EP0434887A1 - Hitzebeständiger austenitischer rostfreier Stahl - Google Patents

Hitzebeständiger austenitischer rostfreier Stahl Download PDF

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Publication number
EP0434887A1
EP0434887A1 EP90102879A EP90102879A EP0434887A1 EP 0434887 A1 EP0434887 A1 EP 0434887A1 EP 90102879 A EP90102879 A EP 90102879A EP 90102879 A EP90102879 A EP 90102879A EP 0434887 A1 EP0434887 A1 EP 0434887A1
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Prior art keywords
content
steel
hot
steels
corrosion
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EP90102879A
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English (en)
French (fr)
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EP0434887B1 (de
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Yoshihiro Uematsu
Isami Shimizu
Naoto Hiramatsu
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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
    • 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
    • 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

  • This invention relates to a heat-resistant austenitic stainless steel which has excellent high temperature salt corrosion resistance as well as hot salt corrosion resistance of welds in addition to weld hot cracking resistance, hot-workability and weldability, and is usable in hot-corrosive environments, especially under conditions that the steel is subjected to repeated heating and cooling in environments in which corrosion by salt, including corrosion by molten salt, may occur.
  • Heat-resistant steels are employed for uses under severely corrosive conditions such as automobile exhaust emission control systems, parts of furnaces, parts of heat-exchangers, electric appliances for cooking such as electric range and grill.
  • Such steels are required to be provided with hot gas corrosion resistance under burning conditions, hot corrosion resistance in environments containing various oxides such as PbO, V2O5, etc., chlorides such as PbCl2, NaCl, MgCl2, KCl, etc., and resistance to hot corrosion by molten salt in addition to general high temperature characteristics such as high temperature strength, high temperature oxidation resistance, adherence of scale, etc.
  • these steels must be resistive to wet corrosion by condensed water at low temperatures. Under these severely corrosive environments, carbon steel sheets which are surface-treated for heat resistance cannot stand, and, therefore, heat-resistant austenitic stainless steels are used.
  • incinerators for treating a large quantity of waste materials tuyere burners of blast furnaces, heavy oil burners, exhaust gas pipes of internal combustion engines, etc. and parts of apparatus which are used in environments in which adhesion of salt or ash occurs such as in the cold districts where antifreezing agents are sprinkled on the roads, often suffer remarkable high temperature corrosion.
  • Investigations of cases of this kind of corrosion have revealed that accelerated oxidation of intergranular corrosion type is observed in common in all the cases. This is a corrosion by adhering salt or molten salt and the corrosion with chlorides is marked.
  • Japanese Laid-Open Patent Publication No. 63-213643 (1988) discloses a stainless steel having excellent high temperature corrosion resistance in the presence of chlorides, said steel comprising not more than 0.03% C, 10 - 20% Cr, 10 - 30% Ni, not more than 2% Mn, 1 - 6% Si, 0.5 - 5% Mo and 0.02 - 0.4% N, wherein the D value defined as 24.4 Cr + 28 Ni + 6.7 Mn - 48.8 Si - 56.9 Mo - 148.0 Nb is not more than 500.
  • the steel may contain 0.1 - 1% in total of at least one of Ti, Zr, Nb and Ta. However, improvement in weld hot cracking resistance is not considered in this steel.
  • a heat-resistant austenitic stainless steel basically comprising:
  • Nb, Ti and V at least one of Nb, Ti and V: 0.05 - 0.5% in total and/or
  • REM 0.005 - 0.1% (Rare Earth Metal), the balance being Fe and unavoidable impurities, wherein the value of (Si% + Mo%) (Formula (1) below) is not less than 3, the value % (2.5 Si% + Mo%) (Formula (2) below) is not more than 11 and the D value represented by Formula (3) below is not less than 6 and not more than 11, when the steel contains REM or B from the viewpoint of weldability, and is not less than 7 and not more than 11 when the steel does not contain these elements.
