WO2020036370A1 - Acier inoxydable austénitique ayant une résistance améliorée - Google Patents

Acier inoxydable austénitique ayant une résistance améliorée Download PDF

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WO2020036370A1
WO2020036370A1 PCT/KR2019/009977 KR2019009977W WO2020036370A1 WO 2020036370 A1 WO2020036370 A1 WO 2020036370A1 KR 2019009977 W KR2019009977 W KR 2019009977W WO 2020036370 A1 WO2020036370 A1 WO 2020036370A1
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stainless steel
austenitic stainless
content
improved strength
less
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PCT/KR2019/009977
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English (en)
Korean (ko)
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이재화
조규진
김영태
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주식회사 포스코
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Priority to US17/266,011 priority Critical patent/US20210292877A1/en
Priority to CN201980065501.9A priority patent/CN112789365B/zh
Priority to EP19849274.6A priority patent/EP3822384B8/fr
Priority to FIEP19849274.6T priority patent/FI3822384T3/fi
Publication of WO2020036370A1 publication Critical patent/WO2020036370A1/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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of 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
    • 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
    • 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
    • C21D8/0247—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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/18—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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 more particularly, to an austenitic stainless steel having improved strength while maintaining elongation and corrosion resistance.
  • stainless steel refers to steel having strong corrosion resistance because corrosion, which is a weak point of carbon steel, is suppressed.
  • stainless steel is classified according to chemical composition or metal structure. According to the metal structure, stainless steel can be classified into austenitic, ferrite, martensite and dual phase systems.
  • austenitic stainless steel is most commonly used as a steel containing a large amount of chromium (Cr) and nickel (Ni).
  • Cr chromium
  • Ni nickel
  • 316L stainless steel is applied to various industrial fields by securing corrosion resistance and molding properties based on 16-18% Cr, 10-14% Ni, and 2-3% Molybdenum based component system. have.
  • Ni and Mo have problems in terms of price competitiveness due to high material prices, and raw material supply and demand are unstable due to extreme fluctuations in material prices and it is difficult to secure stability of supply prices.
  • 216 stainless steel is basically a steel with 7% or more of Mn added to reduce the Ni content below a certain amount to lower the material price and to ensure the stability of the austenite phase according to the Ni reduction. Cr, 5-7% Ni, 7.5-9% Mn and 2-3% Mo.
  • 216 stainless steel can achieve corrosion resistance similar to that of 316L stainless steel, but due to the addition of a large amount of Mn, a large amount of Mn fume is generated during the steelmaking process.
  • MnS rigid inclusions
  • Duplex stainless steel is a stainless steel having a microstructure in which the austenitic phase and the ferrite phase are mixed. Specifically, the austenitic stainless steel and the ferritic stainless steel are characterized by the presence of about 35 to 65% by volume of the austenitic phase and the ferrite phase, respectively. Indicates both.
  • Duplex stainless steel is getting the spotlight as industrial steel such as desalination equipment, pulp, paper, and chemical facilities that require corrosion resistance with low Ni content and easy to secure high strength with low Ni content while securing corrosion resistance equivalent to 316L stainless steel.
  • Embodiments of the present invention to provide an austenitic stainless steel with improved strength while ensuring elongation and corrosion resistance of the existing 316L stainless steel.
  • Austenitic stainless steel with improved strength according to an embodiment of the present invention, in weight percent, C: 0.02 to 0.14%, Si: 0.2 to 0.6%, S: less than 0.01%, Mn: 2.0 to 4.5%, Ni : 2.5 to 5.0%, Cr: 19.0 to 22.0%, Cu: 1.0 to 3.0%, Mo: less than 1.0%, N: 0.25 to 0.40%, the remainder containing Fe and unavoidable impurities, represented by the following formula (1):
  • the SNL (Solubility of Nitrogen in Liquid) value is more than the content of N.
  • C + N may be 0.5% or less (excluding 0).
  • it may further include at least one of B: 0.001 to 0.005% and Ca: 0.001 to 0.003%.
