EP0241553B1 - Hochfester rostfreistahl und dessen herstellung - Google Patents

Hochfester rostfreistahl und dessen herstellung Download PDF

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EP0241553B1
EP0241553B1 EP85905113A EP85905113A EP0241553B1 EP 0241553 B1 EP0241553 B1 EP 0241553B1 EP 85905113 A EP85905113 A EP 85905113A EP 85905113 A EP85905113 A EP 85905113A EP 0241553 B1 EP0241553 B1 EP 0241553B1
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Prior art keywords
steel
stainless steel
less
corrosion resistance
strength
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EP85905113A
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English (en)
French (fr)
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EP0241553A4 (de
EP0241553A1 (de
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Yoshinobu Honkura
Yoshihiro 3-8 Togane Nakajima
Touru Matsuo
Koji Murata
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Aichi Steel Corp
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Aichi Steel Corp
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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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • 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

  • This invention relates to high strength, corrosion resistant austenitic stainless steel for use in chemical, seawater, nuclear power plants, etc.
  • Austenitic stainless steel is in wide use as it offers excellent corrosion resistance - heat resistance, workability and mechanical properties.
  • SUS304, SUS316, SUS304L and SUS316L are typical of the sort.
  • SUS304LN and SUS316LN showed over 25 kg/mm2 of proof stress, and SUS304N and SUS316 over 28 kg/mm2, i.e., the results were found unsatisfactory. In the case of SUS304N2, the stress was over 35 kg/mm2, which was relatively high but still considered not always satisfactory.
  • SUS316LN, 316N, 316L, 316, 304LN, 304N1, 304 and 304L do not have a sufficient strength, and SUS304N2 has problems and disadvantages in that cracks are produced during hot working and sufficient corrosion resistance is not obtained. Accordingly, they have not yet been put to practical use.
  • SUS304N, SUS304N2 and SUS316N are inferior in strength, whereas SUS304N, SUS304N2 and SUS316N are inferior in intergranular corrosion resistance, sensitivity to anti-stress corrosion cracking. Furthermore, problematical is sharp reduction in their corrosion resistance after welding.
  • the present invention is intended to remedy the shortcomings of conventional stainless steel and has succeeded in not only providing satisfactory strength with, and improving the corrosion resistance of, austenitic stainless steel by adding a proper quantity of N, Nb, restricting the quantity of an impurity B and decreasing C content but also increasing the strength further by subjecting the steel to controlled rolling or thus rolled steel to thermo-mechanical treatment such as low temperature solution heat treatment.
  • the present inventors have studied the effects of C, N, Nb, B and roll finishing temperatures on the strength and corrosion resistance of austenitic stainless steel and found in the first place that, as shown in Fig. 1, intergranular corrosion resistance greater than that of SUS304L can be obtained by simultaneously adding 0.15 - 0.28% of N and 0.05 - 0.25% of Nb and limiting C to 0.03% or lower and B to 20 ppm.
  • a first example of steel embodying the present invention contains 0.03% or lower by weight C (hereinafter % refers to % by weight), 2.00% or lower of Si, 5.0% or lower of Mn, 0.030% or lower of S, 16 - 20% of Cr, 6 - 13% of Ni, 0.15 - 0.28% of N, 0.05 - 0.25% of Nb, 0.0020% or lower but more than 0 % of B, remaining Fe and impurity elements.
  • a second example of steel according to the present invention contains 4% or lower of Cu in addition to the elements contained in the first example or otherwise 0.005% or lower of S so as to improve the corrosion resistance of the first example.
  • a third example of steel according to the present invention contains either or both of 0.030-0.080% of S and 0.005 - 0.080% of Se to improve the machinability of the first example.
  • seventh and eight examples of steel according to the present invention are obtained by heating the first, second and third examples of steel according to the present invention to 950 - 1,300°C, then rolling them at rolling temperatures of 900 - 1,250°C, controlling the roll finishing temperature so that it may be within the range of 900 - 1,000°C, subsequently cooling them at a rate of 4°C/min or higher, setting the total reduction quantity at 30% or higher, letting them have recrystallized microstructure and a proof stress of greater than 50kg/mm2 to improve the strength of the first, second and third examples.
