EP0549286B1 - Gegen hohe Temperatur beständige Ni-Cr-Legierung - Google Patents

Gegen hohe Temperatur beständige Ni-Cr-Legierung Download PDF

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Publication number
EP0549286B1
EP0549286B1 EP92311611A EP92311611A EP0549286B1 EP 0549286 B1 EP0549286 B1 EP 0549286B1 EP 92311611 A EP92311611 A EP 92311611A EP 92311611 A EP92311611 A EP 92311611A EP 0549286 B1 EP0549286 B1 EP 0549286B1
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EP
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Prior art keywords
alloy
yttrium
nitrogen
chromium
less
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Revoked
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EP92311611A
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English (en)
French (fr)
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EP0549286A1 (de
Inventor
Ian Christopher Elliott
Wai-Yan Chan
Norman Charles Farr
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Inco Alloys Ltd
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Inco Alloys Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W

Definitions

  • This invention is related to the field of Ni-Cr-Fe alloys and particularly to alloys used in high temperature (1200°C) applications.
  • Ni-Cr-Fe alloys such as INCONEL® alloy 601 have historically been used for general-purpose engineering applications requiring heat and corrosion resistance. (INCONEL is a registered trademark of the Inco family of companies.) In addition, INCONEL alloy 601 has excellent resistance to thermal cycle fatigue in combination with high temperature oxidation resistance. Commercial uses of INCONEL alloy 601 include thermal processing equipment, chemical processing applications, petrochemical applications, pollution control applications and turbine engine components.
  • INCONEL alloy 601 has been widely used as a roller alloy for applications within high temperature kilns used in firing of ceramic tiles.
  • rollers are typically exposed to oxidizing conditions at temperatures as high as 1000°C or 1165°C. At such high temperatures, roller alloys have a tendency to slowly fail due to gradual oxidation. At increased temperatures of about 1200°C, oxidation rate and spalling rate increase unacceptably.
  • the invention provides a heat and corrosion resistant alloy as defined in the accompanying claims.
  • Figure 1 is a plot of mass change versus time for various alloys in an air atmosphere at 1165°C.
  • Figure 2 is a plot of mass charge versus time for various alloys in an air atmosphere at 1200°C.
  • the invention provides a Ni-Cr-Fe-Al alloy with improved high temperature cyclic oxidation resistance.
  • a nickel-base alloy containing a combination of chromium, yttrium, silicon and aluminum has been found to dramatically improve oxidation resistance at 1200°C.
  • the 1200°C temperature is particularly useful for kilns used for firing lead-free frits.
  • test heats of Ni-Cr-Fe alloys were cast into 10 kg ingots.
  • Ingot 7 originated from a commercial heat.
  • Chemical compositions of the test heats expressed in weight percent are given below in Table 1. (All compositions in this specification are expressed in weight percent unless specifically indicated.)
  • Ingot numbers 1-6 represent experimental heats; and Ingot number 7 represents an alloy within the commercial range of INCONEL alloy 601.
  • the ingots were machined, dressed and forged at 1140°C into 50.8 mm round bars. The round bars were annealed at 1175°C for 30 minutes.
  • Test coupons were machined from forged bar into plates having approximate dimensions of 15 mm x 20 mm x 3 mm. Plates were pierced with a 3 mm diameter hole for attaching the coupon to a jig. All oxidation test specimens were polished with silicon carbide paper to a 240 grade finish. Following recordation of sample size, all test samples were degreased and dried in hot air.
  • sample numbers correspond to the ingot numbers of Table 1. From the above high temperature experiment it was determined that the composition of ingot 4 at 1200°C provided the best oxidation resistance. Scale integrity was found to increase with decreased amounts of titanium. Segregation of yttrium rich phases at the alloy/scale interface was found to increase scale adhesion and may have an effect in modifying alloy oxidation mechanism leading to improved oxidation resistance. The tightly adherent scale layer of high yttrium sample number 4 was found to provide an effective barrier for preventing internal oxidation. In addition, the increased aluminum content of sample number 4 was believed to also contribute high temperature stability of the oxide scale.
  • Alloy A provided a Ni-Cr-Fe-Al alloy with improved high temperature (1200°C) oxidation resistance.
  • a combination of chromium, yttrium, silicon and aluminum was found to dramatically improve oxidation resistance.
  • the improved Ni-Cr-Fe-Al alloy had only a slight decrease in hot ductility in comparison to commercial INCONEL alloy 601.
  • the first series of tests containing the compositions listed below in Table 4 was prepared.
  • the series of 12.5 kg cast ingots were machined, dressed and then forged at about 1150°C to 15 mm thick slabs. Each slab was then hot rolled at about 1150°C in stages to produce 4 mm thick hot band. Each sample was final annealed for 30 minutes at 1177°C and air cooled to room temperature. Prior to oxidation testing, the specimens were ground on silicon carbide paper to a 240 grade finish as previously provided for the samples of Table 1.
  • Table 5 on average were slightly poorer than alloy 601 at 1100°C. However, alloys of the invention provided some improvement in cyclic oxidation at 1200°C. It is believed that results of Table 5 would be improved if the stable oxide were formed by an initial oxidation treatment at a temperature of at least 1100°C prior to testing.