  • Md 30 value represented by the following formula (2) may satisfy -50 or less.
  • C, N, Si, Mn, Cr, Ni, Cu, Mo means the content (% by weight) of each element.
  • Equation (3) Creq / Nieq ⁇ 1.8
  • the pitting index value represented by the following formula (4) may satisfy 22 or more.
  • the yield strength (0.2 off-set) of the austenitic stainless steel may be 400 to 450 MPa, tensile strength 700 to 850 MPa.
  • the elongation of the austenitic stainless steel may be 35% or more.
  • an austenitic stainless steel with improved strength while ensuring elongation and corrosion resistance of the existing 316L stainless steel.
  • Thermocalc for deriving the SNL (Solubility of Nitrogen in Liquid) value of the austenitic stainless steel according to an embodiment of the present invention. This is a graph to explain the correlation between the calculation result and the regression application value.
  • Austenitic stainless steel with improved strength according to an embodiment of the present invention, in weight percent, C: 0.02 to 0.14%, Si: 0.2 to 0.6%, S: less than 0.01%, Mn: 2.0 to 4.5%, Ni : 2.5 to 5.0%, Cr: 19.0 to 22.0%, Cu: 1.0 to 3.0%, Mo: less than 1.0%, N: 0.25 to 0.40%, the remainder containing Fe and unavoidable impurities, represented by the following formula (1):
  • the SNL (Solubility of Nitrogen in Liquid) value is more than the content of N.
  • Austenitic stainless steel with improved strength according to an aspect of the present invention, in weight%, C: 0.02 to 0.14%, Si: 0.2 to 0.6%, S: less than 0.01%, Mn: 2.0 to 4.5%, Ni: 2.5 to 5.0%, Cr: 19.0 to 22.0%, Cu: 1.0 to 3.0%, Mo: less than 1.0%, N: 0.25 to 0.40%, and the balance includes Fe and unavoidable impurities.
  • the content of C is 0.02 to 0.14%.
  • Carbon (C) is an element effective for stabilizing austenite phase, but when the content is low, it may be added at least 0.02% as an additional austenite stabilizing element is required. However, if the content is excessive, not only the workability is lowered by the solid solution strengthening effect, but also it may adversely affect the ductility, toughness and corrosion resistance by inducing grain boundary precipitation of Cr carbide due to heat affected zone of welded part and latent heat after hot rolled coiling. Therefore, the upper limit can be limited to 0.14%.
  • the content of Si is 0.2 to 0.6%.
  • Si Silicon
  • Si may be added as 0.2% or more as an effective element to improve the corrosion resistance while acting as a deoxidizer during the steelmaking process.
  • Si is an effective element for stabilizing ferrite phase, and when excessively added, it promotes the formation of delta ferrite in the cast slab, which not only decreases the hot workability but also decreases the ductility / toughness of the steel due to the solid solution effect. It can be limited.
  • the content of Mn is 2.0 to 4.5%.
  • Manganese (Mn) is an austenite-stable stabilizing element added in place of nickel (Ni) in the present invention, is effective in improving the cold rolling properties by suppressing the production of organic martensite, solubility of nitrogen (N) during steelmaking process to be described later 2.0% or more may be added as an element to increase.
  • the upper limit can be limited to 4.5% because it may decrease the ductility, toughness and corrosion resistance of the steel as it increases the S-based inclusions (MnS).
  • the content of Ni is 2.5 to 5.0%.
  • Nickel (Ni) is a strong austenite stabilizing element, which is essential to ensure good hot workability and cold workability. In particular, addition of more than 2.5% is essential even if a certain amount or more of Mn is added. However, Ni is an expensive element, which leads to an increase in raw material cost when a large amount is added. Therefore, the upper limit can be limited to 5.0% in consideration of both the cost and efficiency of the steel.
  • the content of Cr is 19 to 22%.
  • chromium (Cr) is a ferrite stabilizing element, it is effective in suppressing martensitic phase formation and is a basic element for securing corrosion resistance required for stainless steel.
  • 19% or more may be added as an element to increase the solubility of nitrogen (N) during the steelmaking process described later.
  • N solubility of nitrogen
  • austenite stabilizing elements such as Ni, Mn, etc.
  • the upper limit can be limited to 22%.
  • the content of P is less than 0.1%.
  • Phosphorus (P) can limit the upper limit to 0.1% as it reduces corrosion resistance and hot workability.
  • the content of S is less than 0.01%.
  • S Sulfur
  • S can limit the upper limit to 0.01% as it lowers the corrosion resistance and hot workability.
