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WO2022045595A1 - Acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée - Google Patents

Acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée Download PDF

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Publication number
WO2022045595A1
WO2022045595A1 PCT/KR2021/009569 KR2021009569W WO2022045595A1 WO 2022045595 A1 WO2022045595 A1 WO 2022045595A1 KR 2021009569 W KR2021009569 W KR 2021009569W WO 2022045595 A1 WO2022045595 A1 WO 2022045595A1
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stainless steel
austenitic stainless
less
work hardening
excluding
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PCT/KR2021/009569
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English (en)
Korean (ko)
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김경훈
김지수
전종진
박미남
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주식회사 포스코
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Priority to US18/019,187 priority Critical patent/US20230287549A1/en
Priority to JP2023512177A priority patent/JP2023539140A/ja
Priority to EP21861894.0A priority patent/EP4177368A4/fr
Priority to CN202180055978.6A priority patent/CN116096934A/zh
Publication of WO2022045595A1 publication Critical patent/WO2022045595A1/fr

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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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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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Definitions

  • the present invention relates to austenitic stainless steel with improved deep drawing, and more particularly, to austenitic stainless steel that does not crack when deep machining is applied to convert a plate material into a three-dimensional part. is about
  • Deep machining can omit additional processes such as welding and stress relief heat treatment, so it is an effective method for reducing manufacturing cost.
  • cylindrical molding such as a cup or a battery, a material excellent in deep workability is required.
  • Austenitic stainless steels have excellent elongation, no problem in making complex shapes, and excellent work hardenability, and are used in various fields involving deep machining.
  • austenitic stainless steel is deformed in shape while work hardening occurs during cold working. At this time, it is known that when the austenitic stainless steel has excellent work hardenability, forming is easy.
  • Embodiments of the present invention are intended to provide an austenitic stainless steel capable of securing formability when deep machining is applied by minimizing an increase in strength due to work hardening.
  • Austenitic stainless steel with improved deep workability by weight, C: 0.01 to 0.05%, N: 0.01 to 0.25%, Si: 1.5% or less (excluding 0), Mn: 0.3 to 3.5%, Cr: 17.0 to 22.0%, Ni: 9.0 to 14.0%, Mo: 2.0% or less (excluding 0), Cu: 0.2 to 2.5%, remaining Fe and unavoidable impurities, including the following formula (1 ) is satisfied.
  • Cr, Si, Mo, Ni, Cu, C, and N mean wt% of each element.
  • Equation (2) 0 ⁇ 2.4*Cr+1.7*Mo+3.9*Si-2.1*Ni-Mn-0.4*Cu-58*C-64*N-13 ⁇ 5.5
  • Cr, Mo, Si, Ni, Mn, Cu, C, and N mean weight% of each element.
  • Al 0.04% or less (excluding 0)
  • Ti 0.003% or less (excluding 0)
  • B 0.0025% or less (excluding 0)
  • P 0.035% or less
  • S It may further include one or more of 0.0035% or less.
  • the true strain value when the work hardening index is the maximum may be 0.2 or less.
  • ⁇ is the stress
  • K is the strength modulus
  • ⁇ is the strain rate
  • n is the work hardening index
  • the difference between the true strain value when the work hardening index is the maximum and the true strain value when the work hardening index is 0 may be 0.11 or more.
  • the elongation may be 35% or more.
  • the tensile strength may be 360 MPa or more.
  • cracks may not occur until five-stage molding.
  • an austenitic stainless steel applicable as a deep machining material because it is possible to omit an intermediate heat treatment process and minimize an increase in strength due to work hardening when deep machining is applied.
  • 1 is a graph for explaining the relationship between stress-strain according to a tensile test of a material.
  • FIG. 2 is a graph showing the relationship between stress-strain together with a work hardening index during a tensile test of austenitic stainless steel according to the disclosed embodiment.
  • Austenitic stainless steel with improved deep workability by weight, C: 0.01 to 0.05%, N: 0.01 to 0.25%, Si: 1.5% or less (excluding 0), Mn: 0.3 to 3.5%, Cr: 17.0 to 22.0%, Ni: 9.0 to 14.0%, Mo: 2.0% or less (excluding 0), Cu: 0.2 to 2.5%, remaining Fe and unavoidable impurities, including the following formula (1 ) is satisfied.
  • Cr, Si, Mo, Ni, Cu, C, and N mean wt% of each element.
  • Austenitic stainless steel has high elongation and excellent formability, so it is a steel grade used for products of various shapes. When austenitic stainless steel is subjected to stress, deformation occurs by transformation from an unstable austenite phase to a martensite phase at room temperature, that is, transformation induced plasticity.
  • the strength of the material also increases.
  • the austenitic stainless steel exhibits both deformation and strength increase due to work-hardening.
  • Work hardening capacity is expressed using work-hardening exponent, which changes according to strain.
  • work hardening of austenitic stainless steels is related to the degree of stabilization of the austenite phase. By increasing the degree of stabilization of the austenite phase through component control, work hardening of austenitic stainless steel can be suppressed.
  • the present inventors have obtained the following knowledge as a result of various studies in order to secure the elongation of the austenitic stainless steel and suppress the increase in strength due to work hardening when deep machining is applied.
  • Austenitic stainless steel with improved deep workability by weight, C: 0.01 to 0.05%, N: 0.01 to 0.25%, Si: 1.5% or less (excluding 0), Mn: 0.3 to 3.5%, Cr: 17.0 to 22.0%, Ni: 9.0 to 14.0%, Mo: 2.0% or less (excluding 0), Cu: 0.2 to 2.5%, remaining Fe and unavoidable impurities.
  • the unit is % by weight.
  • the content of C is 0.01 to 0.05%.
  • Carbon (C) is an effective element for stabilizing the austenite phase, and may be added in an amount of 0.01% or more to suppress martensite formation during deformation and secure strength.
