US20170349985A1 - Austenitic stainless steels excellent in flexibility - Google Patents

Austenitic stainless steels excellent in flexibility Download PDF

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Publication number
US20170349985A1
US20170349985A1 US15/539,874 US201515539874A US2017349985A1 US 20170349985 A1 US20170349985 A1 US 20170349985A1 US 201515539874 A US201515539874 A US 201515539874A US 2017349985 A1 US2017349985 A1 US 2017349985A1
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United States
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less
austenitic stainless
stainless steel
flexibility
steel excellent
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Abandoned
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US15/539,874
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English (en)
Inventor
Hyung Gu KANG
Gyu Jin JO
Dong Chul CHAE
Jae Hwa Lee
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Posco Holdings Inc
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Posco Co Ltd
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Assigned to POSCO reassignment POSCO ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: JO, GYU JIN, LEE, JAE HWA, KANG, HYUNG GU, CHAE, DONG CHUL
Publication of US20170349985A1 publication Critical patent/US20170349985A1/en
Abandoned legal-status Critical Current

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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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21D8/0221—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
    • C21D8/0247—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
    • C22C38/02—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
    • C22C38/58—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies 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
    • 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
    • C22C2202/00—Physical properties

Definitions

  • the present invention relates to austenitic stainless steels excellent in flexibility.
  • a metal material has a property that when subjected to strain such as tensile or compression, work hardening occurs and it becomes stronger as it is subjected to strain.
  • strain such as tensile or compression
  • the bending of pipe is a complex action of tension and compression, and as the degree of bending increases, the material becomes more hardened.
  • SUS 304 which is most widely used as austenitic stainless steel, has a severe degree of work hardening, and it is very difficult to bend piping by manpower in a space where air conditioner piping work is required.
  • TS-YS Work hardening is expressed as TS-YS, which is the difference between the yield strength (YS) indicating the strength at the start of material deformation and the tensile strength (TS) indicating the maximum strength due to maximization of work hardening of the material.
  • YS yield strength
  • TS tensile strength
  • Patent Literature 0001 KR 10-2010-0099726 A (2010.09.13)
  • An object of the present invention is to provide austenitic stainless steels excellent in flexibility by controlling the content of component elements affecting the degree of work hardening and controlling the size of crystal grains in order to solve such conventional problems.
  • an austenitic stainless steel excellent in flexibility is characterized by comprising, by weight percent, 0.1 to 0.65% of Si, 1.0 to 3.0% of Mn, 6.5 to 10.0% of Ni, 16.5 to 18.5% of Cr, 6.0% or less of Cu (excluding 0), 0.13% or less of (C+N) (excluding 0), and the remainder comprising Fe and unavoidable impurities, wherein the work hardening formula H1 defined by the following formula is 300 or less.
  • H1 ⁇ 459+79.8Si ⁇ 10.2Mn ⁇ 8.16Ni+48.0Cr ⁇ 13.2Cu+623(C+N)
  • the austenitic stainless steel excellent in flexibility according to the present invention is characterized by having the size of structure (D) of 20 to 40 ⁇ m.
  • an austenitic stainless steel excellent in flexibility is characterized by comprising, by weight percent, 0.1 to 0.65% of Si, 1.0 to 3.0% of Mn, 6.5 to 10.0% of Ni, 16.5 to 18.5% of Cr, 6.0% or less of Cu (excluding 0), 0.13% or less of (C+N) (excluding 0), and the remainder comprising Fe and unavoidable impurities, wherein the work hardening formula H2 defined by the following formula is 300 or less.
  • H2 4.27+0.875( ⁇ 459+79.8Si ⁇ 10.2Mn ⁇ 8.16Ni+48.0Cr ⁇ 13.2Cu+623(C+N)) ⁇ 287D (D: the size of structure)
  • the size of structure (D) is characterized by being 20 to 300 ⁇ m.
  • An austenitic stainless steel excellent in flexibility according to the present invention is characterized by comprising, by weight percent, 0.1 to 0.65% of Si, 1.0 to 3.0% of Mn, 6.5 to 10.0% of Ni, 16.5 to 18.5% of Cr, 6.0% or less of Cu (excluding 0), 0.13% or less of (C+N) (excluding 0), and the remainder comprising Fe and unavoidable impurities, wherein M d30 defined by the following formula is 0 or less.
  • M d30 is ⁇ 100 to 0.
  • the difference value between TS (tensile strength) and YS (yield strength) is characterized by being 300 MPa or less.
  • the present invention has an advantage that austenitic stainless steels excellent in flexibility can be produced by controlling the content of elements, the size of crystal grains, and the like.
  • FIG. 1 is a diagram showing a correlation between the work hardening formula H1 and actually measured values of work hardening degree
  • FIG. 2 is a diagram showing a change of the work hardening formula H1 according to the size of crystal grains:
  • FIGS. 3 to 5 show size distributions of crystal grains:
  • FIG. 6 is a diagram showing a correlation between the modified work hardening formula H2 and actually measured values of the work hardening degree
  • FIG. 7 is a diagram showing a correlation between the austenite stabilization index and actually measured values of the work hardening degree.
  • An austenitic stainless steel according to the present invention is characterized by containing, by weight percent, 0.1 to 0.65% of Si, 1.0 to 3.0% of Mn, 6.5 to 10.0% of Ni, 16.5 to 18.5% of Cr, 6.0% or less of Cu (excluding 0), 0.13% or less of (C+N) (excluding 0), and the remainder comprising Fe and unavoidable impurities.
  • C+N should be added to 0.13 wt % or less.
  • C and N not only harden the austenitic stainless steel as interstitial solid solution strengthening elements but also increase the work hardening degree of the material by hardening the strain induced martensite generated during processing if the contents of C and N are high. Therefore, there is a need to limit the content of C and N, and in the present invention, the content of C+N is limited to 0.13% or less.
