US3910788A - Austenitic stainless steel - Google Patents

Austenitic stainless steel Download PDF

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Publication number
US3910788A
US3910788A US461335A US46133574A US3910788A US 3910788 A US3910788 A US 3910788A US 461335 A US461335 A US 461335A US 46133574 A US46133574 A US 46133574A US 3910788 A US3910788 A US 3910788A
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percent
steel
solid solution
austenitic stainless
stainless steel
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Expired - Lifetime
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US461335A
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English (en)
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Tokio Fujioka
Kazuo Hoshino
Kenjiro Ito
Takashi Igawa
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Nippon Steel Nisshin Co Ltd
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Nisshin Steel Co Ltd
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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

Definitions

  • AISI 301 is preferably used as the material for stretching, because when this steel is subjected to plastic deformation, strain-induced martensite is easily formed, which prevents local neckings and gives remarkable elongation to the material.
  • this steel undergoes drawing in which compression strain is given to the material and the material retains tension stress after drawing, delayed cracking occurs within a short period of time when the steel is simply allowed to stand in the at mosphere after drawing.
  • AISI 305 is more stable against strain-induced martenistic transformation and less sensitive to delayed cracking.
  • A131 305 is inferior in stretchability and deep drawability because of its lower Work hardening coefficient.
  • the lower work hardening coefficient is due to high Ni content of the steel, which means that the material is expensive, too.
  • austenitic stainless steels of this kind in which a portion of Ni is replaced by Cu are known.
  • Cu is effective for inhibiting the strain-induced martensitic transformation as well as Ni.
  • the C content is defined as less than 0. 15 percent, 0.08 percent and 0.12 percent respectively. But they usually contain 0.04 percent or more C and 0.015 percent or more N and the total of the two elements is 0.055 percent or more. In the steel of U.S. Pat. No. 3,282,684, 0.04-0.10 percent N is intentionally added.
  • the decrease in work hardening coefficient caused by decrease in the contents of C and N in the solid solution state is compensated for by increase in the contents of Si, Mn and Cu, and thus an austenitic stainless steel which has excellent formability and is highly resistant to delayed cracking after deep drawing is provided at the price of the same level as that of A18] 304.
  • stainless steel with excellent drawability and stretchability and high resistance to delayed cracking essentially consisting of 10-25 percent Si, l.55.0 percent Mn, 15-19 percent Cr, 10-40 percent Cu, 6.0-9.0 percent Ni, not more than 0.06 percent C, not more than 0.03 percent N and balance Fe with incidental impurities, in which the total content of C and N in the solid solution state is less than 0.04 percent is provided.
  • Si improves work hardening property of austenite phase itself, and the effect is proportional to the content.
  • the austenitic stainless steel, in which the content of C and N in the solid solution state is restricted. is inferior in work hardening coefficient. Therefore, in this invention Si is an indispensable element that conpensates for the drop of the work hardening coefficient. Also Si improves resistance to pitting corrosion. At least 1.0 percent Si is required to accomplish this object. But Si in excess of 2.5 percent will cause formation of S-ferrite, which impairs hot workability or causes hot cracking.
  • the Si content is preferably 1.0-2.0 percent, and more preferably 1.2-1.8 percent.
  • Mn has the effect of inhibiting strain-induced martensitic transformation of the austenite phase as well as Ni, but is different from Ni in that it strengthens the strain-induced rnartsite and enhances work hardening coefficient and improves stretchability and drawability of the material.
  • the S-ferrite-inhibiting effect of Mn is not so strong as Ni. And a rather high percentage thereof is lost during steel making. So this element does not contribute so much to cost cutting as expected from the difference in prices of these elements.
  • the reasonable content of Mn is within a range of 1.0-5.0 percent, preferably 1.5-3.0 percent and more preferably 1.8-2.8 percent.
  • Cu has the effect of inhibiting straininduced martensitic transformation of austenite phase and strengthens the strain-induced rnartsite, and improves work hardening coefficient of the material as the result.
  • too much Cu impairs hot workability.
  • the reasonable content of Cu is 1.0-4.0 percent, preferably 1.0-3.0 percent and more preferably 1.5-2.5 percent.
  • Ni which is an expensive element, does not contribute so much to work hardening property of the austenite phase or strain-induced rnartsite per se and therefore it is desirable to use this element at a content as low as possible.
  • the reasonable content, thereof, is 6.0-9.0 percent, preferably 6.5-8.5 percent and more preferably 6.7-8 percent.