  • Fifth, seventh and eight examples of steel according to the present invention are obtained by heating the first, second and third examples according to the present invention to 950 - 1,300°C, then rolling them at rolling temperatures of 600 - 1,250°C, controlling the roll finishing temperature so that it may be within the range of 600 - 900°C, subsequently cooling them at a rate of 4°C/min or higher, setting the total reduction quantity at 30% or higher, letting them have unrecrystallized reduced structure and a proof stress of greater than 60 kg/mm2 to improve the strength of the first, second and third examples.
  • Sixth example of steel according to the present invention is obtained by heating the first example according to the present invention to 950 - 1,300°C, then rolling it at rolling temperatures of 900 - 1,250°C, controlling the roll finishing temperature so that it may be lower than 1,000°C, subsequently subjecting it to low temperature solution heat treatment at 900 - 1,010°C, letting it have a grain size number of greater than 7.5 and a proof stress of greater than 40 kg/mm2 to improve the strength of the first example.
  • the element C in the present invention is important because it reduces the corrosion resistance after controlled rolling, and hot workability during controlled rolling to a large extent; consequently, it must be decreased to 0.03% or lower, so that an upper limit is set at 0.03%.
  • the element Si is added as a deoxidizer and also used to improve the strength, however it causes cracking at high temperatures at the time of welding and reduce the quantity N of the solid solution at the time of solidification; accordingly, it must be decreased to 2.0% or lower with 2.0% as an upper limit to obtain good steel ingots.
  • the element Mn is added as a deoxidizer and used to increase the solubility of N but it will impair the corrosion resistance and hot workability if the content of Mn increases; consequently, the upper limit is set at 5.0%.
  • Cr is the basic element of stainless steel and over 16% of it is at least required to provide superior corrosion resistance. However, because the excessive content of Cr will damage the balance between ⁇ / ⁇ structure at high temperatures, the upper limit is set at 20%.
  • Ni is the basic element of austenitic stainless steel and over 6% of it is required to obtain excellent corrosion resistance and austenitic structure. However, because the excessive content of Ni will cause weld cracks and reduce hot workability and corrosion resistance after controlled rolling, the upper limit is set at 13%.
  • N is the most important reinforcing element according to the present invention since it has penetration type solution strengthening action, crystal grain micronizing action resulting from Nb (C, N) precipitation and precipitation accelerating action, and contributes to improvement in corrosion resistance after controlled rolling.
  • the lower limit was set at 0.15%.
  • the upper limit is set at 0.28%.
  • Nb is an important element in the present invention for fixing the remaining C in the form of NbC, improving corrosion resistance after controlled rolling, rifining of crystal grain because of Nb (C, N) precipitation and increasing strength after controlled rolling; thus over 0.05% of Nb content is at least required.
  • Nb is an expensive element and, because the excessive content of it will damage hot workability, the upper limit is set at 0.25%.
  • the upper limit is set at 0.0020% and preferably 0.005% or lower.
  • Both of Mo and Cu are the elements to improve the corrosion resistance of the steel according to the present invention.
  • Mo and Cu are expensive elements and the content exceeding 4% will damage hot workability.
  • the upper limits are set at 4% each.
  • S is the element to improve corrosion resistance provided that its content is reduced by a large amount, ductility and toughness (particularly in the direction perpendicular to that of rolling) after controlled rolling.
  • S and Se are the elements used to improve the machinability of the steel according to the present invention, and 0 030% or higher of S and 0.005% or higher of Se must be contained therein according to the third embodiment.
  • the upper limit is set at 0.080%.
  • the reason why the heating temperatures were set at 950 - 1,300°C during controlled rolling is to reduce deformation resistance at the controlled rolling.
  • the rolling will become difficult because of large deformation resistance if the temperature is lower than 950°C and, if it exceeds 1,300°C, the rolling will also become difficult because partial intergranular fusion is developed or coarse crystal grains are produced.