  • the content is excessive, there is a problem in that corrosion resistance is deteriorated by inducing grain boundary precipitation of Cr carbides by bonding with Cr, so the upper limit can be limited to 0.05%.
  • the content of N is 0.01 to 0.25%.
  • the content of Si is 1.5% or less (excluding 0).
  • Silicon (Si) acts as a deoxidizer during the steelmaking process and is an element that secures the strength and corrosion resistance of austenitic stainless steel.
  • silicon which is a ferrite phase stabilizing element
  • the upper limit may be limited to 1.5%.
  • the content of Mn is 0.3 to 3.5%.
  • the upper limit may be limited to 3.5% because it may reduce the corrosion resistance and surface gloss of the austenitic stainless steel by forming an excessive amount of S-based inclusions (MnS).
  • the content of Cr is 17.0 to 22.0%.
  • Chromium (Cr) is a basic element that stabilizes ferrite and contains the most among elements for improving corrosion resistance of stainless steel. In the present invention, 17.0% or more may be added to form a passivation film to inhibit oxidation to secure corrosion resistance.
  • Ni 9.0 to 14.0%.
  • Nickel (Ni) is the most powerful austenite phase stabilizing element, and as its content increases, the austenite phase is stabilized to soften the material, and 9% or more is added to suppress work hardening caused by the occurrence of strain-induced martensite. It is essential However, since Ni is an expensive element, it causes an increase in raw material cost when a large amount is added. Accordingly, the upper limit may be limited to 14.0% in consideration of both the cost and efficiency of the steel.
  • the content of Mo is 2.0% or less (excluding 0).
  • Molybdenum (Mo) is an effective element for corrosion resistance of steel.
  • the content of molybdenum, a ferrite phase stabilizing element is excessive, the austenite phase stabilization degree decreases, making it difficult to secure deep machinability, and mechanical properties and corrosion resistance are lowered by precipitation of intermetallic compounds such as ⁇ phase.
  • the upper limit can be limited to 2.0%.
  • the content of Cu is 0.2 to 2.5%%.
  • Copper (Cu) is an austenite phase stabilizing element added instead of expensive nickel (Ni), and may be added in an amount of 0.2% or more to secure price competitiveness and deep workability. However, if the content is excessive, ⁇ -Cu precipitation phase with a low melting point may be formed, which may deteriorate the surface quality, so the upper limit may be limited to 2.5%.
  • Al 0.04% or less (excluding 0)
  • Ti 0.003% or less (excluding 0)
  • B 0.0025% or less (excluding 0)
  • P 0.035% or less
  • S It may further include one or more of 0.0035% or less.
  • the content of Al is 0.04% or less (excluding 0).
  • Aluminum (Al) is an element that lowers the oxygen content in molten steel as a strong deoxidizer. However, if the content is excessive, there is a problem that the sleeve defect of the cold-rolled strip occurs due to an increase in non-metallic inclusions, so the upper limit may be limited to 0.04%.
  • the content of Ti is 0.003% or less (excluding 0).
  • Titanium (Ti) preferentially combines with interstitial elements such as carbon (C) and nitrogen (N) to form precipitates (carbonitrides), thereby reducing the amount of solid solution C and solid solution N in steel and reducing the formation of a Cr depleted region It is an effective element for securing corrosion resistance of steel by suppressing it.
  • interstitial elements such as carbon (C) and nitrogen (N)
  • carbonitrides carbonitrides
  • the content of B is 0.0025% or less (excluding 0).
  • Boron (B) is an effective element for suppressing crack generation during casting to ensure good surface quality.
  • nitride (BN) may be formed on the surface of the product during the annealing/pickling process to deteriorate the surface quality, and thus the upper limit may be limited to 0.0025%.
  • the content of P is 0.035% or less.
  • Phosphorus (P) is an impurity that is unavoidably contained in steel and is an element that causes intergranular corrosion or inhibits hot workability.
  • the upper limit of the P content is managed as 0.035%.
  • the content of S is 0.0035% or less.
  • S is an impurity that is unavoidably contained in steel, and is an element that segregates at grain boundaries and is a major cause of inhibiting hot workability, so it is desirable to control its content as low as possible.
  • the upper limit of the S content is managed to 0.0035% or less.
  • the remaining component of the present invention is iron (Fe).
  • Fe iron
  • phase transformation increases the strength of the austenitic stainless steel until the material is damaged.
  • the following formula (1) was derived in consideration of the phase transformation caused by the deformation of the austenitic stainless steel.
  • the content of austenite stabilizing elements such as Mn, N, Cu, and Ni was increased to increase the degree of stabilization of the austenite phase. Accordingly, the phase transformation to the martensitic phase was suppressed, and work hardening of the austenitic stainless steel could be suppressed.
  • Cr, Si, Mo, Ni, Cu, C, and N mean wt% of each element.
  • Equation (1) satisfies the range of 63 or more.
  • the present inventors confirmed that the lower the value of Equation (1), the greater the change in strength during deformation due to external stress. Specifically, when the value of Equation (1) is less than 63, the austenitic stainless steel of the above alloy composition system exhibits abrupt strain-induced martensitic transformation behavior due to external deformation or plasticity non-uniformity due to twin crystal formation. . Accordingly, there is a problem in that the elongation of the austenitic stainless steel and the deep workability during multi-stage forming are reduced, so that the lower limit of Equation (1) is limited to 63.
  • 1 is a graph for explaining the relationship between stress-strain according to a tensile test of a material.
  • the increase in strength due to work hardening can be explained by the stress-strain curve of FIG. 1 .
  • the work-hardening exponent (n) indicating the degree of work-hardening ability can be expressed as follows.
  • ⁇ is the stress
  • K is the strength factor
  • ⁇ is the strain