  • Cr contributes to corrosion resistance in proportion to the content thereof. But at too high content, it causes formation of S-ferrite and impairs hot workability. Thus the Cr content is limited to 15-19 percent, the preferable content range being 15.5-17.5 percent and more preferably range is 16-17 percent.
  • the total content of C and N in the solid solution state must be less than 0.04 percent. This can be achieved by reducing the amounts of C and N by the so-called Vacuum Oxygen Decarbonization Process or Argon Oxygen Decarbonization Process. In the ordinary electric steel making process the total amount of C and N cannot be reduced to less than 0.04 percent, so up to 0.5 percent of Al and/or Ti is added to the melt so as to reduce C and N in the solid solution state to less than 0.04 percent.
  • A1 fixes N as MN and is effective to reduce N in the solid solution state when the N content is high. But high 4 content thereof contributes to formation of S-ferrite.
  • Ti fixes C and N as Ti(C, N) and is effective to reduce C and N in the solid solution state. Therefore the content of Al and/or Ti is limited to less than 0.5 percent and preferably 0.3 percent.
  • the total amount of C (both of the fixed and that in the solid solution state) should be 0.06 percent or less.
  • the total amount of N (both of the fixed and that in the solid solution state) should be 0.03 percent or less.
  • the amounts of the total C and the total N should preferably be not more than 0.06 percent and 0.03 percent respectively.
  • the S content should be 0.03 percent or less, and the P content should be 0.04 percent or less.
  • the austenitic stainless steel of this invention can be made by the Vacuum Oxygen Decarbonization Process or Argon Oxygen Decarbonization Process or by the ordinary electric steel making with the aid of Al and/or Ti as mentioned above. And there is no necessity of explaining the manufacturing process for the steel in detail here.
  • the austenitic stainless steel of this invention is characterized in that it is provided with excellent drawability and stretchability and is highly resistant to delayed cracking.
  • the Si present is the residual of the Si that was used for deoxidation and does not function at all to improve the steel properties.
  • Si is intentionally added for the enhancement of work hardening coefficient and it is contained in an amount of 1.0 percent or more.
  • N is intentionally added in an amount of 0.04-0.10 percent in order to stabilize its austenite phase against the strain-induced martensitic transformation.
  • the N content is defined as not more than 0.03 percent and the C content is defmed as not more than 0.15 percent. But in the specification proper, it is explained that the C content should be at least 0.04 percent and the preferred range is 0.05-0.08 percent. And none of the examples is the total content of C and N less than 0.08 percent.
  • the total content ofC and N of 48A02, 48AO3 and 48A09 is in excess of 6 delayed cracking, there is significant difference between them. That is to say, the austenite phase of AlSl 305 is markedly stable against the strain-induced martensitic transformation as duly anticipated from the ex- 0.04 percent. But these numerical values include the 5 perimental results of Schaller et al. On the other hand, amounts of the fixed C and N. That is.
  • the steel of this invention and the steel of AlSl 305 are similar in that they are very resistant to attached drawing.
  • the specimens shown in the drawing (photograph) are of the steel of this invention (48M0l AlSl 301, Cr-Ni-Cu-N steel and Cr'Ni-Cu steel from the left to the right respectively.
  • the sample sheet of 48M01 did not suffer delayed cracking even after having undergone drawing of drawing ratio 3.10.
  • the sample sheet of Cr-Ni-Cu-N steel suffered slight delayed cracking after having undergone drawing of drawing ratio 2.41.
  • the steel sheet of Cr-Ni-Cu steel suffered delayed cracking after having undergone drawing of drawing ratio 2.32.
  • this invention provides a novel austenitic stainless steel which is provided with excellent drawability and stretchability and remarkably resistant to delayed cracking, by restricting the total content of C and N in solid solution state to less than 0.04 percent and adding rather high amounts of Si and Mn.
  • the steel of this invention can be supplied at the price of the same level as that of A181 304.
  • Austenitic stainless steel that is provided with excellent drawability and stretchability and is highly resistant to delayed cracking essentially consisting of 1.0-2.5 percent Si, 1.5-5.0 percent Mn, 1.0-4.0 percent Cu, 6.0-9.0 percent Ni, 15.0-19.0 percent Cr, -0.5 percent of at least one of Al and Ti, not more than 0.06 percent C, not more than 0.03 percent N and balance Fe and incidental impurities, in which the total 8 amount ol'(" 11ml l ⁇ in the solid solution state is less than 0.04 percent.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
US461335A 1973-04-21 1974-04-16 Austenitic stainless steel Expired - Lifetime US3910788A (en)

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JP48044656A JPS5129854B2 (enrdf_load_stackoverflow) 1973-04-21 1973-04-21

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US3910788A true US3910788A (en) 1975-10-07

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JP (1) JPS5129854B2 (enrdf_load_stackoverflow)
GB (1) GB1419736A (enrdf_load_stackoverflow)