  • the roll finishing temperatures are set at 900 - 1,000°C so as to control the strength of the steel according to the present invention; the lower the roll finishing temperature, the greater the strength thereof becomes.
  • the temperature exceeding 1,000°C will make recrystallized grains coarse and satisfactory strength unavailable, whereas the temperature lower than 900°C will make recrystallized microstructure unavailable and act to form unrecrystallized reduced structure, so that ductility and toughness in the direction perpendicular to that of rolling are reduced.
  • the roll finishing temperatures are set at 600 - 900°C because unrecrystallized reduced structure will be present at lower than 900°C and the strength of the steel will increase as the roll finishing temperature becomes lower. On the other hand, its ductility and toughness will decrease. Accordingly, it is preferred to set the percentage of S at 0.005 or lower during rolling at 600 - 900°C.
  • the temperature lower than 600°C is lower than the recovery temperature of the steel according to the present invention, the deformation resistance during rolling will be raised sharply and thus undesirable because rolling becomes difficult.
  • the low temperature solution heat treatment temperatures are set at 900 - 1,010°C because the solid solubility of C is possible with heat addition at 900 - 1,010°C and, when the recrystallization temperature is higher than 900°C, the crystal grain size, if treated at lower temperatures, will be minimized, whereas the strength will be increased.
  • C will not be solid - soluble nor recrystallized at temperatures lower than 900°C, whereas its crystal grain will become as coarse as 7.5 or smaller if the temperature exceeds 1,010°C and the strength will thus decrease.
  • the reason why the cooling rate after rolling is set at higher than 4°C/min is that the intergranular precipitation of Cr23C6 or Cr2N will be caused by slow cooling at a rate lower than 4°C/min and the corrosion resistance will decrease.
  • the reason why the total reduction ratio within the rolling temperature range of 900°C - 1,250°C is set at 30% is that the desired structure is unobtainable because the scarcity of the lattice defect and the accumulated energy introduced into the crystal as the result of working will allows coarse structure to remain while heated if the total reduction ratio is lower than 30%.
  • Fig. 1 is a graph illustrating the relation between sensitizing temperatures affecting intergranular corrosion resistance and retention time.
  • Fig. 2 is a graph illustrating roll finishing temperatures affecting strength.
  • Fig. 3 is a graph illustrating working temperatures affecting hot workability.
  • Fig. 4 is a graph illustrating roll finishing temperatures affecting corrosion resistance.
  • Table 1 shows chemical components of test pieces.
  • Table 2 shows the strength, corrosion resistance and hot workability of the examples A - Q of steel subjected to solution heat treatment (1,050°C x 30 min ⁇ W, Q) shown in Table 1.
  • JIS No. 4 test pieces were used to measure proof stress.
  • step structure is represented by ⁇
  • DUAL composite structure
  • DITCH switch structure
  • the examples A, C of conventional steel were superior in hot workability but inferior in proof stress, e.g., 25.0, 22.8 kg/mm2, also the examples A, C are inferior in inter granular corrosion resistance, sensitivity to anti-stress corrosion cracking, and the portion affected by welding heat.
  • the example B was superior in hot workability and the corrosion resistance of the base material and the portion affected by welding heat but inferior in proof stress, e.g., affected by welding heat but inferior in strength, e.g., 25.2 kg/mm2, intergranular corrosion resistance, and sensitivity to anti-stress corrosion cracking.
  • the example D was superior in sensitivity to anti-stress corrosion cracking, hot workability and the corrosion resistance of the base material and the portion affected by welding heat but inferior in proof stress, e.g., 23.4 kg/mm2 and intergranular corrosion resistance.
  • the example E prepared by adding 0.22% of N to the example A showed substantial improvement in proof stress, e.g., 32.1 kg/mm2 compared with the example A but a shortage of strength as high strength stainless steel.
  • the example F prepared by adding 0.10% of Nb to the example E showed further improvement in proof stress, e.g., 40.7 kg/mm2 and had satisfactory strength as high strength stainless steel but indicated reduced hot workability.
