EP1577414A2 - Hitzebeständiger austenitischer rostfreier Stahl und Verfahren zu seiner Herstellung - Google Patents

Hitzebeständiger austenitischer rostfreier Stahl und Verfahren zu seiner Herstellung Download PDF

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Publication number
EP1577414A2
EP1577414A2 EP05004809A EP05004809A EP1577414A2 EP 1577414 A2 EP1577414 A2 EP 1577414A2 EP 05004809 A EP05004809 A EP 05004809A EP 05004809 A EP05004809 A EP 05004809A EP 1577414 A2 EP1577414 A2 EP 1577414A2
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Prior art keywords
heat
stainless steel
austenitic stainless
less
resistant austenitic
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French (fr)
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EP1577414A3 (de
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Shuji Hamano
Tetsuya Shimizu
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Daido Steel Co Ltd
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Daido 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
    • C22C38/001—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten

Definitions

  • the present invention relates to a heat-resistant austenitic stainless steel and a production process thereof, more specifically relates to a heat-resistant austenitic stainless steel suitable for a steel material for heat-resistant members used in exhaust systems of an automobile engine and an aeroengine, industrial manufacturing facilities and the like, and a production process thereof.
  • an austenitic stainless steel e.g., SUS304 and SUS316
  • a precipitation hardened stainless steel e.g., SUS631J1
  • an Fe-based superalloy e.g., SUH660 (A286)
  • an Ni-based superalloy e.g., Inconel 718 and Inconel X750
  • the heat-resistant steel material which is low in cost and more excellent in the high-temperature strength and sag-resistance is strongly required.
  • the conventional austenitic stainless steel and the precipitation hardened stainless steel are relatively low in cost; however, the working temperatures thereof are limited.
  • the Fe-based or Ni-based superalloy satisfies a requirement for high-temperature strength and sag-resistance at not less than 550°C, so that a heat-resistant member capable of resisting working temperatures of up to about 700°C may be obtained.
  • the heat-resistant member made from the superalloy causes increases in a melting cost and a process cost as well as a raw material cost, so that there arises a problem of high manufacturing costs.
  • Japanese Patent Application Unexamined Publication No.Hei9-143633 discloses a martensitic stainless steel for a heat-resistant spring consisting of 11wt% to 14wt% Cr, 4.5wt% to 7.0wt% Ni, 1.0wt% to 3.0wt% Mo, 1.0wt% to 3.0wt% Al, 0.10wt% to 0.20wt% C, less than 10 ⁇ C wt% Nb, and Fe and unavoidable impurities (see claim 1 and paragraph 0023).
  • Japanese Patent Application Unexamined Publication No.2000-239804 discloses a stainless steel wire for a heat-resistant spring containing 0.04wt% to 0.40wt% C, 0.02wt% to 0.30wt% N, 0.24wt% to 0.60wt% C + N, 1.5wt% to 20.0wt% Mn, 17.0wt% to 19.0wt% Cr, 2.0wt% to 12.0wt% Ni and 0.5wt% to 2.0wt% Mo as well as at least one element selected from 0.8wt% Nb, 0.6wt% to 1.2wt% Si, 1.0wt% Ti and 1.0wt% W, and the remainder substantially consisting of Fe and unavoidable impurities (see paragraphs 0008 and 0009, and Tables 1 and 3).
  • Japanese Patent Application Unexamined Publication No.2003-73784 discloses a heat-resistant steel wire containing 0.02wt% to 0.30wt% C, 0.02wt% to 3.5wt% Si, 0.02wt% to 2.5wt% Mn, 20wt% to 30wt% Ni, 15wt% to 25wt% Cr, 1.0wt% to 5.0wt% Ti and 0.002wt% to 1.0wt% Al as well as one or more elements selected from 0.1wt% to 2.0wt% Nb, 0.1wt% to 2.0wt% Ta and 0.1wt% to 4.0wt% Mo - the total content of Ti, Al, Nb and Ta is 2.0wt% to 7.0wt% -, and the remainder substantially consisting of Fe and unavoidable impurities (see claim 1 and paragraph 0053).