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4162930A (en) * 1976-03-30 1979-07-31 Nippon Steel Corporation Austenitic stainless steel having excellent resistance to intergranular and transgranular stress corrosion cracking
US4390367A (en) * 1980-06-25 1983-06-28 Mannesmann Aktiengesellschaft High-alloyed steel being resistive to corrosion by natural gas
US4816085A (en) * 1987-08-14 1989-03-28 Haynes International, Inc. Tough weldable duplex stainless steel wire
FR2728271A1 (fr) * 1994-12-20 1996-06-21 Inst Francais Du Petrole Acier anti-cokage
EP1091006A1 (en) * 1999-10-04 2001-04-11 Hitachi Metals, Ltd. Strain-induced type martensitic steel having high hardness and high fatigue strength
WO2003056052A1 (en) * 2001-12-11 2003-07-10 Sandvik Ab Precipitation hardenable austenitic steel
US20030183292A1 (en) * 2000-08-01 2003-10-02 Masato Otsuka Stainless steel oil feeding pipe
WO2008009722A1 (de) * 2006-07-20 2008-01-24 Actech Gmbh Nichtrostender austenitischer stahlformguss, verfahren zu dessen herstellung, und seine verwendung
US20100233015A1 (en) * 2006-12-27 2010-09-16 Junichi Hamada Stainless Steel Sheet for Structural Components Excellent in Impact Absorption Property
RU2691446C1 (ru) * 2015-07-27 2019-06-13 Зальцгиттер Флахшталь Гмбх Высоколегированная сталь и способ производства труб из этой стали при помощи формования внутренним высоким давлением
CN111876653A (zh) * 2020-07-27 2020-11-03 四川六合特种金属材料股份有限公司 一种纯净奥氏体不锈钢的制备方法

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5129313A (en) * 1974-09-06 1976-03-12 Nippon Steel Corp Nanshitsudekakosei taishokuseinosuguretaoosutenaitogatasutenresuko
JPS52110215A (en) * 1976-03-13 1977-09-16 Nippon Metal Ind Deep drawing austenite stainless steel
JPH07103445B2 (ja) * 1986-04-30 1995-11-08 日新製鋼株式会社 ブレ−ドの基板用ステンレス鋼
JPH0248614B2 (ja) * 1987-07-15 1990-10-25 Nippon Yakin Kogyo Co Ltd Netsukankakoseinisugurerukotaishokuseioosutenaitosutenresukotosonoseizohoho
DE102005024029B3 (de) 2005-05-23 2007-01-04 Technische Universität Bergakademie Freiberg Austenitischer Leichtbaustahl und seine Verwendung
FI125442B (fi) 2010-05-06 2015-10-15 Outokumpu Oy Matalanikkelinen austeniittinen ruostumaton teräs ja teräksen käyttö

Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2150901A (en) * 1938-02-01 1939-03-21 Arness William Bell Rustless iron
US3152934A (en) * 1962-10-03 1964-10-13 Allegheny Ludlum Steel Process for treating austenite stainless steels
US3154412A (en) * 1961-10-05 1964-10-27 Crucible Steel Co America Heat-resistant high-strength stainless steel
US3159480A (en) * 1962-11-28 1964-12-01 Int Nickel Co Austenitic chromium-nickel stainless steels resistant to stress-corrosion cracking
US3282686A (en) * 1965-02-01 1966-11-01 Armco Steel Corp Stainless steel and articles
US3303023A (en) * 1963-08-26 1967-02-07 Crucible Steel Co America Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
US3337331B1 (enrdf_load_stackoverflow) * 1964-01-29 1967-08-22
US3523788A (en) * 1967-06-02 1970-08-11 United States Steel Corp Austenitic stainless steel of improved stress corrosion resistance
US3563728A (en) * 1968-03-12 1971-02-16 Westinghouse Electric Corp Austenitic stainless steels for use in nuclear reactors
US3697258A (en) * 1969-10-13 1972-10-10 Int Nickel Co Highly corrosion resistant maraging stainless steel
US3795507A (en) * 1972-03-31 1974-03-05 Armco Steel Corp Semi-austenitic cr-ni-al-cu stainless steel