  • Oxidation penetration was also tested for alloys of the invention and alloy 601. Oxidation penetration test result data are given below in Table 7. TABLE 7 OXIDE PENETRATION MEASUREMENTS OF ALLOY A AND RELATED ALLOYS AFTER EXPOSURE FOR SIX WEEKLY CYCLES IN AIR AT TEMPERATURES SHOWN Maximum Depth of Oxidation* mm at Temperatures of Heat No.
  • Nickel in an amount of 55-65% provides workability, fabricability and general oxidation resistance to the alloy. Chromium in an amount of 19-25% provides oxidation resistance. Oxidation resistance is insufficient at less than 19% chromium. At chromium levels above 25%, deleterious chromium phases may form. Initial testing has indicated that chromium levels above 20% have a neutral effect and do not contribute additional oxidation resistance. Aluminum is beneficial to oxidation properties and increased aluminum is believed to contribute to adherence of the oxide scale. Aluminum in an amount of at least 1% or most advantageously at least 2.7% provides high temperature oxidation resistance. Aluminum is limited to 4.5% (preferably 3.5%) to limit adverse hot workability effects.
  • Yttrium in an amount of at least 0.045% and preferably at least 0.05% contributes to stabilizing the oxide.
  • Yttria was not readily visible with optical microscopy in the samples tested. Excess yttrium (above 0.3%) is believed to adversely affect hot workability and welding properties. Most advantageously yttrium is limited to 0.07%.
  • Titanium is added as a reactive element to combine with nitrogen and carbon. At least 0.15% titanium is added for tying up nitrogen. Excess titanium above 1% adversely affects oxidation resistance and workability. Iron acts as an inexpensive substitute for nickel. Most advantageously at least 10% iron is present to lower the cost of the alloy. Furthermore, iron is most advantageously limited to 20 or 18% to limit reduction of nickel's beneficial properties. Carbon in an amount of 0.005% or preferably 0.01% provides adequate grain size control. An upper limit of 0.5% carbon or preferably 0.2% carbon is maintained to limit excessive carbide formation that ties up useful elements and to limit grain boundary embrittlement. At least 0.1% silicon and advantageously 0.5% silicon is added for oxidation resistance. Silicon is limited to 1.5% or preferably 1% to limit weldability and workability problems.
  • Manganese is limited to 1% and most advantageously manganese is limited to 0.5%.
  • At least 0.005% total magnesium, calcium and/or cerium are added for improved malleability and deoxidation.
  • Total magnesium and/or calcium is limited to 0.5% and most advantageously 0.2% to minimize adverse effects upon weldability and workability.
  • Boron in an amount of 0.0001% or preferably 0.001% provides improved malleability. Boron is limited to 0.1% to minimize adverse effects upon malleability and weldability.
  • boron is limited to 0.05% and most advantageously boron is limited to 0.01% or 0.006%.
  • Zirconium may optionally be added for malleability and grain size control.
  • Zirconium reacts with nitrogen to form nitrides that inhibit grain growth at elevated temperature. Zirconium is limited to 0.5% and most advantageously 0.2% to limit adverse effects upon weldability and workability. Similarly, nitrogen is added to provide an effective amount of grain growth resistance. Nitrogen, typically is provided in sufficient quantity as an impurity of raw materials. A quantity of at least 0.0001% nitrogen or 0.001% nitrogen provides resistance against grain growth. Most advantageous grain growth control may be obtained by maintaining a level of at least 0.03% nitrogen. Alternatively, grain growth may be controlled by limiting stored energy in the alloy by additional annealing steps between deformation processes. Nitrogen is limited to 0.2% to avoid excess internal oxidation of beneficial elements. Nitrogen is advantageously limited and most advantageously to 0.1% and 0.05% respectively.
  • Cerium in an amount up to 1% may optionally be added as a magnesium substitute or for additional oxidation resistance.
  • cerium is not necessary for oxidation resistance.
  • Cobalt is acceptable in quantities up to 10% and acts as a substitute for nickel.
  • cobalt is limited to 5% and most advantageously cobalt is maintained below 1%. Due to the relatively high cost of cobalt, cobalt is preferably not deliberately added. Copper, molybdenum, niobium, vanadium and tungsten are advantageously held to the limits of Table 8 to improve appearance of the alloy.
  • copper, molybdenum, niobium, vanadium and tungsten are held as low as commercially practical.
  • Lead, tin, antimony, bismuth, phosphorous, sulfur and oxygen are all incidental impurities maintained at levels as low as commercially practical.
  • the total lead, tin, antimony, bismuth, phosphorous, sulfur plus oxygen level is maintained below 0.1%.
  • alloy of the invention was tested to provide acceptable mechanical properties. Initial welding tests indicated a tendency for solidification cracking linked to increased yttrium content. However, the tests were not performed on alloys of the invention. Alloys of the invention are readily fabricated in seamless tubes by conventional extrusion or extrusion and cold working techniques. The tubes are then cut into short length rollers especially useful for kilns having operating temperatures around 1200°C.
  • the oxide formed at high temperature is extremely adherent and less prone to discoloration of ceramics than conventional alloy 601.
  • the adherent scale is especially useful for white ceramics.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Powder Metallurgy (AREA)
  • Solid Thermionic Cathode (AREA)
  • Chemically Coating (AREA)
  • Fuel Cell (AREA)
  • Heat Treatment Of Steel (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)