  • the content of Cu is 1.0 to 3.0%.
  • Copper (Cu) is an austenite stabilizing element added in place of nickel (Ni) in the present invention, and improves the moldability by improving the corrosion resistance in a reducing environment and reducing the stacking fault energy (SFE). 1.0% or more may be added to fully express this effect. However, if the content is excessive, the upper limit can be limited to 3.0% because not only the increase in material cost but also the hot workability can be lowered.
  • the content of Mo is less than 1.0%.
  • Molybdenum (Mo) is an element effective in improving the corrosion resistance of stainless steel by modifying a passive film.
  • Mo is an expensive element
  • the addition of a large amount of raw materials not only increases the raw material cost but also lowers the hot workability. Therefore, the upper limit may be limited to 1.0% in consideration of cost-efficiency and hot workability of the steel.
  • the content of N is 0.25 to 0.40%.
  • Nitrogen (N) is an effective element for improving corrosion resistance and is a strong austenite stabilizing element. Therefore, nitrogen alloying can reduce the material cost by enabling lower use of Ni, Cu, Mn. 0.25% or more may be added to fully express this effect. However, if the content is excessive, the upper limit can be limited to 0.40% because the workability and formability may be reduced by the solid solution strengthening effect.
  • the content of C + N is 0.5% or less.
  • C and N are effective elements for improving strength, but when the content is excessive, there is a problem of degrading workability, and the upper limit of the total can be limited to 0.5%.
  • the austenitic stainless steel with improved strength according to an embodiment of the present invention may further include one or more of B: 0.001 to 0.005 and Ca: 0.001 to 0.003%.
  • the content of B is 0.001 to 0.005%.
  • Boron (B) is an effective element for suppressing the occurrence of cracks during casting to ensure good surface quality, can be added 0.001% or more. However, if the content is excessive, the surface quality can be reduced by forming nitride (BN) on the surface of the product during the annealing / pickling process, the upper limit can be limited to 0.005%.
  • the content of Ca is 0.001 to 0.003%.
  • Calcium (Ca) is an element that suppresses the formation of MnS steelmaking inclusions generated at the grain boundary when containing high Mn and improves the cleanliness of the product, and may be added at least 0.001%. However, when the content is excessive, the hot workability due to the formation of Ca-based inclusions and the surface quality of the product may be lowered, and the upper limit thereof may be limited to 0.003%.
  • the remaining component of the present invention is iron (Fe).
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, not all of them are specifically mentioned in the present specification.
  • the content of N that can be dissolved within the melt temperature at 1150 ° C. is derived according to the amount of each alloy element (C, Si, Mn, Ni, Cr, Cu, Mo) It was.
  • Thermocalc for deriving SNL (Solubility of Nitrogen in Liquid) value of the austenitic stainless steel according to an embodiment of the present invention. This is a graph to explain the correlation between the calculation result and the regression application value.
  • the limit value of the solid solution of nitrogen in the molten metal was calculated and expressed as "N.”
  • the SNL value is greater than the N content.
  • the SNL value is set higher than the N content to increase the nitrogen solubility limit, it was confirmed that the steelmaking operation of the target alloy component is performed well.
  • Austenitic stainless steels are applied to products requiring a beautiful surface.
  • Bright annealing of cold rolled materials is common for products requiring a beautiful surface.
  • Such bright annealing is performed during the heat treatment process of the stainless steel cold rolled material by performing heat treatment of the stainless steel cold rolled material under a reducing atmosphere (Dew point -40 to -60 ° C) using nitrogen (N 2 ), hydrogen (H 2 ), or the like.
  • N 2 nitrogen
  • H 2 hydrogen
  • Bright annealing using hydrogen is the most common atmosphere gas used for bright annealing, because it is most widely used to suppress discoloration of the surface as well as high heat capacity.
  • the hydrogen atoms penetrated into the surface layer are naturally baked out after a certain time at room temperature for ferrite or martensite phases having a general BCC and BCT structure so that they do not significantly affect physical properties.