  • Japanese Patent Application Unexamined Publication No.2000-109955 discloses a heat-resistant stainless steel containing 0.02wt% to 0.30wt% C, 0.02wt% to 3.5wt% Si, 0.02wt% to 2.5wt% Mn, 10wt% to 50wt% Ni, 12wt% to 25wt% Cr, 1.0wt% to 5.0wt% Ti and 0.002wt% to 1.0wt% Al as well as one or more elements selected from 0.1wt% to 3.0wt% Nb, 0.001wt% to 0.01wt% B and 0.1wt% to 4.0wt% Mo - the total content of Ti, Al and Nb is 3.0wt% to 7.0wt% (see claim 1 and paragraph 0037).
  • Japanese Patent Application Unexamined Publication No.2000-345268 discloses a high-heat-resistant alloy wire for a spring containing not more than 0.1wt% C, 18.0wt% to 21.0wt% Cr, 12.0wt% to 15.0wt% Co, 3.5wt% to 5.0wt% Mo, 2.0wt% to 4.0wt% Ti and 1.0wt% to 3.0wt% Al, and the remainder substantially consisting of Ni (see claim 1, and paragraphs 0022 and 0068).
  • a cold wire drawing process is performed to obtain the alloy wire with a worked austenitic structure where a grain size is predetermined, having surface roughness within a predetermined range and being not more than 5mm in diameter, and thereby the sag-resistance at not less than 600°C is improved.
  • Japanese Patent Application Unexamined Publication No.Hei8-269632 discloses a high-strength and high-corrosion-resistant nitrogen-contained austenitic stainless steel consisting of not more than 0.1wt% C, not more than 1.0wt% Si, 5wt% to 10wt% Mn, not more than 0.01wt% S, 8wt% to 15wt% Ni, 15wt% to 25wt% Cr, 0.5wt% to 4wt% Mo and 0.3wt% to 1.0wt% N, and the remainder substantially consisting of Fe (see claim 1, and paragraph 0024).
  • dissolving nitrogen completely in solid solution through a solution heat treatment at not more than 1100°C allows room-temperature strength and corrosion resistance to improve.
  • Japanese Patent Application Unexamined Publication No.Hei9-279315 discloses an austenitic stainless steel for a metal gasket consisting of not more than 0.1wt% C, not more than 1.0wt% Si, 1.0wt% to 10.0wt% Mn, not more than 0.01wt% S, not more than 3.0wt% Cu, 7.0wt% to 15.0wt% Ni, 15.0wt% to 25.0wt% Cr, not more than 5.0wt% Mo, 0.35wt% to 0.8wt% N and not more than 0.02wt% Al, and the remainder substantially consisting of Fe (see claim 1, and paragraphs 0006 and 0029).
  • the materials disclosed in the above-mentioned Publications No.Hei9-143633 and No.2000-239804 are prepared for working temperatures of not more than 500°C, and not more than 550°C, respectively, so that they do not satisfy requirements for high-temperature strength and sag-resistance at temperatures higher than 550°C. Further, the amounts of nitrogen contained in these materials are 0.3wt% at the maximum (see Table 1 of No.2000-239804)
  • the materials disclosed in the above-mentioned Publications No.2003-73784, No.2000-109955 and No.2000-345268 are prepared for working temperatures of not less than 550°C;
  • costs of the materials rise up to the same as or more than that of the Fe-based superalloy (e.g., SUH660) since improvement in heat resistance is attempted in the respective materials by adding a large amount of Ni or Co so that precipitation on the ⁇ ' phase (Ni 3 Al) is mainly reinforced.
  • An object of the invention is to overcome the problems described above and to provide a heat-resistant austenitic stainless steel having high-temperature strength and sag-resistance capable of resisting working temperatures of not less than 550°C as well as being low in cost, and a production process thereof.