  • the work hardening index n corresponds to the slope of the graph, and the larger the slope, the greater the increase in the strength of the material during plastic deformation.
  • Cr, Mo, Si, Ni, Mn, Cu, C, and N mean weight% of each element.
  • Equation (2) satisfies the range of 0 or more and 5.5 or less.
  • Equation (2) the higher the value of Equation (2), the easier the martensitic transformation due to external stress occurred, resulting in an excessive increase in strength and lowering of the formability.
  • the value of Equation (2) is 5.5 or more, there is a problem in that the strength increases continuously from tensile deformation to just before fracture, resulting in rapid fracture. Accordingly, there is a problem that the elongation cannot be secured, so the upper limit of Equation (2) is to be limited to 5.5.
  • Equation (2) when the value of Equation (2) was too low, it was confirmed that the cross-slip expression of the austenite phase due to external stress became difficult. Specifically, when the value of Equation (2) is less than 0, the austenitic stainless steel exhibits only planar slip behavior with respect to deformation, so that the accumulation of dislocations due to external stress proceeds, and plastic non-uniformity and high work hardening are exhibited. . Accordingly, there is a problem in that the elongation and yield ratio of the austenitic stainless steel decrease, and the lower limit of the value of Equation (2) is to be limited to 0.
  • FIG. 2 is a graph showing the relationship between stress-strain together with a work hardening index during a tensile test of austenitic stainless steel according to the disclosed embodiment.
  • the true strain value when the work hardening index is maximum may be 0.2 or less.
  • the hardening index decreases after the point A, even if the deformation proceeds. That is, it can be seen that the intensity gradually increases from point A to point B.
  • the point A in order to improve the deep workability of the austenitic stainless steel, paying attention to the point that it should be possible to secure a certain amount or more of deformation without excessive strength increase, the point A, where the increase in strength is maximum, is arranged at a relatively low amount of deformation, It was derived that it is necessary to obtain a certain amount of deformation from point A to reach point B.
  • the ferritic stainless steel with improved surface properties according to the disclosed embodiment has a true strain value of 0.2 or less when the work hardening index is maximum.
  • the difference between the true strain value when the work hardening index is maximum and the true strain value when the work hardening index is 0 is 0.11 or more.
  • the ferritic stainless steel with improved surface properties according to the disclosed embodiment satisfying the alloy element composition range and relational expression can secure an elongation of 35% or more and a tensile strength of 360 MPa or more.
  • the ferritic stainless steel with improved surface properties according to the disclosed embodiment does not crack when formed in two or more stages under the condition of a drawing ratio of 1.7 to 4.3, and cracks do not occur until forming in 5 stages.
  • Example 1 0.022 0.39 0.79 0.030 0.0011 21.4 10.3 0.5 0.8 0.206 0.003 0.002 0.0023 67.4 3.53
  • Example 2 0.020 0.40 0.70 0.032 0.0010 20.9 10.5 0.6 1.0 0.190 0.003 0.002 0.0023 67.4 3.22
  • Example 3 0.022 0.51 0.65 0.028 0.0010 21.2 10.6 0.5 0.7 0.200 0.003 0.002 0.0023 67.6 3.56
  • Example 4 0.025 0.39 0.80 0.008 0.0035 21.0 10.1 0.6 0.8 0.210 0.004 0.002 0.0022 67.1 2.71
  • Example 5 0.023 0.40 0.64 0.010 0.0005 21.3 10.3 0.6 0.9 0.210 0.004 0.002 0.0022 68.2 3.30
  • Example 6 0.029 0.38 0.81 0.034 0.0011 21.3 9.3 0.5 0.7 0.224 0.003 0.003 0.0022 65.5 3.
  • the number of multi-stage forming and work hardening index were measured. Specifically, in deep drawing forming, a blank with a diameter of 85 mm was used in 5 steps with a diameter of 1st punch 50mm, 2nd punch diameter 38mm, 3rd stage punch diameter 30mm, 4th stage punch diameter 24mm, and 5th stage punch diameter 20mm. did.
  • the drawing ratio for each stage is 1.7 in 1st stage, 2.2 in 2nd stage, 2.8 in 3rd stage, 3.5 in 4th stage, and 4.3 in 5th stage.
  • Example 1 5 0.37 0.17 0.29 0.12 450 37.4
  • Example 2 5 0.36 0.18 0.29 0.12 451 37.5
  • Example 3 5 0.36 0.18 0.29 0.12 450 37.5
  • Example 4 5 0.30 0.17 0.30 0.14 441 42.2
  • Example 5 5 0.27 0.17 0.30 0.13 467 41.0
  • Example 6 5 0.35 0.17 0.32 0.15 401 46.0
  • Example 7 5 0.35 0.18 0.32 0.15 404 46.7
  • Example 8 5 0.35 0.18 0.32 0.14 402 46.2
  • Example 9 5 0.36 0.17 0.32 0.15 386 45.6
  • Example 10 5 0.36 0.17 0.32 0.15 387 45.4
  • Example 11 5 0.36 0.17 0.32 0.15 388 45.5
  • Example 12 5 0.39 0.17 0.31 0.14 420 42.4
  • Example 13 5 0.39 0.17 0.31 0.14 421 42.5
  • Example 14 5 0.39 0.17 0.31 0.14 419 42.4
  • Example 15 5 0.38 0.15 0.30 0.15 441
  • Equation (1) was less than 63, resulting in a continuous increase in strength during work hardening, and the value of Equation (2) exceeded 5.5, resulting in martens due to deformation. Site transformation was active and cracks were frequent during multi-stage molding.
  • the alloy component and the relational expression when forming two or more stages under the condition of a drawing ratio of 1.7 to 4.3, cracks do not occur until five stages forming, an elongation of 35% or more, and a tensile strength of 360 MPa or more
  • the secured austenitic stainless steel can be manufactured.
  • the present invention can be used in various industrial fields such as fields involving deep machining.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention concerne un acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée. L'acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée, selon la présente invention, comprend, en % en poids, de 0,01 à 0,05 % de C, de 0,01 à 0,25 % de N, de 1,5 % ou moins de Si (à l'exclusion de 0), de 0,3 à 3,5 % de Mn, de 17,0 à 22,0 % de Cr, de 9,0 à 14,0 % de Ni, de 2,0 % ou moins de Mo (à l'exclusion de 0), de 0,2 à 2,5 % de Cu, et le reste étant du Fe et des impuretés inévitables, et répond à la formule (1). Formule (1) : Cr + Si + 2 * Mo + 3 * (Ni + Cu) + 50 * (C + N) ≥ 63, où Cr, Si, Mo, Ni, Cu, C et N signifient les % en poids de chaque élément.
PCT/KR2021/009569 2020-08-31 2021-07-23 Acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée WO2022045595A1 (fr)