  • the D values as defined above of all the steels of the working examples described in the above-mentioned Japanese Laid-Open Patent Publication No. 63-213643 are less than 4.
  • We have found that the weld hot cracking resistance of austenitic stainless steels containing high-Mo high-Si is improved by adjusting the composition so that said D value is more than 6 or 7.
  • the preferred steels of the present invention have the composition: C: 0.03 - 0.06%, Si: 2 - 3%, Mn: 0.5 - 1%, P: not more than 0.03%, S: not more than 0.005%, Ni: 12 - 16%, Cr: 16 - 18%, Mo: 2 - 3.2%, Al: 0.01 - 0.03%, N: not more than 0.03% and the balance being Fe and unavoidable impurities.
  • the more preferred steels of the present invention have the composition: C: 0.03 - 0.05, Si: 2 - 2.8, Mn: 0.5 - 1%, P: not mroe than 0.03, S: not more than 0.005%, Ni: 12 - 14, Cr: 16 - 18%, Mo: 2 - 2.8, Al: 0.01 - 0.03%, N: not more than 0.03% and the balance being Fe and unavoidable impurities.
  • This element that is unavoidable is a strong austenite former and an important necessary component for the steel of the present invention from the viewpoint of the composition balance. Carbon is also useful for saving expensive nickel. Further C is an interstitial solute and effective for enhancing the high temperature strength. However, the addition of an excessive amount of C makes the steel brittle and deteriorates workability. From such consideration, the upper limit of the content is defined as 0.06%. On the other hand, the reduction of the C content lengthens the refining time and thus invites increase of the manufacturing cost and at least 0.03% of C is required for the desired high temperature strength.
  • Si This element is one of the most important components that improve oxidation resistance and high temperature salt corrosion. At least 1% and preferably 2% of this element is required to achieve the satisfactory effect thereof. On the other hand, Si induces precipitation of the ⁇ -phase, which deteriorates toughness of the steel. Also, this element deteriorates hot workability, weldability and formability. From the consideration of these facts the upper limit content of this element is defined as 4%, preferably, 3%.
  • Mn This element is effective for fixing and excluding the deleterious S as MnS. If the Mn content is not sufficient, MnS deposits as a film at the granular interfaces and promotes deterioration of the intergranular strength. But MnS globurizes and reduces its effect for deteriorating intergranular strength when Mn is contained in higher concentration. At least 0.5% Mn is required but its effect saturates at around 4%. Thus the Mn content is defined as 0.5 - 4%. When the D value is considered, however, the Mn content is preferably not more than 1%.
  • Ni This element is one of the fundamental elements of austenitic stainless steels. From the viewpoint of the weld hot cracking resistance, the lower limit of the content thereof is defined as 10%, because ⁇ -ferrite must be formed in the weld. The upper limit is defined as 17% from the consideration of the balance of the composition and the manufacturing cost. When the D value is considered, however, the preferred content of Ni is 12 - 16%.
  • Mo This element is effective for achieving corrosion resistance in high temperature corrosive environments and high temperature salt-corrosive environments and thus must be positively added.
  • the lower limit of the content thereof is defined as 1%, since the effect thereof cannot be well exhibited with less than 1%.
  • Mo is an expensive element and promotes deposition of the ⁇ -phase and thus invites deterioration of toughness of the steel. With addition of over 4%, hot workability of the steel is impaired. Therefore, the Mo content should be not higher than 4%. When the D value is considered, 2 - 3.2% is preferred.
  • Al This is a most effective element for improvement of oxidation resistance and effective for improving the cleanness of the steel. It is desired that Al is contained in an amount of at least 0.01%. However, Al is a strong ferrite former and thus the upper limit is restricted to 0.5% from the viewpoint of the composition balance as well as of the toughness of the product. When the D value is considered, the preferred range is 0.01 - 0.03%.
  • B This element is effective for enhancing intergranular strength and improving hot workability and weld hot cracking resistance. With less than 0.0005%, however, the effect is not remarkable. With more than about 0.02%, borides are formed, which degrade the intergranular strength. Therefore, the B content is defined as 0.0005 - 0.02%.