  • the example G prepared by adding 0.17% of N to the example B showed improvement in proof stress, e.g., 39.2 kg/mm2 and excellent strength but still reduced intergranular corrosion resistance and sensitivity anti-stress corrosion cracking in addition to reduced hot workability like the example F.
  • the examples H - Q of the steel according to the present invention being prepared by simultaneously adding 0.15 - 0.28% of N and 0.05 - 0.25% of Nb and limiting the quantity of C to 0.03% or lower and the quantity of B to 20 ppm or less, showed such strength as a stress proof of 48 kg/mm2 or greater, STEP (step structure) respecting intergranular corrosion resistance, no cracking regarding sensitivity to anti-stress corrosion cracking despite immersion for 50 Hr, no reduction in hot workability unlike the conventional steet, a contraction of area of over 70%, and excellent corrosion resistance of the base material and the portion affected by welding heat at 0.3V or higher.
  • each of the steel according to the present invention is superior in all of the strength, intergranular corrosion resistance, sensitivity to anti-stress corrosion cracking, hot workability, the corrosion resistance of the base material and the portion affected by welding heat.
  • Table 3 illustrates the strength and corrosion resistance of the examples A, C, E, F, J, M and P shown in Table 1 and, as for those subjected to low temperature solution heat treatment, and their crystal grain sizes.
  • the flat steel by 10 x 40 mm was heated to 1,150°C and then rolled with the roll finishing temperature controlled at about 950°C or 800°C, before being cooled at 50°C/min or higher and the total reduction ratio of 96%.
  • the steel thus heated and rolled with the roll finishing temperature controlled at 950°C was cooled at 50°C/min and the total reduction ratio of 96% and then subjected to low temperature solution heat treatment for holding it at 980°C x 30 min.
  • the roll finishing temperature controlled at 950°C or 800°C resulted, as shown in Table 3, in causing the proof stress of the example A to increase from 25 kg/mm2 to 33, 42 kg/mm2, that of the example C from 22.8 kg/mm2 to 25, 31 kg/mm2 and that of that of the example E from 32.1 kg/mm2 to 44, 53 kg/mm2 but still failing to attaining the desired 50, 60 kg/mm2.
  • all of the examples A, C, E subjected to controlled rolling showed reduction in corrosion resistance by a large margin.
  • the roll finishing temperature controlled at 950°C allowed the examples J, M, P of the steel according to the present invention to have recrystallized microstructure and improved the proof stress of each from about 50 kg/mm2 to 65 kg/mm2, whereas the roll finishing temperature controlled at 800°C permitted them to have uncrystallized reduced structure and considerably improved the proof stress of each up to about 77 kg/mm2; in other words, controlled rolling applied to the steel according to the present invention obviously acted to improve its proof stress by a large amount.
  • the examples J, M, P according to the present invention showed pitting corrosion potential equivalent to what was not subjected to controlled rolling and, unlike the conventional steel, no reduction in corrosion resistance because of the controlled rolling applied.
  • each of the examples J, M, P according to the present invention was allowed to have recrystallized microstructure with a crystal grain size of over 7.5 by that treatment and showed the proof stress raised up to over 50 kg/mm2 and pitting corrosion potential roughly equivalent to what was subjected to solution heat treatment (1,050°C x 30 min ⁇ W,Q.) and no reduction in corrosion resistance due to controlled rolling and low temperature solution heat treatment.
  • the present invention relates to economical stainless steel and a process for manufacturing the same having high strength, e.g., over 35 kg/mm2 in terms of proof stress, the strength being improvable up to 50 kg/mm2 or greater and further 70 kg/mm2 or greater by controlled rolling; excellent corrosion resistance, particularly intergranular corrosion resistance and sensitivity to anti-stress corrosion clacking; pitting corrosion and acid resistance superior to SUS304; corrosion resistance without being reduced after welding; excellent hot workability; and producibility through the same process as that of SUS304 manufacture.
  • the corrosion resistance of the steel according to the present invention is made further improvable by adding Mo, Cu as occasion demands and its machinability is also improvable by adding small quantities of S, Se.
  • the steel according to the present invention is superior in strength and corrosion resistance and suitable for use as a high strength member in various plants such as chemical seawater and nuclear power plants.