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US18/019,187 US20230287549A1 (en) 2020-08-31 2021-07-23 Austenitic stainless steel with improved deep drawing
JP2023512177A JP2023539140A (ja) 2020-08-31 2021-07-23 深絞り性が向上したオーステナイト系ステンレス鋼
EP21861894.0A EP4177368A4 (fr) 2020-08-31 2021-07-23 Acier inoxydable austénitique présentant une aptitude à l'emboutissage profond améliorée
CN202180055978.6A CN116096934A (zh) 2020-08-31 2021-07-23 具有改善的深拉延性的奥氏体不锈钢

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0734203A (ja) * 1993-07-21 1995-02-03 Nippon Yakin Kogyo Co Ltd 熱間加工性に優れる軟質オーステナイト系ステンレス鋼
JP2002371339A (ja) * 2001-04-12 2002-12-26 Nisshin Steel Co Ltd 加工性，冷間鍛造性に優れた軟質ステンレス鋼板
KR20190020393A (ko) * 2017-08-21 2019-03-04 주식회사 포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
KR20190065720A (ko) * 2017-12-04 2019-06-12 주식회사 포스코 성형성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강
WO2020054999A1 (fr) * 2018-09-13 2020-03-19 주식회사 포스코 Acier inoxydable austénitique présentant une excellente expansibilité de tuyau et une excellente résistance à la fissuration liée au vieillissement