  • the amount of martensite phase formed on the surface of the austenitic stainless steel together with the alloying components must be controlled to secure beautiful surface quality and workability through bright annealing.
  • the Md 30 value represented by the following formula (2) satisfies the range of -50 ° C or less.
  • martensite transformation occurs by plastic working at a temperature higher than the martensite transformation start temperature (Ms).
  • Ms martensite transformation start temperature
  • the upper limit temperature which causes phase transformation by such a process is represented by Md value, and is a measure which shows the extent to which phase transformation occurs by processing.
  • the temperature (° C.) at which 50% phase transformation to martensite occurs when 30% strain is given is defined as Md 30 . If the Md 30 value is high, it is easy to form a processed organic martensite phase, whereas if the Md 30 value is low, it can be judged to be a relatively difficult steel type. In general, the Md 30 value is used as an index for determining the austenite stabilization degree of ordinary austenitic stainless steel, and can be calculated through the Nohara regression equation represented by Equation (2).
  • Forming various kinds of phases by the difference in alloy content is because the effect of each alloy component added on the phase balance is different.
  • the degree that each alloy component affects the phase balance can be calculated through Creq and Nieq, and the phase generated at room temperature can be predicted through the Creq / Nieq ratio expressed as in Equation (3) below.
  • Creq Cr + Mo + 1.5 ⁇ Si
  • Nieq Ni + 0.5 ⁇ Mn + 30 ⁇ (C + N) + 0.5 ⁇ Cu.
  • the PREN value was set to 22 or more.
  • a slab having a thickness of 200 mm was prepared through ingot melting, and heated at 1,240 ° C. for 2 hours, followed by hot rolling to prepare a hot rolled steel sheet having a thickness of 3 mm.
  • Example 1 0.104 0.48 2.91 0.005 3.53 20.8 2.1 0.52 0.3 0.404
  • Example 2 0.103 0.49 3.4 0.005 3.35 19.6 1.16 0.39 0.27 0.373
  • Example 3 0.088 0.31 3.41 0.004 3.7 21.7 2.51 0.10 0.34 0.428
  • Example 4 0.035 0.31 3.8 0.006 4.2 21 2.48 0.20 0.33 0.365
  • Comparative Example 1 0.02 0.52 1.4 0.004 10.4 16.6 0.39 2.00 0.018 0.038
  • Comparative Example 2 0.014 0.55 2.4 0.006 2.4 20.3 0.1 1.30 0.2 0.166
  • Comparative Example 4 0.15 0.46 3.8 0.004 3.6 21.6 2.04 0.32 0.35 0.500
  • the mechanical properties were measured using No. 5 test piece specified in Japanese Industrial Standard JIS Z 2201. Specifically, the tensile test was conducted using JIS Z 2201, yield strength (MPa), tensile strength (Tensile Strength, MPa) and elongation (%) measured accordingly are described in Table 2 below. .
  • the comparative example 1 corresponding to the component system of general 316L stainless steel, it shows the structure comprised by the austenite phase and showing PREN value of 22 or more.
  • the mechanical property evaluation results show a yield strength of 220 MPa and a tensile strength of 540 MPa, which are generally applied to materials requiring high strength due to the properties of soft austenitic stainless steels. There is a problem that is difficult to do.
  • Comparative Example 3 in which the content of Ni and Mn was slightly increased compared to Comparative Example 2 and the Creq / Nieq ratio was set to 1.8 or less, a microstructure was observed to form austenitic tissue, and the mechanical properties of Comparative Example 1 It is harder than 316L, and it can be seen that it shows soft physical properties compared to Duplex stainless steel of Comparative Example 2.
  • the Md 30 value is -5 °C, which is highly likely to cause hydrogen embrittlement in the future production of bright annealing materials.
  • the N content is significantly affected by the content of Cr is low, the addition amount of N to 0.21% level, it is not possible to maximize the nitrogen factor of the PREN value, there is a problem that it is difficult to secure the pitting resistance of 316L level.
  • the C + N content is 0.5%, exceeding the upper limit of 0.5% of the present invention, showing hard mechanical properties, and an elongation of less than 35%.
  • the Ni and Mo contents were relatively low, and it was confirmed that the PREN value was more than 22 while securing price competitiveness, and the mechanical property evaluation showed that high strength properties were achieved compared to 316L and good elongation of 35% or more was obtained. It was.
  • Austenitic stainless steel according to the present invention can be used as a substitute material of the existing 316L stainless steel while improving the strength while ensuring elongation and corrosion resistance.