  • Si is added in a controlled amount with the range of 0.1 to 0.65 wt %.
  • Si is an element added essentially for deoxidation, 0.1% or more is added.
  • the upper limit is limited to 0.65%.
  • Mn is added in a controlled amount with the range of 1.0 to 3.0 wt %.
  • Mn which is an element not only added essentially for deoxidation but also increases the degree of stabilization of the austenite phase, is added at 1.0% or more for maintaining the austenite balance.
  • the addition of an excessively high content of Mn reduces the corrosion resistance of the material, so the upper limit is limited to 3.0%.
  • Ni is added in a controlled amount with the range of 6.5 to 10.0 wt %.
  • Ni is not only effective for improving the corrosion resistance such as pitting corrosion resistance by being added with Cr in combination, but also can increase softening of austenite steel when its content is increased.
  • Ni is an element contributing to improvement of phase stability of austenitic stainless steel, and is added at 6.5% or more in order to maintain an austenite balance.
  • the addition of an excessively high content of Ni results in an increase in the cost of the steel, so the upper limit is limited to 10.0%.
  • Cr is added in a controlled amount with the range of 16.5 to 18.5 wt %.
  • Cr is an indispensable element for improving the corrosion resistance, and in order to be used for general purpose, 16.5% or more of Cr should be added. However, the addition of an excessively high content of Cr causes austenite phase hardening and increases the cost, so the upper limit is limited to 18.5%.
  • Cu is added in a controlled amount with the range of 6.0 wt % or less.
  • Cu can cause softening of the austenite steel.
  • the addition of an excessively high content of Cu lowers the hot workability and can rather harden the austenite phase, so the upper limit is limited to 6.0%.
  • the component control method provided by the present invention is important.
  • the following description will be made with reference to the embodiments of the present invention.
  • the materials described in the following embodiments were prepared by preparing ingots with a 150 mm thickness, heating them to 1,250° C., hot rolling them to 3 mm, and then heat treating them at 1,100° C. for 60 seconds or more.
  • such a manufacturing method does not limit the characteristics of the material provided in the present invention, but merely adopts one of the conventional methods of manufacturing austenitic stainless steel, and is merely an example of producing a material for evaluating characteristics.
  • the characteristics of the material change depending on the component control method provided by the present invention.
  • the yield strength YS and the tensile strength TS are values obtained by uniaxially tensioning the material.
  • H1 shown in Table 1 is defined by the following formula.
  • H1 ⁇ 459+79.8Si ⁇ 10.2Mn ⁇ 8.16Ni+48.0Cr ⁇ 13.2Cu+623(C+N)
  • the H1 values are defined using the component elements constituting the present invention, and the correlation between the H1 values and the actually measured TS-YS values were analyzed.
  • FIG. 1 it can be seen that the relationship between the H1 values obtained through the component control and the actually measured TS-YS values is shown, and the above description is implemented. In particular, as shown by a dotted line, a linearly smooth relationship is established therebetween. Therefore, it can be seen that even if the lower limit of the H1 value is not set in the present invention, it is possible to manufacture an austenitic steel having more excellent flexibility through production of a material having a lower H1 value.
  • the crystal grain size of the austenitic stainless steel produced by a conventional manufacturing process is generally 30 ⁇ 10 ⁇ m.
  • the crystal grain size (D) of the austenitic stainless steel excellent in flexibility of the present invention is also present in the interval of 30 ⁇ 10 ⁇ m, and it can be seen that when H1 is obtained as 329 as in Comparative Example 1 of Table 2, the actual TS-YS value is obtained as 328, indicating that the flexibility is not good.
  • FIGS. 3 to 5 show size distributions of crystal grains, in which FIG. 3 is a structure photograph showing the crystal grain size of the austenitic stainless steel according to the following Invention Example 6, FIG. 4 is a structure photograph showing the crystal grain size of the austenitic stainless steel according to the following Comparative Example 6, and FIG. 5 is a structure photograph showing the crystal grain size of the austenitic stainless steel according to the following Invention Example 17.
  • a modified work hardening formula H2 is provided so as to obtain a material having a low work hardening degree even when the crystal grain size is larger than usual.
  • austenitic stainless steels excellent in flexibility can be produced by controlling the range of the modified work hardening formula H2 to 300 MPa or less.
  • Table 3 shows the component contents of Invention Examples 17 to 21 and Comparative Examples 4 to 6 disclosed in Table 2.
  • the TS-YS values may be limited by the following austenite stability M d30 .
  • M d30 In order to maintain the M d30 in the range of 0 or less, Si, Mn, Ni, Cu and Cr which are the main additive elements must be added.
  • M d30 -related component parameters for maintaining the TS-YS values at 300 MPa or less are presented.
  • the TS-YS values can be maintained at 300 MPa or less, which indicates that the flexibility is improved.
  • the component element contents should be further increased.
  • the lower limit value is preferably limited to ⁇ 100.
  • the austenitic stainless steels excellent in flexibility according to the embodiments of the present invention are applicable to air conditioner refrigerant piping and the like for domestic use and automobiles.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Materials For Medical Uses (AREA)
US15/539,874 2014-12-26 2015-12-01 Austenitic stainless steels excellent in flexibility Abandoned US20170349985A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
KR1020140191165A KR101659186B1 (ko) 2014-12-26 2014-12-26 가요성이 우수한 오스테나이트계 스테인리스강
KR10-2014-0191165 2014-12-26
PCT/KR2015/012973 WO2016104974A1 (ko) 2014-12-26 2015-12-01 가요성이 우수한 오스테나이트계 스테인리스강