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05320756A (ja) * 1992-05-21 1993-12-03 Nippon Steel Corp 耐海水性に優れた高強度オーステナイト系ステンレス鋼の製造方法
JPH07113144A (ja) * 1993-10-18 1995-05-02 Nisshin Steel Co Ltd 表面性状に優れた非磁性ステンレス鋼及びその製造方法
JPH0853738A (ja) * 1994-08-10 1996-02-27 Nisshin Steel Co Ltd 抗菌性に優れたコイン用オーステナイト系ステンレス鋼
JP3464297B2 (ja) * 1994-08-31 2003-11-05 日新製鋼株式会社 高速温間絞り成形用オーステナイト系ステンレス鋼板およびその温間絞り成型法
JPH08283915A (ja) * 1995-04-12 1996-10-29 Nkk Corp 加工性に優れたオーステナイトステンレス鋼
JP2006291296A (ja) * 2005-04-11 2006-10-26 Nisshin Steel Co Ltd 深絞り性に優れたオーステナイト系ステンレス鋼
JP5116265B2 (ja) * 2006-07-13 2013-01-09 新日鐵住金ステンレス株式会社 強度及び延性に優れたオーステナイト系ステンレス圧延鋼板及びその製造方法
CN102330033B (zh) * 2010-07-15 2013-07-31 宝山钢铁股份有限公司 一种耐腐蚀性能优良的低成本奥氏体不锈钢
KR102173302B1 (ko) * 2018-11-12 2020-11-03 주식회사 포스코 비자성 오스테나이트계 스테인리스강 및 그 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0734203A (ja) * 1993-07-21 1995-02-03 Nippon Yakin Kogyo Co Ltd 熱間加工性に優れる軟質オーステナイト系ステンレス鋼
JP2002371339A (ja) * 2001-04-12 2002-12-26 Nisshin Steel Co Ltd 加工性，冷間鍛造性に優れた軟質ステンレス鋼板
KR20190020393A (ko) * 2017-08-21 2019-03-04 주식회사 포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
KR20190065720A (ko) * 2017-12-04 2019-06-12 주식회사 포스코 성형성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강
WO2020054999A1 (fr) * 2018-09-13 2020-03-19 주식회사 포스코 Acier inoxydable austénitique présentant une excellente expansibilité de tuyau et une excellente résistance à la fissuration liée au vieillissement

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4177368A4 *

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US20230287549A1 (en) 2023-09-14
JP2023539140A (ja) 2023-09-13
EP4177368A1 (fr) 2023-05-10
KR102448741B1 (ko) 2022-09-30
EP4177368A4 (fr) 2024-04-17

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