  • Nb, Ti and V These elements combine with C and N to form minute precipitate and thus are effective for corrosion resistance as well as high temperature strength, especially for improvement of creep strength. These effects are manifested at the content of 0.05% or higher. However, as the content increases, workability and toughness are deteriorated. Therefore, the upper limit is defined as 0.5% in total. The preferred range is 0.05 - 0.4%.
  • REM These elements fix deleterious S as high melting point compounds at the early stage of solidification and thus improve cracking susceptibility. Also, they are effective for enhancing the resistance to pealing off of the oxide scales which result from heating-cooling cycles. These effects are manifested at the content of 0.005% or higher. And this deteriorate intergranular strength at high temperatures, which spoils the improvement in the hot cracking susceptibility. On the contrary, when REM are contained in too high concentrations, large amounts of REM oxides deposit at the grain boundaries. Therefore, the upper limit is restricted to 0.1% or less.
  • Cu This element is effective for improvement of stress corrosion cracking resistance and weatherability, for which at least 0.5% is required.
  • the upper limit is defined as 2.5%.
  • the preferred content range is 1 - 1.3%.
  • N This element is effective for improvement of high temperature strength. However, excessive addition of N impairs workability and thus the upper limit is defined as 0.03% or less.
  • the total amount of Si and Mo is regulated by formulas (1) and (2).
  • the lower limit value (Si% + Mo%) must be 3 or more for better hot molten salt corrosion resistance.
  • the upper limit value (2.5 Si% + Mo%) must be 11 or less in order to minimize degradation in hot workability, weld hot cracking resistance, ⁇ -brittleness resistance and formability.
  • the reason why the D value is defined as above in as follows. Steels containing high Si or high Mo are very susceptible to weld hot cracking.
  • the D value is an index for precipitation of ferrite.
  • the D value must be 6 or more when REM or B is contained and 7 or more when they are not contained. Appearance of a larger amount of ⁇ -ferrite causes hot work cracking and deteriorates manufacturability.
  • the upper limit of the D value is defined as 11.
  • Fig. 1 is a graph showing the relation between the corrosion weight loss (mg/cm2) and the (Si + Mo)% value with respect to the steels of the present invention.
  • Fig. 2 is a graph showing the relation between the null point and the 2.5(Si + Mo)% value with respect to the steels of the present invention.
  • Fig. 3 is a graph showing the relation between the critical strain ⁇ c (%) and the D value of the steel.
  • Figs. 4 - 6 are microphotographs (x about 70) of TIG welding welds which were subjected to repeated heating in the presence of NaCl of SUS304 steel, SUSXM15JI steel and a steel of the present invention respectively.
  • steels the compositions of which are shown in Table 1 were prepared by vacuum melting and specimens thereof were subjected to the high temperature tensile tests and the high temperature salt corrosion test.
  • the high temperature tensile test 20 x 20 x 110 mm pieces were prepared from ingots, the pieces were heat-treated at 1200°C for 2 hours and they were worked into rod specimens having a diameter of 10 mm.
  • the high temperature salt corrosion test ingots were forged into 30 mm thick plates, which were held at 1200°C and thereafter hot-rolled to 5 mm in thickness and further reduced to 2 mm by ordinary cold rolling and the plates were finally annealed.
  • Fig. 2 shows the relation between the null point and the (Si + Mo)% value.
  • the null point is the temperature at which the rupture reduction value (the value of cross-sectional reduction at rupture), is 0 when the steel specimens were subjected to a high speed high temperature tensile test at 800 - 1400°C and the rupture reduction value in % were measured. From these results, it is apparent that the null point is lowered as the contents of Si and Mo increase, and, especially, the effect of Si is 2.5 times that of Mo. This is because liquation cracking owing to intergranular melting is promoted when the contents of Si and Mo increase. Therefore, addition of large amounts of Si and Mo is not allowed and it is desirable that (2.5 Si + Mo) is not more than 11.