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Claims (8)

  1. Hochfester, rostfreier Stahl, umfassend nach dem Gewicht 0,03 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, 0,030 % oder weniger S, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, 0,0020 % oder weniger, aber mehr als 0 % B, wobei der Rest Fe zusammen mit Verunreinigungselementen ist.
  2. Hochfester, rostfreier Stahl, umfassend nach dem Gewicht 0,03 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, 0,0020 % oder weniger, aber mehr als 0 % B, ein Element, gewählt aus der Gruppe, bestehend aus 4 % oder weniger Cu und 0,005 % oder weniger, aber mehr als 0 % S, der Rest ist Fe zusammen mit Verunreinigungselementen.
  3. Hochfester, rostfreier Stahl, umfassend nach dem Gewicht 0,03 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, 0,0020 % oder weniger B, wenigstens ein Element, gewählt aus der Gruppe, bestehend aus 0,030 - 0,080 % S, und 0,005 - 0,08 % Se, der Rest ist Eisen zusammen mit Verunreinigungselementen.
  4. Verfahren zur Herstellung eines hochfesten, rostfreien Stahles mit einer rekristallisierten Mikrostruktur, umfassend dem Gewicht nach 0,03 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, weniger als 0,030 % und mehr als 0 % S, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, weniger als 0,0020 % und mehr als 0 % B, der Rest ist Eisen zusammen mit Verunreinigungselementen, wobei das Verfahren die folgenden Schritte umfaßt:
    - Erhitzen des Stahles auf eine Temperatur von 950 - 1300 °C,
    - Walzen des Stahles bei einer Temperatur von 900 - 1250 °C,
    - Steuern der Temperaturen beim Fertigwalzen dieses Stahles zwischen 900 - 1000 °C, wobei der gesamte Reduktionsgrad des Stahles 30 % oder mehr beträgt und
    - Abkühlen des gewalzten Stahles mit einer Geschwindigkeit von 4 °C/min oder mehr.
  5. Verfahren zur Herstellung eines hochfesten, rostfreien Stahles mit einer nichtrekristallisierten Mikrostruktur, umfassend dem Gewicht nach 0,030 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, weniger als 0,030 % und mehr als 0 % S, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, weniger als 0,0020 % und mehr als 0 % B, der Rest ist Eisen zusammen mit Verunreinigungselementen, wobei das Verfahren die folgenden Schritte umfaßt:
    - Erhitzen des Stahles auf eine Temperatur von 950 - 1300 ° C,
    - Walzen des Stahles bei einer Temperatur von 600 - 1250 °C,
    - Steuern der Temperaturen des Fertigwalzens für diesen Stahle auf 600 - 900 °C, wobei der gesamte Reduktionsgrad des Stahles 30 % oder mehr beträgt und
    - Abkühlen des gewalzten Stahles mit einer Geschwindigkeit von 4 °C/min oder mehr.
  6. Verfahren zur Herstellung eines hochfesten, rostfreien Stahles mit einer Kristallkörnungsnummer von 7,5 oder mehr, umfassend dem Gewicht nach 0,03 % oder weniger C, 2,00 % oder weniger Si, 5,0 % oder weniger Mn, weniger als 0,030 % und mehr als 0 % S, 16 - 20 % Cr, 6 - 13 % Ni, 0,15 - 0,28 % N, 0,05 - 0,25 % Nb, weniger als 0,0020 % und mehr als 0 % B, der Rest ist Eisen zusammen mit Verunreinigungselementen, wobei das Verfahren die folgenden Schritte umfaßt:
    - Erhitzen des Stahles auf eine Temperatur von 950 - 1300 ° C,
    - Walzen des Stahles bei einer Temperatur von 900 - 1250 °C,
    - Steuern der Temperaturen des Fertigwalzens für diesen Stahl auf Temperaturen unter 1000 °C,
    - Abkühlen des gewalzten Stahles mit einer Geschwindigkeit von 4 °C/min oder mehr und
    - Aussetzen des Stahles einer Tieftemperatur-Lösungsglühbehandlung bei einer Temperatur von 900 - 1010 °C.
  7. Verfahren zur Herstellung eines hochfesten, rostfreien Stahles nach Anspruch 4 oder 5, des weiteren umfassend wenigstens ein Element, ausgewählt aus der Gruppe, bestehend aus 4 % oder weniger Cu und 0,005 % oder weniger S.
  8. Verfahren zur Herstellung eines hochfesten, rostfreien Stahles nach Anspruch 4 odfer 5, des weiteren umfassend wenigstens ein Element, ausgewählt aus der Gruppe, bestehend aus 0,030 - 0,080 % S und 0,005 - 0,080 % Se.
EP85905113A 1985-10-15 1985-10-15 Hochfester rostfreistahl und dessen herstellung Expired - Lifetime EP0241553B1 (de)