  • a heat-resistant austenitic stainless steel consistent with the preferred embodiment of the present invention contains not more than 0.1wt% C, less than 1.0wt% Si, 1.0wt% to 10.0wt% Mn, not more than 0.03wt% P, not more than 0.01wt% S, 0.01wt% to 3.0wt% Cu, 7.0wt% to 15.0wt% Ni, 15.0wt% to 25.0wt% Cr, 0.5wt% to 5.0wt% Mo, not more than 0.03wt% Al, 0.4wt% to 0.8wt% N, and the remainder substantially consisting of Fe and unavoidable impurities.
  • a production process of a heat-resistant austenitic stainless steel consistent with the preferred embodiment of the present invention includes the steps of applying solution treatment to the heat-resistant austenitic stainless steel consistent with the present invention, providing cold-working at a cold working ratio of 40% to 70% to the steel subjected to the solution treatment, and applying aging treatment at temperatures of 400°C to 650°C for not less than one minute to the steel subjected to the cold working.
  • the heat-resistant austenitic stainless steel consistent with the preferred embodiment of the present invention is low in cost since an addition amount of Ni is restrained. Further, an austenitic phase is stabilized since amounts of respective alloying elements such as Mn, Cr and Mo, which contribute to an increase in a solution amount of N, are kept in balance, and thereby the N-content is increased to the highest level above which N exceeds an amount of N-solubility in molten metal under the atmosphere. Furthermore, excellent high-temperature strength is attained through the aging treatment after the cold working. Moreover, the Al-content is made not more than 0.03wt%, so that generation of AlN which leads to decline in strength, toughness and ductility is suppressed. Therefore, by optimizing conditions of the cold working and the aging treatment, a heat-resistant member having high-temperature strength and sag-resistance approximately equal to those of an Fe-based superalloy is obtained.
  • the heat-resistant austenitic stainless steel consistent with the present invention is characterized as containing elements as provided below, and the remainder thereof substantially consisting of Fe and unavoidable impurities.
  • elements as provided below, and the remainder thereof substantially consisting of Fe and unavoidable impurities.
  • C is an interstitial element which contributes to improvement in strength. Further, C acts to improve heat resistance by combining with Cr, Mo, W, V, Ti and Nb described later to form carbide. Therefore, it is preferable for the heat-resistant austenitic stainless steel to contain C so as to attain excellent high-temperature strength and sag-resistance.
  • a C-content is preferably not less than 0.001wt%, more preferably not less than 0.005wt%, and still more preferably not less than 0.010wt%.
  • the C-content is preferably not more than 0.1wt%, more preferably not more than 0.05wt%, and still more preferably not more than 0.04wt%.
  • the present steel is characterized in that N may be dissolved in solid solution to the maximum solution amount.
  • Si functions similarly to Al as a deoxidation element; however, since Al reacts with N and generates AlN to decrease a solution amount of N in the matrix phase, and the generated AlN significantly declines the high-temperature strength, toughness and ductility, it is preferable to use Si as the deoxidation element to reduce an Al-content in the steel.
  • an Si-content is preferably not less than 0.01wt%, more preferably not less than 0.05wt%, and still more preferably not less than 0.10wt%.
  • the Si-content is preferably less than 1.0wt%, more preferably not more than 0.7wt%, and still more preferably not more than 0.5wt%.
  • Mn is an austenite-stabilizing element which contributes to stabilization of an austenitic phase. Further, Mn is an important element which contributes to improvement in the strength since it significantly increases the solution amount of N. Furthermore, Mn is effective as deoxidation and desulfurization elements. Specifically, an Mn-content is preferably not less than 1.0wt%, more preferably not less than 3.0wt%, and still more preferably not less than 4.0wt%.
  • the Mn-content is preferably not more than 10.0wt%, more preferably not more than 9.0wt%, and still more preferably not more than 8.0wt%.
  • a P-content is preferably small, specifically not more than 0.03wt%. Excessive reduction in P, however, causes a cost rise.
  • an S-content is preferably small, specifically not more than 0.01wt%. Excessive reduction in S, however, causes a cost rise.
  • Cu is an austenite-stabilizing element which contributes to the stabilization of the austenitic phase. Further, Cu contributes to improvement in the toughness at the time of the cold working. Specifically, a Cu-content is preferably not less than 0.01wt%, and more preferably not less than 0.02wt%.
