracks of the bent part, the property of the bent part, the center line average roughness (Ra) of the bent part, and the ten-point average roughness (Rz) of the bent part were measured after the 180° bending experiment.
  • the 180 ° bending experiment was conducted by making the bending portion curvature (R) value the same as the thickness of the cold-rolled annealed material and performing the bending once.
  • 'O' in the bending part crack in Table 2 below means a case where the bending part crack is good.
  • 'X' means a case where a crack occurs in the bending part.
  • 'O' means a case where the properties of the bending part are good.
  • 'X' means a case where the properties of the bending part are poor.
  • Inventive Examples 1 to 13 all had an ⁇ value of Equation (1) in the range of -10 or more and 10 or less, and the average grain size (d) value was 5 ⁇ m or less. . In addition, Inventive Examples 1 to 13 satisfied the martensite area fraction (%) of 10% or less measured at the bent portion after the 180 ° bending experiment.
  • Comparative Examples 12 to 14 Ni, which can soften the material, was added more than Comparative Examples 1 to 11, so no surface cracks occurred on the bent portion. However, in Comparative Examples 12 to 14, the cold rolling annealing temperature was low, and band-shaped non-recrystallized portions were generated. Therefore, in Comparative Examples 12 to 14, the center line average roughness (Ra) of 1.16 to 3.92 ⁇ m and the ten-point average roughness (Rz) of 7.05 to 16.20 ⁇ m were measured for surface roughness at the bent portion, and the surface properties were poor.
  • Ra center line average roughness
  • Rz ten-point average roughness
  • FIGS. 1 and 2 are photographs for comparing the presence or absence of surface cracks in the bent portion after the 180 ° bending experiment of the inventive example and the comparative example.
  • 1 is a photograph of Inventive Example 5
  • FIG. 2 is a photograph of Comparative Example 4. Comparing FIGS. 1 and 2, it can be confirmed that surface cracks do not occur in the austenitic stainless steel according to an example of the present invention.
  • FIGS. 3 and 4 are photographs for comparing the surface characteristics of the bent portion after the 180 ° bending experiment of the inventive example and the comparative example.
  • 3 is a photograph of Inventive Example 5
  • FIG. 4 is a photograph of Comparative Example 14. Comparing FIGS. 3 and 4, it can be confirmed that the austenitic stainless steel according to an example of the present invention has good surface properties.
  • FIGS. 5 and 6 are photographs of the thickness center microstructures of the inventive examples and the comparative examples through an Electron Backscatter Diffraction (EBSD).
  • EBSD Electron Backscatter Diffraction
  • 5 is a photograph of Inventive Example 5
  • FIG. 6 is a photograph of Comparative Example 14. Comparing FIGS. 5 and 6, it can be confirmed that the austenitic stainless steel according to an example of the present invention is an ultra-fine particle without band-shaped unrecrystallized portions.
  • an austenitic stainless steel having excellent surface roughness and no surface cracks in a bent portion is provided through ultra-fine manufacturing technology that realizes bending formability and sound surface properties of the bent portion, and a method for manufacturing the same can do.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • 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)

Abstract

Sont divulgués dans la présente invention : un acier inoxydable austénitique exempt de fissures de surface dans une partie courbée et présentant une excellente rugosité de surface ; et son procédé de fabrication. L'acier inoxydable austénitique selon un mode de réalisation de la présente invention comprend de 0,005 à 0,03 % en poids de C, de 0,1 à 1 % en poids de Si, de 0,1 à 2 % en poids de Mn, de 6 à 12 % en poids de Ni, de 16 à 20 % en poids de Cr, de 0,01 à 0,2 % en poids de N, et au plus 0,25 % en poids de Nb, le reste étant constitué de Fe et d'impuretés inévitables, la valeur de dimension moyenne des grains (d) au niveau d'une partie centrale dans le sens de l'épaisseur étant inférieure ou égale à 5 µm, et la fraction de zone martensitique mesurée dans la partie courbée après un essai de flexion de 180° pouvant être d'au plus 10 %.
PCT/KR2022/008454 2021-06-21 2022-06-15 Acier inoxydable austénitique et son procédé de fabrication WO2022270814A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
CN202280043970.2A CN117529571A (zh) 2021-06-21 2022-06-15 奥氏体系不锈钢及其制造方法
EP22828661.3A EP4343013A1 (fr) 2021-06-21 2022-06-15 Acier inoxydable austénitique et son procédé de fabrication
JP2023575582A JP2024522170A (ja) 2021-06-21 2022-06-15 オーステナイト系ステンレス鋼及びその製造方法

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KR1020210080002A KR20220169655A (ko) 2021-06-21 2021-06-21 오스테나이트계 스테인리스강 및 그 제조방법
KR10-2021-0080002 2021-06-21

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101550738B1 (ko) * 2015-04-29 2015-09-08 성기천 연성이 우수한 스테인리스강 및 이를 이용한 냉매 배관용 스테인리스 파이프
WO2016047734A1 (fr) * 2014-09-25 2016-03-31 新日鐵住金株式会社 Tôle d'acier inoxydable austénitique et procédé de production de ladite tôle
KR101735007B1 (ko) * 2015-12-23 2017-05-15 주식회사 포스코 주름 저항성이 우수한 오스테나이트계 스테인리스 강관
KR20170069338A (ko) * 2015-12-10 2017-06-21 주식회사 포스코 절곡능이 향상된 듀플렉스 스테인리스강 및 그 제조방법
KR20190020393A (ko) * 2017-08-21 2019-03-04 주식회사 포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
JP2020050940A (ja) 2018-09-28 2020-04-02 国立研究開発法人日本原子力研究開発機構 オーステナイト系微細粒ステンレス鋼の製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016047734A1 (fr) * 2014-09-25 2016-03-31 新日鐵住金株式会社 Tôle d'acier inoxydable austénitique et procédé de production de ladite tôle
KR101550738B1 (ko) * 2015-04-29 2015-09-08 성기천 연성이 우수한 스테인리스강 및 이를 이용한 냉매 배관용 스테인리스 파이프
KR20170069338A (ko) * 2015-12-10 2017-06-21 주식회사 포스코 절곡능이 향상된 듀플렉스 스테인리스강 및 그 제조방법
KR101735007B1 (ko) * 2015-12-23 2017-05-15 주식회사 포스코 주름 저항성이 우수한 오스테나이트계 스테인리스 강관
KR20190020393A (ko) * 2017-08-21 2019-03-04 주식회사 포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
JP2020050940A (ja) 2018-09-28 2020-04-02 国立研究開発法人日本原子力研究開発機構 オーステナイト系微細粒ステンレス鋼の製造方法

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