Applications Claiming Priority (1)

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PCT/JP1985/000573 WO1987002388A1 (fr) 1985-10-15 1985-10-15 Acier inoxydable a haute resistance et son procede de fabrication

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EP0241553A1 EP0241553A1 (de) 1987-10-21
EP0241553A4 EP0241553A4 (de) 1989-01-18
EP0241553B1 true EP0241553B1 (de) 1992-06-17

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JP2602015B2 (ja) * 1986-08-30 1997-04-23 愛知製鋼株式会社 耐腐食疲労性、耐海水性に優れたステンレス鋼およびその製造方法
KR100411286B1 (ko) * 1996-12-24 2004-04-03 주식회사 포스코 내식성및내후성이우수한고강도오스테나이트계스테인레스강및이를이용한강판제조방법
RU2173729C1 (ru) * 2000-10-03 2001-09-20 Федеральное государственное унитарное предприятие "ЦНИИчермет им. И.П. Бардина" Аустенитная коррозионностойкая сталь и изделие, выполненное из нее

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JPS58144420A (ja) * 1982-02-19 1983-08-27 Kawasaki Steel Corp オ−ステナイト系ステンレス大型鍛鋼の製造方法
JPS6092422A (ja) * 1983-10-25 1985-05-24 Nippon Kokan Kk <Nkk> 亀裂開口変位の優れた含Νｉ低温用鋼の製造方法
DE3407305A1 (de) * 1984-02-24 1985-08-29 Mannesmann AG, 4000 Düsseldorf Verwendung einer korrosionsbestaendigen austenitischen legierung fuer mechanisch hoch beanspruchte, schweissbare bauteile
JPS60197817A (ja) * 1984-03-19 1985-10-07 Nippon Kokan Kk <Nkk> 耐食性に優れた高降伏強度オ−ステナイト・ステンレス鋼材の製造方法
JPS60208459A (ja) * 1984-03-30 1985-10-21 Aichi Steel Works Ltd 高強度ステンレス鋼およびその製造法

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* Cited by examiner, † Cited by third party
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JPS54151505A (en) * 1978-05-09 1979-11-28 Kobe Steel Ltd Austenitic stainless steel microcrystal grain generation
JPS558404A (en) * 1978-06-30 1980-01-22 Nippon Steel Corp Manufacture of austenitic stainless steel used in atmosphere of high-temperature and high-pressure water
JPS6089518A (ja) * 1983-10-22 1985-05-20 Sumitomo Metal Ind Ltd オ−ステナイト系材料の製造方法
JPS60100621A (ja) * 1983-11-07 1985-06-04 Nippon Steel Corp 高温強度の優れたオ−ステナイトステンレス鋼の製造方法

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DE3586247T2 (de) 1993-02-25
DE3586247D1 (de) 1992-07-23
EP0241553A1 (de) 1987-10-21
WO1987002388A1 (fr) 1987-04-23

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