  • the Cu-content is preferably not more than 3.0wt%, more preferably not more than 2.5wt%, and still more preferably not more than 2.0wt%.
  • Ni is an austenite-stabilizing element which contributes to the stabilization of the austenitic phase. Further, Ni contributes to the improvement in the high-temperature strength. Specifically, an Ni-content is preferably not less than 7.0wt%, and more preferably not less than 7.5wt%, and still more preferably not less than 8.0wt%.
  • the Ni-content is preferably not more than 15.0wt%, more preferably not more than 14.0wt%, and still more preferably not more than 12.0wt%.
  • a Cr-content is preferably not less than 15.0wt%, and more preferably not less than 18.0wt%, and still more preferably not less than 21.0wt%.
  • the Cr-content is preferably not more than 25.0wt%, and more preferably not more than 24.0wt%.
  • Mo is an element for increasing the solution amount of N, which improves the corrosion resistance, the high-temperature strength and the sag-resistance. Furthermore, similarly to Cr, Mo combines with C to form the carbide, and improves the heat resistance. Specifically, an Mo-content is preferably not less than 0.5wt%, and more preferably not less than 0.8wt%, and still more preferably not less than 1.0wt%.
  • the Mo content is preferably not more than 5.0wt%, and more preferably not more than 4.5wt%, and still more preferably not more than 4.0wt%.
  • an Al-content is preferably not more than 0.03wt%, and more preferably not more than 0.025wt%, and still more preferably not more than 0.020wt%.
  • N is the interstitial element which is one of the most important elements in the present invention, and highly effective in improving the strength and the corrosion resistance and stabilizing the austenitic phase. Further, N is highly effective in improving the high-temperature strength and the sag-resistance through the aging treatment after the cold working. Specifically, an N-content is preferably not less than 0.4wt%, and more preferably not less than 0.42wt%.
  • the N-content is preferably not more than 0.8wt%, and more preferably not more than 0.7wt%, and still more preferably not more than 0.6wt%.
  • the heat-resistant austenitic stainless steel consistent with the present invention may further include at least one element selected from W and Co.
  • W and Co the heat-resistant austenitic stainless steel consistent with the present invention.
  • W is an element for increasing the solution amount of N which contributes to improvement in the high-temperature strength and the sag-resistance. Further, similarly to Mo, W combines with C to form carbide, and improves the heat resistance. Specifically, a W-content is preferably not less than 0.01wt%, and more preferably not less than 0.05wt%, and still more preferably not less than 0.10wt%.
  • the W-content is preferably not more than 1.0wt%, and more preferably not more than 0.9wt%, and still more preferably not more than 0.8wt%.
  • Co contributes to the improvement in the high-temperature strength and the sag-resistance.
  • a Co-content is preferably not less than 0.01wt%, and more preferably not less than 0.05wt%, and still more preferably not less than 0.10wt%.
  • the Co-content is preferably not more than 5.0wt%, and more preferably not more than 4.5wt%, and still more preferably not more than 4.0wt%.
  • the heat-resistant austenitic stainless steel consistent with the present invention may further include at least one element selected from Ti, Nb and V.
  • at least one element selected from Ti, Nb and V may further include at least one element selected from Ti, Nb and V.
  • descriptions will be given on ranges of addition amounts of Ti, Nb and V, and reasons for limitation of the ranges.
  • Ti combines with C and N, and contributes to the improvement in the high-temperature strength and refining of crystal grains.
  • a Ti-content is preferably not less than 0.03wt%, and more preferably not less than 0.035wt%, and still more preferably not less than 0.04wt%.
  • the Ti-content is preferably not more than 0.5wt%, and more preferably not more than 0.4wt%, and still more preferably not more than 0.3wt%.
  • Nb 0.03wt% to 0.5wt%
  • Nb combines with C and N, and contributes to the improvement in the high-temperature strength and the refining of the crystal grains.