  • addition of Si and Mo is regulated by the total amount thereof.
  • the lower limit is determined from the viewpoint of hot salt corrosion resistance and the upper limit is determined from the viewpoint of hot-workability, weld hot cracking and ⁇ - brittleness.
  • B is added. That is,B, which enhances intergranular strength, is effective for improvement of hot-workability.
  • Figs. 4, 5 and 6 are photomicrographs (x Ca. 70) of welds of repsectively of SUS304, SUSXM15J1 and the E57 steel specimens which underwent the following test. That is, the steels were made into plates the thickness of which is 0.3 mm or less by the ordinary hot and cold rolling and annealing. After the steel specimens were subjected to TIG welding. They were wetted with a 5 % NaCl solution of 60°C for 1 hour, dried at 60°C for 3 days and held at 350°C for 4 hours, and this cycle was repeated 10 times.
  • Ingots of the steels of Table 2 were prepared by vacuum melting and made into 30 mm thick slabs by forging, the slabs were held at 1200°C and thereafter, they were hot-rolled to 5 mm thick plates and further cold-rolled to 1.5 mm thick plates, which were finally annealed. The plates were worked into 40 x 200 mm specimens.
  • the weld hot cracking test was carried out by holding the two ends of a specimen by the chucks and subjecting the specimen to TIG welding under a longitudinal tensile load applied. Five to ten welded samples were obtained with tensile load varied. After welding, the strain was measured from the marking lines scratched beforehand.
  • Steel E75 which does not positively contain Mo, suffers high degree corrosion and the null point thereof is low because of high content of Si. Although the D value was adjusted to 8.8 so that some amount of ⁇ - ferrite was formed, the critical strain is very low because of high content of Si. Steel E76, which contains high degrees of Si and Mo, has a low null point and a very low critical strain. Steel F6, the composition of which falls in the general composition range of the present invention but out of the claimed scope in that the D value thereof is as low as 4.5, exhibited an extremely low critical strain.
  • Steels F1 and E57 of the present invention contain Si and Mo, which are effective for hot salt corrosion resistance, exhibited small corrosion weight losses, high critical strains and high null points, because the D value is adjusted to 8.5.
  • Steel E60 contains Si and Mo, which are effective for hot salt corrosion resistance, as well as Cu, which is effective for stress corrosion cracking resistance, recorded a small corrosion weight loss, a high critical strain and a high null point like F1 and E57.
  • Steels E61 - E66 and F9 positively contain Si and Mo like the above-described steels, and, therefore, their corrosion weight losses are small.
  • E61 contains Nb and Ti which are especially effective for improvement of creep strength
  • E62 contains V from the same consideration
  • E64 contain Cu, Nb and V and their D values were adjusted to 6.2 - 8.5, which is a range proper for prevention of weld hot cracking.
  • These steels exhibited high critical strain values.
  • Steels F9, E63, E65 and E66 contain B, which is effective for improving hot workability, and in addition to Cu, Nb or Ti or V. Therefore, they exhibited high null points.
  • Steels F10 and E67 - E73 positively contain Si and Mo, which are effective for hot salt cracking resistance, like the above-described steels and, therefore, their corrosion weight losses are small. They also contain REM, which are effective for improvement of weld hot cracking and, resistance therefore, they recorded high critical strain values although their D values are relatively low.
  • E67 further contains Cu
  • E68 contains Nb
  • E71 contains Cu and Nb, but their null points are high.
  • E69, E70, E72 and E73 contains B in addition to REM or Nb, etc., and, therefore, their null points are high.
  • the steels of the present invention are provided with excellent hot salt corrosion resistance, excellent weld hot cracking resistance as well as excellent hot-workability.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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EP90102879A 1989-12-20 1990-02-14 Hitzebeständiger austenitischer rostfreier Stahl Expired - Lifetime EP0434887B1 (de)