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Abstract

La présente invention concerne un acier inoxydable austénitique ayant une résistance améliorée. L'acier inoxydable austénitique de l'invention comprend, en % en poids, 0,02 à 0,14 % de C, 0,2 à 0,6 % de Si, S en une quantité inférieure à 0,01 %, 2,0 à 4,5 % de Mn, 2,5 à 5,0 % de Ni, 19,0 à 22,0 % de Cr, 1,0 à 3,0 % de Cu, Mo en une quantité inférieure à 1,0 %, 0,25 à 0,40 % de N, et le reste étant Fe et des impuretés inévitables, l'indice de solubilité d'azote dans le liquide (SNL) exprimé par la relation suivante (1) étant supérieure ou égale à la quantité de N. Relation (1) : SNL = -0,188 - 0,0423 × C - 0,0517 × Si + 0,012 × Mn + 0,0048 × Ni + 0,0252 × Cr - 0,00906 × Cu + 0,00021 × Mo, dans laquelle C, Si, Mn, Ni, Cr, Cu et Mo désignent la quantité (en % en poids) des éléments respectifs.
PCT/KR2019/009977 2018-08-13 2019-08-08 Acier inoxydable austénitique ayant une résistance améliorée WO2020036370A1 (fr)

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US17/266,011 US20210292877A1 (en) 2018-08-13 2019-08-08 Austenitic stainless steel having improved strength
CN201980065501.9A CN112789365B (zh) 2018-08-13 2019-08-08 具有改善的强度的奥氏体不锈钢
EP19849274.6A EP3822384B8 (fr) 2018-08-13 2019-08-08 Acier inoxydable austénitique ayant une résistance améliorée
FIEP19849274.6T FI3822384T3 (fi) 2018-08-13 2019-08-08 Parannetun lujuuden omaava austeniittinen ruostumaton teräs

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Publication number Priority date Publication date Assignee Title
KR101056235B1 (ko) * 2008-11-25 2011-08-11 주식회사 포스코 오스테나이트계 스테인리스강 냉연제품의 재질특성 예측방법
KR20120091075A (ko) * 2009-11-02 2012-08-17 에이티아이 프로퍼티즈, 인코퍼레이티드 절약형 오스테나이트 스테인레스강
WO2012143610A1 (fr) * 2011-04-18 2012-10-26 Outokumpu Oyj Procédé de fabrication et d'utilisation d'acier inoxydable ferritique-austénitique
JP2014001422A (ja) * 2012-06-18 2014-01-09 Nippon Steel & Sumitomo Metal オーステナイト系ステンレス鋼板およびその製造方法
JP2016065296A (ja) * 2014-09-26 2016-04-28 エア・ウォーターＮｖ株式会社 遊戯用鋼球およびその製造方法

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA2348909A1 (fr) * 1998-11-02 2000-05-11 Crs Holdings, Inc. Acier inoxydable austenitique cr-mn-ni-cu
JP3696552B2 (ja) * 2001-04-12 2005-09-21 日新製鋼株式会社 加工性，冷間鍛造性に優れた軟質ステンレス鋼板
KR20090005252A (ko) * 2004-01-29 2009-01-12 제이에프이 스틸 가부시키가이샤 오스테나이트·페라이트계 스테인레스 강
WO2009082501A1 (fr) * 2007-12-20 2009-07-02 Ati Properties, Inc. Acier inoxydable austénitique pauvre résistant à la corrosion
SE533635C2 (sv) * 2009-01-30 2010-11-16 Sandvik Intellectual Property Austenitisk rostfri stållegering med låg nickelhalt, samt artikel därav
EP2804962B1 (fr) * 2012-01-20 2021-06-09 Solu Stainless Oy Procede de fabrication d'un acier inoxidable austenitique
CN103627970A (zh) * 2013-10-30 2014-03-12 振石集团东方特钢股份有限公司 一种含钒奥氏体不锈钢
FI125105B (en) * 2013-11-04 2015-06-15 Outokumpu Oy Grain boundary corrosion resistant austenitic stainless steel and method for its production
KR20150074697A (ko) * 2013-12-24 2015-07-02 주식회사 포스코 저 니켈 함유 스테인리스강
JP6763759B2 (ja) * 2015-11-20 2020-09-30 日本精線株式会社 磁気特性に優れた二相系のステンレス鋼線、及び篩用、ネットコンベア用又はフィルタ用の磁性金網製品
KR101952808B1 (ko) * 2017-08-22 2019-02-28 주식회사포스코 열간가공성 및 내수소취성이 우수한 저Ni 오스테나이트계 스테인리스강

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101056235B1 (ko) * 2008-11-25 2011-08-11 주식회사 포스코 오스테나이트계 스테인리스강 냉연제품의 재질특성 예측방법
KR20120091075A (ko) * 2009-11-02 2012-08-17 에이티아이 프로퍼티즈, 인코퍼레이티드 절약형 오스테나이트 스테인레스강
WO2012143610A1 (fr) * 2011-04-18 2012-10-26 Outokumpu Oyj Procédé de fabrication et d'utilisation d'acier inoxydable ferritique-austénitique
JP2014001422A (ja) * 2012-06-18 2014-01-09 Nippon Steel & Sumitomo Metal オーステナイト系ステンレス鋼板およびその製造方法
JP2016065296A (ja) * 2014-09-26 2016-04-28 エア・ウォーターＮｖ株式会社 遊戯用鋼球およびその製造方法

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KR20200018995A (ko) 2020-02-21
CN112789365A (zh) 2021-05-11
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