  • an Nb-content is preferably not less than 0.03wt%, and more preferably not less than 0.035wt%, and still more preferably not less than 0.04wt%.
  • the Nb-content is preferably not more than 0.5wt%, and more preferably not more than 0.4wt%, and still more preferably not more than 0.3wt%.
  • V 0.03wt% to 1.0wt%
  • V combines with C and N, and contributes to the improvement in the high-temperature strength and the refining of the crystal grains.
  • a V-content is preferably not less than 0.03wt%, and more preferably not less than 0.04wt%, and still more preferably not less than 0.05wt%.
  • the V-content is preferably not more than 1.0wt%, and more preferably not more than 0.9wt%, and still more preferably not more than 0.8wt%.
  • the heat-resistant austenitic stainless steel consistent with the present invention may further include at least one element selected from B and Zr.
  • B and Zr are elements selected from B and Zr.
  • B contributes to the improvement in the high-temperature strength and the sag-resistance. Further, B is effective in improving the hot workability. Specifically, a B-content is preferably not less than 0.001wt%.
  • the B-content is preferably not more than 0.010wt%, and more preferably not more than 0.008wt%, and still more preferably not more than 0.005wt%.
  • a Zr-content is preferably not less than 0.01wt, and more preferably not less than 0.02wt%, and still more preferably not less than 0.03wt%.
  • the Zr-content is preferably not more than 0.10wt%, and more preferably not more than 0.09wt%, and still more preferably not more than 0.08wt%.
  • the heat-resistant austenitic stainless steel consistent with the present invention may further include at least one element selected from Ca and Mg.
  • at least one element selected from Ca and Mg may be given on ranges of addition amounts of Ca and Mg, and reasons for limitation of the ranges.
  • Ca is effective in improving the hot workability, and is also effective in improving machinability.
  • a Ca-content is preferably not less than 0.001wt%.
  • the Ca-content is preferably not more than 0.010wt%, and more preferably not more than 0.008wt%, and still more preferably not more than 0.005wt%.
  • Mg is effective in improving the hot workability. Specifically, an Mg-content is preferably not less than 0.001wt%.
  • the Mg-content is preferably not more than 0.010wt%, and more preferably not more than 0.008wt%, and still more preferably not more than 0.005wt%.
  • PN PN value of not less than 60 when expressed in the following Equation 1 is preferable for the heat-resistant austenitic stainless steel consistent with the present invention.
  • PN 2.4Mn-Cu-0.6Ni+3Cr+0.8Mo(wt%)
  • Equation 1 Mn, Cu, Ni, Cr and Mo are selected as an element which contributes to the solution amount of N, and contribution rates of the respective elements to the solution amount of N are obtained.
  • the PN value expressed by Equation 1 is not less than 60, it means that the solution amount of N capable of satisfying a requirement for a high-temperature property is secured.
  • the PN value is more preferably not less than 62, and still more preferably not less than 64.
  • the solution treatment is applied to a forged and rolled alloy for the purpose of uniforming the structure so that the cold workability is secured and Cr 2 N precipitates while being refined and dispersed uniformly at the time of the aging treatment.
  • a condition necessary and sufficient for uniforming the structure may be applied.
  • a temperature of the solution treatment is preferably 1000°C to 1150°C, and the time is preferably 0.1 hour to 2 hours.
  • a cold working ratio is preferably 40% to 70%.
  • the cold working ratio is below 40%, an increase in the strength by work hardening becomes small, and further, no increase can be attained at the succeeding aging treatment.
  • primary hardness of 45HRC at room temperature cannot be secured, and a residual stress ratio in a relaxation test at 700 °C becomes 25% or less.
  • the cold working ratio rises over 70%, the residual stress ratio falls, which is not preferable.
  • a method for the cold working is not limited, and various methods such as wire drawing, cold rolling and swaging may be applied.
  • the aging treatment is applied to the alloy, which is cold-worked at 40 to 70% after the solution treatment, for the purpose of improving the strength and the sag-resistance.