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JP330128/89 1989-12-20
JP1330128A JP2530231B2 (ja) 1989-12-20 1989-12-20 耐熱用オ―ステナイト系ステンレス鋼

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EP0434887A1 true EP0434887A1 (de) 1991-07-03
EP0434887B1 EP0434887B1 (de) 1994-12-14

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KR (1) KR930005899B1 (de)
CA (1) CA2010174C (de)
DE (1) DE69015140T2 (de)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0658633A2 (de) * 1989-05-16 1995-06-21 Nippon Steel Corporation Rostfreie Stahlfolie für Katalysatorträger in Auspuffentgiftungsanlagen für Kraftfahrzeuge und Verfahren zu ihrer Herstellung
WO1999006602A1 (en) * 1997-08-01 1999-02-11 Acciai Speciali Terni S.P.A. Austenitic stainless steel strips having good weldability as cast
EP1311711A1 (de) * 2000-08-18 2003-05-21 ATI Properties, Inc. Oxidations- und korrosionsresistente austenitische rostfreie stähle mit molybdän
EP1352980A1 (de) * 2000-12-14 2003-10-15 Yoshiyuki Shimizu Siliciumreicher nichtrostender stahl
US20110248071A1 (en) * 2008-12-18 2011-10-13 Japan Atomic Energy Agency Austenitic welding material, and preventive maintenance method for stress corrosion cracking and preventive maintenance method for intergranular corrosion, using same
US20190283189A1 (en) * 2018-03-15 2019-09-19 Nisshin Steel Co., Ltd. Stainless steel material for diffusion bonding jig
CN114438408A (zh) * 2021-12-31 2022-05-06 嘉兴精科科技有限公司 一种低成本高强度耐热耐蚀不锈钢材料及应用其生产的精密零件的制备方法
CN114635077A (zh) * 2020-12-16 2022-06-17 宝武特种冶金有限公司 一种超级奥氏体不锈钢及其制备方法

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JP2602411B2 (ja) * 1994-06-02 1997-04-23 日本冶金工業株式会社 熱間加工性および温水中での耐食性に優れるオーステナイト系ステンレス鋼
JP3572789B2 (ja) * 1996-03-26 2004-10-06 住友金属工業株式会社 耐高温塩害腐食性に優れたオーステナイト系ステンレス鋼
KR100286679B1 (ko) * 1996-12-23 2001-04-16 이구택 내열 내마모 합금
JP3901293B2 (ja) * 1997-07-25 2007-04-04 日新製鋼株式会社 耐食性に優れた焼却炉体
JP3923163B2 (ja) * 1998-01-26 2007-05-30 日新製鋼株式会社 廃棄物焼却炉
JP4485325B2 (ja) * 2004-11-05 2010-06-23 新日鐵住金ステンレス株式会社 耐高温塩害性に優れたオーステナイト系ステンレス鋼
US7985304B2 (en) 2007-04-19 2011-07-26 Ati Properties, Inc. Nickel-base alloys and articles made therefrom
JP4775910B2 (ja) * 2007-05-17 2011-09-21 日新製鋼株式会社 耐高温塩害腐食性に優れたオーステナイト系ステンレス鋼
JP6618670B2 (ja) * 2014-03-14 2019-12-11 日鉄日新製鋼株式会社 耐σ脆化特性および溶接性に優れた高耐食オーステナイト系ステンレス鋼
JP6879133B2 (ja) * 2017-09-05 2021-06-02 日本製鉄株式会社 オーステナイト系ステンレス溶接部材

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2228119A1 (de) * 1973-05-04 1974-11-29 Nippon Steel Corp
FR2324752A1 (fr) * 1975-06-24 1977-04-15 Sandvik Ab Acier inoxydable resistant a l'acide sulfurique concentre
DE3241414A1 (de) * 1981-11-10 1983-05-19 Japan Atomic Energy Research Institute, Tokyo Hochtemperaturbestaendiger stahl fuer hochtemperaturgasofen

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5416444A (en) * 1977-07-07 1979-02-07 Sumitomo Chem Co Ltd Optically active alpha-cyano-3-phenoxybenzyl 2-(4-chlorophenyl)-isovalerate and its preparation
JPS60230966A (ja) * 1984-04-27 1985-11-16 Sumitomo Metal Ind Ltd 塩化物の存在する高温乾食環境用鋼