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EP (1) EP3239341A4 (ko)
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KR (1) KR101659186B1 (ko)
CN (1) CN107429367A (ko)
WO (1) WO2016104974A1 (ko)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180106557A1 (en) * 2016-03-28 2018-04-19 Lg Electronics Inc. Stainless steel and pipe made thereof
US20190010588A1 (en) * 2015-12-23 2019-01-10 Posco Austenitic stainless steel having improved processability

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101923922B1 (ko) * 2016-12-23 2018-11-30 주식회사 포스코 표면특성이 우수한 오스테나이트계 스테인리스강 가공품 및 이의 제조 방법
KR20180104513A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104507A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104514A (ko) * 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104511A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104509A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104520A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104506A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR102357608B1 (ko) * 2017-03-13 2022-02-04 엘지전자 주식회사 공기 조화기
KR20180104508A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104521A (ko) 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180104519A (ko) * 2017-03-13 2018-09-21 엘지전자 주식회사 공기 조화기
KR20180111416A (ko) 2017-03-31 2018-10-11 엘지전자 주식회사 연성 스테인리스 강관
KR20190000254A (ko) 2017-06-22 2019-01-02 엘지전자 주식회사 공기 조화기
KR102419898B1 (ko) * 2017-06-26 2022-07-12 엘지전자 주식회사 가스 히트 펌프 시스템
KR102364389B1 (ko) * 2017-09-27 2022-02-17 엘지전자 주식회사 공기 조화기
US11457783B2 (en) 2019-06-05 2022-10-04 Lg Electronics Inc. Cleaner

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030183292A1 (en) * 2000-08-01 2003-10-02 Masato Otsuka Stainless steel oil feeding pipe