  • the aging treatment is preferably conducted for not less than 1 minute at 400°C to 650°C. Under the conditions other than the one above, the primary hardness of 45HRC at room temperature cannot be secured, and the residual stress ratio at 700 °C becomes 25% or less.
  • An upper limit of the aging treatment time is not specified particularly; however, not more than 1 hour is recommended to avoid a cost rise in terms of industrial use.
  • a heat-resistant austenitic stainless steels having the primary hardness of 45HRC at room temperature is obtained.
  • a heat-resistant austenitic stainless steel having the primary hardness of 50HRC at room temperature is obtained.
  • a heat-resistant austenitic stainless steel which has hardness of not less than 45HRC at room temperature after 400-hour heat treatment at 600°C, and hardness of not less than 40HRC at room temperature after 400-hour heat treatment at 700°C.
  • a heat-resistant austenitic stainless steel is obtained, which has the residual stress ratio of not less than 25% after a 50-hour relaxation test at 700 °C.
  • the heat-resistant austenitic stainless steel consistent with the present invention is low in cost compared with the conventional Fe-based or Ni-based superalloys since the addition amount of Ni which causes a cost rise is restrained.
  • the austenitic phase is stabilized, and the excellent high-temperature strength is attained through the aging treatment after the cold working since the amounts of the respective alloying elements such as Mn, Cr and Mo, which contribute to the increase of the solution amount of N, are kept in balance so as to increase the N-content to the highest level above which N exceeds an amount of N-solubility in molten metal under the atmosphere.
  • the amounts of the respective alloying elements so that the PN value becomes not less than 60, the solution amount of N necessary for satisfying the requirement for the high-temperature property may be secured.
  • the generation of AlN which leads to decline in the strength, toughness and ductility may be suppressed since the Al-content is made not more than 0.03wt%.
  • the heat-resistant austenitic stainless steel exhibits the high-temperature strength and the sag-resistance capable of resisting working temperatures of up to 700°C which is approximately equal to those of the Fe-based superalloy. Therefore, when the steel is applied to various heat-resistant members for which the high-temperature strength and the sag-resistance are required, an improvement in performance and thermal efficiency of machines and the like where the heat-resistant members are installed may be yielded while a cost rise is curbed.
  • test procedure is as follows.
  • SUH660 Comparative Example 1
  • a production process of SUH660 before cold working was the same as that of Examples 1 to 14. Further, the cold working was conducted at a cold working ratio of 50%, and SUH660 was formed into a round bar of 17 mm in diameter. Furthermore, for aging treatment, the bar was air-cooled after kept at 720°C for 4 hours.
  • Table 1 shows alloy composition of the respective materials. Further, Table 2 shows primary hardness (HRC) after the aging treatment, tensile strength (MPa) at 600°C and 700°C, hardness (HRC) after kept at 600°C and 700°C for 400 hours, and the residual stress ratio (%). As demonstrated in Tables 1 and 2, Examples 1 to 14 respectively satisfy requirements for both the primary hardness of not less than 45HRC and the residual stress ratio at 700°C of not less than 25% at the same time, while Comparative Examples 1 to 9 cannot satisfy both the requirements at the same time.
  • Tables 1 and 2 shows that the high-temperature tensile strength and the hardness after the long-time heat treatment at a high temperature in Examples 1 to 14 are the same as or greater than those in Comparative Examples 1 to 9.
  • Primary Hardness After Aging Treatment HRC
  • HRC High-temperature Tensile Strength Hardness after Heat Treatment Residual Stress Ratio 600°C (MPa) 700°C (MPa) 600°C/400h (HRC) 700°C/400h (HRC) (%)
  • Example 1 53 1053 853 51 44 36
  • Example 2 51 987 796 50 42 32
  • Example 3 1001 802 50 42 35
  • Example 4 52 1027 844 51 43 31
  • Example 5 1003 801 50 42
  • Example 6 51 992 798 50 42
  • Example 8 51 987 797 50 42 30
  • Example 11 51 996 795 50 42 30
  • Example 3 a material having the same composition as Example 3 was subjected to melting, forging, solution treatment, cold working and aging treatment following the same procedure as above except that only the cold working ratio at the time of the cold working after the solution treatment was changed. A test piece was taken from the obtained material, and residual stress ratios (%) thereof under the above-described conditions were obtained. Table 3 shows the result. As demonstrated in Table 3, in cases where the cold working ratios are below 40%, and over 70%, the residual stress ratios decline. Cold Working Ratio (%) Residual Stress Ratio (%) 30 18 40 31 50 34 60 35 70 32 80 12
  • Example 3 a material having the same composition as Example 3 was subjected to melting, forging, solution treatment, cold working and aging treatment following the same procedure as above except that only the condition of the aging treatment was changed.