Claims (13)

  1. Hitzebeständige korrosionsbeständige Legierung mit (in Gewichtsprozent) 55 bis 65% Nickel, 19 bis 25% Chrom, 1 bis 4,5% Aluminium, 0,045 bis 0,3% Yttrium, 0,15 bis 1% Titan, 0,605 bis 0,5% Kohlenstoff, 0,1 bis 1,5% Silizium, 0 bis 1% Mangan, mindestens 0,005% mindestens eines der Elemente Magnesium, Kalzium und Cer, unter 0,5% Magnesium und Kalzium, unter 1% Cer, 0,0001 bis 0,1% Bor, 0 bis 0,5% Zirkonium, 0,0001 bis 0,2% Stickstoff, 0 bis 10% Kobalt, 0 bis 0,5% Kupfer, 0 bis 0,5% Molybdän, 0 bis 0,3% Niob, 0 bis 0,1% Vanadium und 0 bis 0,1% Wolfram, Rest Eisen und Verunreinigungen.
  2. Legierung nach Anspruch 1, die jedoch 19 bis 22% Chrom, 2,5 bis 4% Aluminium, 0,05 bis 0,15% Yttrium, 0,15 bis 0,75% Titan und 0,5 bis 1% Silizium enthält.
  3. Legierung nach Anspruch 1 oder 2, die jedoch 0,01 bis 0,3% Kohlenstoff, 0,005 bis 0,2% Magnesium, 0,001 bis 0,05% Bor und 0,001 bis 0,1% Stickstoff enthält.
  4. Legierung nach Anspruch 1, die jedoch 57,5 bis 62,5% Nickel, 19 bis 22% Chrom, 2,5 bis 4% Aluminium, 0,05 bis 0,15% Yttrium, 0,15 bis 0,75% Titan, 0,01 bis 0,3% Kohlenstoff, 0,5 bis 1% Silizium, unter 0,2% Magnesium und Kalzium, 0,001 bis 0,05% Bor, 0 bis 0,4% Zirkonium und 0 bis 5% Kobalt enthält.
  5. Legierung nach Anspruch 4, die jedoch 19,5 bis 21% Chrom, 2,7 bis 3,5% Aluminium, 0,05 bis 0,07% Yttrium und 0,3 bis 0,75% Titan enthält.
  6. Legierung nach Anspruch 4 oder 5, die jedoch 0,05 bis 0,15% Kohlenstoff, 0,005 bis 0,2% Magnesium, 0,001 bis 0,01% Bor und 0,001 bis 0,05% Stickstoff enthält.
  7. Legierung nach einem der Ansprüche 1 bis 6, die jedoch unter 20% Eisen enthält.
  8. Legierung nach Anspruch 7, die jedoch 10 bis 18% Eisen enthält.
  9. Legierung nach Anspruch 1, die jedoch 57,5 bis 62,5% Nickel, 19,5 bis 21% Chrom, 2,7 bis 3,5% Aluminium, 0,05 bis 0,07% Yttrium, 0,3 bis 0,75% Titan, 0,5 bis 1% Silizium, 0 bis 0,5% Mangan, unter 0,2% Mangan und Kalzium, 0,001 bis 0,01% Bor, 0 bis 0,2% Zirkonium, 0,001 bis 0,05% Stickstoff, 0 bis 1% Kobalt und 10 bis 18% Eisen enthält.
  10. Legierung nach einem der Ansprüche 1 bis 9, die jedoch unter insgesamt 0,1% Blei, Zinn, Antimon, Wismut, Phosphor, Schwefel und Sauerstoff als Verunreinigungen enthält.
  11. Legierung nach einem der Ansprüche 1 bis 10, die jedoch mindestens 0,03% Stickstoff enthält.
  12. Verwendung einer Legierung nach einem der Ansprüche 1 bis 11 als Werkstoff zum Herstellen von hohen Betriebstemperaturen, insbesondere in Öfen ausgesetzten Gegenständen.
  13. Gegenstand zur Verwendung bei hohen Betriebstemperaturen, insbesondere Ofenteil aus einer Legierung nach einem der Ansprüche 1 bis 11.
EP92311611A 1991-12-20 1992-12-18 Gegen hohe Temperatur beständige Ni-Cr-Legierung Revoked EP0549286B1 (de)