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2228119A1 (de) * 1973-05-04 1974-11-29 Nippon Steel Corp
FR2324752A1 (fr) * 1975-06-24 1977-04-15 Sandvik Ab Acier inoxydable resistant a l'acide sulfurique concentre
DE3241414A1 (de) * 1981-11-10 1983-05-19 Japan Atomic Energy Research Institute, Tokyo Hochtemperaturbestaendiger stahl fuer hochtemperaturgasofen

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0658633A3 (de) * 1989-05-16 1995-10-25 Nippon Steel Corp Rostfreie Stahlfolie für Katalysatorträger in Auspuffentgiftungsanlagen für Kraftfahrzeuge und Verfahren zu ihrer Herstellung.
EP0658633A2 (de) * 1989-05-16 1995-06-21 Nippon Steel Corporation Rostfreie Stahlfolie für Katalysatorträger in Auspuffentgiftungsanlagen für Kraftfahrzeuge und Verfahren zu ihrer Herstellung
WO1999006602A1 (en) * 1997-08-01 1999-02-11 Acciai Speciali Terni S.P.A. Austenitic stainless steel strips having good weldability as cast
AU724431B2 (en) * 1997-08-01 2000-09-21 Acciai Speciali Terni S.P.A. Austenitic stainless steel strips having good weldability as cast
US6568462B1 (en) 1997-08-01 2003-05-27 Acciai Speciali Terni S.P.A. Austenitic stainless steel strips having good weldability as cast
EP1311711A4 (de) * 2000-08-18 2004-09-22 Ati Properties Inc Oxidations- und korrosionsresistente austenitische rostfreie stähle mit molybdän
EP1311711A1 (de) * 2000-08-18 2003-05-21 ATI Properties, Inc. Oxidations- und korrosionsresistente austenitische rostfreie stähle mit molybdän
EP1352980A4 (de) * 2000-12-14 2004-11-17 Yoshiyuki Shimizu Siliciumreicher nichtrostender stahl
EP1352980A1 (de) * 2000-12-14 2003-10-15 Yoshiyuki Shimizu Siliciumreicher nichtrostender stahl
US20110248071A1 (en) * 2008-12-18 2011-10-13 Japan Atomic Energy Agency Austenitic welding material, and preventive maintenance method for stress corrosion cracking and preventive maintenance method for intergranular corrosion, using same
US8322592B2 (en) * 2008-12-18 2012-12-04 Japan Atomic Energy Agency Austenitic welding material, and preventive maintenance method for stress corrosion cracking and preventive maintenance method for intergranular corrosion, using same
US20190283189A1 (en) * 2018-03-15 2019-09-19 Nisshin Steel Co., Ltd. Stainless steel material for diffusion bonding jig
EP3567127A4 (de) * 2018-03-15 2019-11-13 Nisshin Steel Co., Ltd. Edelstahlmaterial zur verwendung in diffusionsschweissgestellen
CN110494580A (zh) * 2018-03-15 2019-11-22 日新制钢株式会社 扩散接合夹具用不锈钢材
US10695874B2 (en) 2018-03-15 2020-06-30 Nisshin Steel Co., Ltd. Stainless steel material for diffusion bonding jig
CN114635077A (zh) * 2020-12-16 2022-06-17 宝武特种冶金有限公司 一种超级奥氏体不锈钢及其制备方法
CN114438408A (zh) * 2021-12-31 2022-05-06 嘉兴精科科技有限公司 一种低成本高强度耐热耐蚀不锈钢材料及应用其生产的精密零件的制备方法
CN114438408B (zh) * 2021-12-31 2022-10-28 嘉兴精科科技有限公司 一种低成本高强度耐热耐蚀不锈钢材料及应用其生产的精密零件的制备方法

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Publication number Publication date
KR910012322A (ko) 1991-08-07
JP2530231B2 (ja) 1996-09-04
JPH03191039A (ja) 1991-08-21
DE69015140D1 (de) 1995-01-26
CA2010174C (en) 2000-09-12
EP0434887B1 (de) 1994-12-14
DE69015140T2 (de) 1995-05-04
CA2010174A1 (en) 1991-06-20
KR930005899B1 (ko) 1993-06-25

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