  • a test piece was taken from the obtained material, and the residual stress ratios (%) thereof under the above-described conditions were obtained. Table 4 shows the result. As demonstrated in Table 4, in cases where the temperatures of the aging treatment are below 400°C, and over 650°C, the residual stress ratios decline.
  • the heat-resistant austenitic stainless steel consistent with the present invention may be applied extensively to a heat-resistant member for which a low cost, and the high-temperature strength and the sag-resistance are required.
  • Examples of specific applications include: a heat-resistant spring used in exhaust systems of an automobile engine and an aeroengine, an industrial manufacturing facilities and the like; a high-temperature bolt and the like which are typically used in the automobile engine, the aeroengine, a generator turbine and the like; a turbo casing; a boiler part; a part for an industrial furnace, and the like.
  • examples of more specific applications include: a nozzle, a vane, a blade, a disk, a casing and a bolt of a gas turbine, a combustor liner, a compressor disk and the like for aviation and generator; intake and exhaust valves for automobile engine, a rotor, a housing, a nozzle and a vane of a turbocharger, an exhaust manifold, a front pipe, a muffler, an exhaust valve spring, an exhaust bolt and the like for an automobile; a boiler, a rotor, a casing, a blade, a bolt and the like for a steam turbine; petrochemical industrial parts such as a heat exchanger, a pressure vessel, an ethylene decomposition tube and a valve; parts for a heat treating furnace such as a fitting, a fixture, a jig for heat treatment, a forging mold or die, a hot reduction roll, a continuous cast roll, a heater sheath and a radiant tube; parts for a

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EP05004809A 2004-03-04 2005-03-04 Hitzebeständiger austenitischer rostfreier Stahl und Verfahren zu seiner Herstellung Withdrawn EP1577414A3 (de)

Applications Claiming Priority (4)

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JP2004060124 2004-03-04
JP2004060124 2004-03-04
JP2005026158A JP2005281855A (ja) 2004-03-04 2005-02-02 耐熱オーステナイト系ステンレス鋼及びその製造方法
JP2005026158 2005-02-02

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EP1577414A2 true EP1577414A2 (de) 2005-09-21
EP1577414A3 EP1577414A3 (de) 2005-11-23

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US9032623B2 (en) 2007-08-06 2015-05-19 Shell Oil Company Method of manufacturing a burner front face
US9546784B2 (en) 2007-08-06 2017-01-17 Shell Oil Company Burner
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US9149779B2 (en) 2008-01-16 2015-10-06 Shell Oil Company Process to provide a particulate solid material to a pressurised reactor
EP3214194A4 (de) * 2014-10-29 2018-03-14 Nippon Steel & Sumitomo Metal Corporation Austenitischer edelstahl und herstellungsverfahren dafür
CN108138280A (zh) * 2015-09-30 2018-06-08 新日铁住金株式会社 奥氏体系不锈钢以及奥氏体系不锈钢的制造方法
EP3358030A4 (de) * 2015-09-30 2019-04-03 Nippon Steel & Sumitomo Metal Corporation Austenitischer edelstahl und verfahren zur herstellung von austenitischem edelstahl
WO2020127788A1 (de) * 2018-12-20 2020-06-25 Voestalpine Böhler Edelstahl Gmbh Co. Superaustenitischer werkstoff
CN113544294A (zh) * 2018-12-20 2021-10-22 奥钢联百乐特殊钢有限两合公司 超级奥氏体材料

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