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Application Number Priority Date Filing Date Title
US81258491A 1991-12-20 1991-12-20
US98911292A 1992-12-11 1992-12-11
US989112 1992-12-11
US812584 1997-03-07

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EP0549286A1 EP0549286A1 (de) 1993-06-30
EP0549286B1 true EP0549286B1 (de) 1995-06-14

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AT (1) ATE123819T1 (de)
DE (1) DE69202965T2 (de)
ES (1) ES2073873T3 (de)

Cited By (8)

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DE102012011162A1 (de) * 2012-06-05 2013-12-05 Outokumpu Vdm Gmbh Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102012011161A1 (de) 2012-06-05 2013-12-05 Outokumpu Vdm Gmbh Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102014001329A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001330A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001328A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Eisen-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102015008322A1 (de) * 2015-06-30 2017-01-05 Vdm Metals International Gmbh Verfahren zur Herstellung einer Nickel-Eisen-Chrom-Aluminium-Knetlegierung mit einer erhöhten Dehnung im Zugversuch
DE102015016729A1 (de) * 2015-12-22 2017-06-22 Vdm Metals International Gmbh Verfahren zur Herstellung einer Nickel-Basislegierung
CN110527856A (zh) * 2019-09-20 2019-12-03 无锡市东杨新材料股份有限公司 一种高表面质量、高强度镍合金带材的制备方法