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2150901A (en) * 1938-02-01 1939-03-21 Arness William Bell Rustless iron
US3154412A (en) * 1961-10-05 1964-10-27 Crucible Steel Co America Heat-resistant high-strength stainless steel
US3152934A (en) * 1962-10-03 1964-10-13 Allegheny Ludlum Steel Process for treating austenite stainless steels
US3159480A (en) * 1962-11-28 1964-12-01 Int Nickel Co Austenitic chromium-nickel stainless steels resistant to stress-corrosion cracking
US3303023A (en) * 1963-08-26 1967-02-07 Crucible Steel Co America Use of cold-formable austenitic stainless steel for valves for internal-combustion engines
US3337331B1 (enrdf_load_stackoverflow) * 1964-01-29 1967-08-22
US3337331A (en) * 1964-01-29 1967-08-22 Sandvikens Jernverks Ab Corrosion resistant steel alloy
US3282686A (en) * 1965-02-01 1966-11-01 Armco Steel Corp Stainless steel and articles
US3523788A (en) * 1967-06-02 1970-08-11 United States Steel Corp Austenitic stainless steel of improved stress corrosion resistance
US3563728A (en) * 1968-03-12 1971-02-16 Westinghouse Electric Corp Austenitic stainless steels for use in nuclear reactors
US3697258A (en) * 1969-10-13 1972-10-10 Int Nickel Co Highly corrosion resistant maraging stainless steel
US3795507A (en) * 1972-03-31 1974-03-05 Armco Steel Corp Semi-austenitic cr-ni-al-cu stainless steel

Cited By (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4162930A (en) * 1976-03-30 1979-07-31 Nippon Steel Corporation Austenitic stainless steel having excellent resistance to intergranular and transgranular stress corrosion cracking
US4390367A (en) * 1980-06-25 1983-06-28 Mannesmann Aktiengesellschaft High-alloyed steel being resistive to corrosion by natural gas
US4816085A (en) * 1987-08-14 1989-03-28 Haynes International, Inc. Tough weldable duplex stainless steel wire
FR2728271A1 (fr) * 1994-12-20 1996-06-21 Inst Francais Du Petrole Acier anti-cokage
EP0718415A1 (fr) * 1994-12-20 1996-06-26 Institut Francais Du Petrole Aciers anti-cokage
US5693155A (en) * 1994-12-20 1997-12-02 Institut Francais Du Petrole Process for using anti-coking steels for diminishing coking in a petrochemical process
EP1091006A1 (en) * 1999-10-04 2001-04-11 Hitachi Metals, Ltd. Strain-induced type martensitic steel having high hardness and high fatigue strength
US6562153B1 (en) 1999-10-04 2003-05-13 Hitachi Metals, Ltd. Strain-induced type martensitic steel having high hardness and having high fatigue strength
US20030183292A1 (en) * 2000-08-01 2003-10-02 Masato Otsuka Stainless steel oil feeding pipe
US6851455B2 (en) * 2000-08-01 2005-02-08 Nisshin Steel Co., Ltd. Stainless steel oil feeding pipe
WO2003056053A1 (en) * 2001-12-11 2003-07-10 Sandvik Ab Precipitation hardenable austenitic steel
WO2003056052A1 (en) * 2001-12-11 2003-07-10 Sandvik Ab Precipitation hardenable austenitic steel
US20050126661A1 (en) * 2001-12-11 2005-06-16 Gustaf Zetterholm Precipitation hardenable austenitic steel
US20070041863A1 (en) * 2001-12-11 2007-02-22 Sandvik Intellectual Property Ab Precipitation hardenable austenitic steel
JP2009543952A (ja) * 2006-07-20 2009-12-10 アクテック ゲーエムベーハー オーステナイト系ステンレス鋳鋼製品、その製造および使用方法
WO2008009722A1 (de) * 2006-07-20 2008-01-24 Actech Gmbh Nichtrostender austenitischer stahlformguss, verfahren zu dessen herstellung, und seine verwendung
US20090324441A1 (en) * 2006-07-20 2009-12-31 Actech Gmbh Austenitic stainless cast steel part, method for production and use thereof
CN101490297B (zh) * 2006-07-20 2012-02-01 Actech有限公司 奥氏体不锈钢铸件的制作方法和应用
RU2451763C2 (ru) * 2006-07-20 2012-05-27 Актех Гмбх Нержавеющая аустенитная литая сталь, способ ее получения и применение
US20100233015A1 (en) * 2006-12-27 2010-09-16 Junichi Hamada Stainless Steel Sheet for Structural Components Excellent in Impact Absorption Property
EP2060646B1 (en) 2006-12-27 2015-06-17 Nippon Steel & Sumikin Stainless Steel Corporation Stainless steel sheet for structural members excellent in impact -absorbing characteristics
RU2691446C1 (ru) * 2015-07-27 2019-06-13 Зальцгиттер Флахшталь Гмбх Высоколегированная сталь и способ производства труб из этой стали при помощи формования внутренним высоким давлением
CN111876653A (zh) * 2020-07-27 2020-11-03 四川六合特种金属材料股份有限公司 一种纯净奥氏体不锈钢的制备方法

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Publication number Publication date
JPS5129854B2 (enrdf_load_stackoverflow) 1976-08-27
JPS49130309A (enrdf_load_stackoverflow) 1974-12-13
GB1419736A (en) 1975-12-31

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