Family Cites Families (28)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2714987B2 (ja) * 1989-08-30 1998-02-16 日新製鋼株式会社 高級洋食器用非磁性オーステナイト系ステンレス鋼
JPH0770705A (ja) * 1993-09-03 1995-03-14 Aichi Steel Works Ltd 熱膨張特性に優れたオーステナイトステンレス鋼
JP2946274B2 (ja) * 1993-11-30 1999-09-06 株式会社栗本鐵工所 オーステナイト系ステンレス鋼製のｔ頭ボルトおよびその製造方法
JP3637991B2 (ja) * 1996-03-29 2005-04-13 日新製鋼株式会社 軟質オーステナイト系ステンレス鋼
JPH09310155A (ja) * 1996-05-16 1997-12-02 Nkk Corp 加工後の表面特性に優れたオーステナイトステンレス鋼
JPH1036922A (ja) * 1996-07-23 1998-02-10 Kawasaki Steel Corp オーステナイト系ステンレス鋼板の結晶粒径制御方法
JPH11181550A (ja) * 1997-12-17 1999-07-06 Sanyo Special Steel Co Ltd 冷間加工性の良好なオーステナイト系ステンレス鋼
JPH11350089A (ja) * 1998-06-12 1999-12-21 Nisshin Steel Co Ltd 抗菌性に優れ高加工性を具備したオーステナイト系ステンレス鋼およびその製造方法
JP2000248339A (ja) * 1999-02-26 2000-09-12 Nisshin Steel Co Ltd 加工性及び耐食性に優れたオーステナイト系快削ステンレス鋼
JP2000303152A (ja) * 1999-04-20 2000-10-31 Nisshin Steel Co Ltd 抗菌性に優れ、２次加工での穴拡げ加工性に優れたオーステナイト系ステンレス鋼およびその製造方法
JP3691341B2 (ja) * 2000-05-16 2005-09-07 日新製鋼株式会社 精密打抜き性に優れたオーステナイト系ステンレス鋼板
ES2250443T3 (es) * 2000-08-01 2006-04-16 Nisshin Steel Co., Ltd. Deposito de carburante en acero inoxidable para automovil.
JP2002206148A (ja) * 2001-01-09 2002-07-26 Nisshin Steel Co Ltd 加工割れ感受性が低いオーステナイト系ステンレス鋼板およびその製造方法
JP3827986B2 (ja) * 2001-10-16 2006-09-27 日新製鋼株式会社 ステンレス鋼製フレキシブル管又はダクト管
JP4907151B2 (ja) * 2005-11-01 2012-03-28 新日鐵住金ステンレス株式会社 高圧水素ガス用オ−ステナイト系高Ｍｎステンレス鋼
JP5165236B2 (ja) * 2006-12-27 2013-03-21 新日鐵住金ステンレス株式会社 衝撃吸収特性に優れた構造部材用ステンレス鋼板
JP2008208430A (ja) * 2007-02-27 2008-09-11 Nippon Steel & Sumikin Stainless Steel Corp 軟質オーステナイト系ステンレス鋼およびその製造方法
US8337749B2 (en) * 2007-12-20 2012-12-25 Ati Properties, Inc. Lean austenitic stainless steel
EP2245202B1 (en) 2007-12-20 2011-08-31 ATI Properties, Inc. Austenitic stainless steel low in nickel containing stabilizing elements
JP5448023B2 (ja) * 2008-02-12 2014-03-19 独立行政法人物質・材料研究機構 塑性加工性に優れた鋼細線又は薄帯鋼板
JP5308726B2 (ja) * 2008-06-17 2013-10-09 新日鐵住金ステンレス株式会社 微細粒組織を有するプレス成形用オーステナイト系ステンレス鋼板およびその製造方法
KR20100069875A (ko) * 2008-12-17 2010-06-25 주식회사 포스코 열간가공성이 우수한 고망간 오스테나이트계 스테인리스강
JP5500960B2 (ja) * 2009-12-01 2014-05-21 新日鐵住金ステンレス株式会社 耐応力腐食割れ性と加工性に優れた微細粒オーステナイト系ステンレス鋼板
KR101177488B1 (ko) * 2009-12-29 2012-08-27 주식회사 포스코 초고강도 고내식 스테인리스 합금 및 그 제조방법
CN103534373B (zh) * 2011-03-01 2017-05-17 新日铁住金株式会社 激光加工用金属板和激光加工用不锈钢板的制造方法
JP5920691B2 (ja) * 2011-06-22 2016-05-18 日本精線株式会社 ソーワイヤー用の高強度金属細線とその製造方法、並びに該金属細線を用いたソーワイヤー
KR101554771B1 (ko) * 2012-12-20 2015-09-21 주식회사 포스코 고연성 린 듀플렉스 스테인리스강.
JP6340870B2 (ja) * 2014-03-31 2018-06-13 新日鐵住金株式会社 オーステナイト系ステンレス鋼

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030183292A1 (en) * 2000-08-01 2003-10-02 Masato Otsuka Stainless steel oil feeding pipe

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20190010588A1 (en) * 2015-12-23 2019-01-10 Posco Austenitic stainless steel having improved processability
US20180106557A1 (en) * 2016-03-28 2018-04-19 Lg Electronics Inc. Stainless steel and pipe made thereof
US10627168B2 (en) * 2016-03-28 2020-04-21 Lg Electronics Inc. Stainless steel and pipe made thereof

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