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DE19524234C1 (de) * 1995-07-04 1997-08-28 Krupp Vdm Gmbh Knetbare Nickellegierung
US5997809A (en) * 1998-12-08 1999-12-07 Inco Alloys International, Inc. Alloys for high temperature service in aggressive environments
US6287398B1 (en) * 1998-12-09 2001-09-11 Inco Alloys International, Inc. High strength alloy tailored for high temperature mixed-oxidant environments
GB2361933A (en) * 2000-05-06 2001-11-07 British Nuclear Fuels Plc Melting crucible made from a nickel-based alloy
DE10302989B4 (de) 2003-01-25 2005-03-03 Schmidt + Clemens Gmbh & Co. Kg Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung
JP4506958B2 (ja) * 2004-08-02 2010-07-21 住友金属工業株式会社 溶接継手およびその溶接材料
SE529003E (sv) * 2005-07-01 2011-10-11 Sandvik Intellectual Property Ni-Cr-Fe-legering för högtemperaturanvändning
US9551051B2 (en) 2007-12-12 2017-01-24 Haynes International, Inc. Weldable oxidation resistant nickel-iron-chromium aluminum alloy
US8506883B2 (en) 2007-12-12 2013-08-13 Haynes International, Inc. Weldable oxidation resistant nickel-iron-chromium-aluminum alloy
CN102216479B (zh) * 2008-11-19 2014-11-26 山特维克知识产权股份有限公司 形成氧化铝的镍基合金
DE102009038693B4 (de) * 2009-08-24 2017-11-16 Sunfire Gmbh Oxidationsbeständiger Verbundleiter und Herstellungsverfahren für den Verbundleiter sowie Brennstoffzellensystem
DE102012013437B3 (de) * 2011-02-23 2014-07-24 VDM Metals GmbH Verwendung einer Nickel-Chrom-Eisen-Aluminium-Legierung mit guter Verarbeitbarkeit
DE102012015828B4 (de) 2012-08-10 2014-09-18 VDM Metals GmbH Verwendung einer Nickel-Chrom-Eisen-Aluminium-Legierung mit guter Verarbeitbarkeit
CN104827206B (zh) * 2015-05-09 2017-01-25 芜湖鼎恒材料技术有限公司 一种Ni‑Cr‑Al纳米焊层及制备方法
DE102018107248A1 (de) 2018-03-27 2019-10-02 Vdm Metals International Gmbh Verwendung einer nickel-chrom-eisen-aluminium-legierung
DE102020132193A1 (de) 2019-12-06 2021-06-10 Vdm Metals International Gmbh Verwendung einer Nickel-Chrom-Eisen-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
CN112921226B (zh) * 2021-02-16 2022-05-17 河南工学院 一种用于镁铝系合金的Mg-AlN中间合金晶粒细化剂及其制备方法
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CN114231795A (zh) * 2021-12-23 2022-03-25 佛山市天禄智能装备科技有限公司 用于回转窑的耐高温合金的制备方法及回转窑窑体
CN118006968B (zh) * 2024-04-08 2024-06-18 无锡市雪浪合金科技有限公司 一种镍基高温合金及其制备方法

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DE102012011162A1 (de) * 2012-06-05 2013-12-05 Outokumpu Vdm Gmbh Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102012011161A1 (de) 2012-06-05 2013-12-05 Outokumpu Vdm Gmbh Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
WO2013182177A1 (de) 2012-06-05 2013-12-12 Outokumpu Vdm Gmbh Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit
DE102012011162B4 (de) * 2012-06-05 2014-05-22 Outokumpu Vdm Gmbh Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102012011161B4 (de) * 2012-06-05 2014-06-18 Outokumpu Vdm Gmbh Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102014001328B4 (de) * 2014-02-04 2016-04-21 VDM Metals GmbH Aushärtende Nickel-Chrom-Eisen-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001330A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001328A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Eisen-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001329A1 (de) * 2014-02-04 2015-08-06 VDM Metals GmbH Aushärtende Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001329B4 (de) * 2014-02-04 2016-04-28 VDM Metals GmbH Verwendung einer aushärtenden Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
DE102014001330B4 (de) * 2014-02-04 2016-05-12 VDM Metals GmbH Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
US10870908B2 (en) 2014-02-04 2020-12-22 Vdm Metals International Gmbh Hardening nickel-chromium-iron-titanium-aluminium alloy with good wear resistance, creep strength, corrosion resistance and processability
US11098389B2 (en) 2014-02-04 2021-08-24 Vdm Metals International Gmbh Hardened nickel-chromium-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and workability
DE102015008322A1 (de) * 2015-06-30 2017-01-05 Vdm Metals International Gmbh Verfahren zur Herstellung einer Nickel-Eisen-Chrom-Aluminium-Knetlegierung mit einer erhöhten Dehnung im Zugversuch
DE102015016729A1 (de) * 2015-12-22 2017-06-22 Vdm Metals International Gmbh Verfahren zur Herstellung einer Nickel-Basislegierung
DE102015016729B4 (de) 2015-12-22 2018-10-31 Vdm Metals International Gmbh Verfahren zur Herstellung einer Nickel-Basislegierung
CN110527856A (zh) * 2019-09-20 2019-12-03 无锡市东杨新材料股份有限公司 一种高表面质量、高强度镍合金带材的制备方法
CN110527856B (zh) * 2019-09-20 2021-04-30 无锡市东杨新材料股份有限公司 一种高表面质量、高强度镍合金带材的制备方法

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DE69202965D1 (de) 1995-07-20
ES2073873T3 (es) 1995-08-16
DE69202965T2 (de) 1996-03-14
EP0549286A1 (de) 1993-06-30
ATE123819T1 (de) 1995-06-15

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