US3890816A - Elimination of carbide segregation to prior particle boundaries - Google Patents

Elimination of carbide segregation to prior particle boundaries Download PDF

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Publication number
US3890816A
US3890816A US400920A US40092073A US3890816A US 3890816 A US3890816 A US 3890816A US 400920 A US400920 A US 400920A US 40092073 A US40092073 A US 40092073A US 3890816 A US3890816 A US 3890816A
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Prior art keywords
carbide
alloy
powder
segregation
carbides
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US400920A
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Robert E Allen
Jon L Bartos
Peter Aldred
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General Electric Co
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General Electric Co
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Priority to US400920A priority Critical patent/US3890816A/en
Priority to CA207,658A priority patent/CA1088784A/en
Priority to IT27583/74A priority patent/IT1022211B/it
Priority to DE2445462A priority patent/DE2445462C3/de
Priority to GB4171174A priority patent/GB1452660A/en
Priority to JP10962374A priority patent/JPS572121B2/ja
Priority to FR7432403A priority patent/FR2244827B1/fr
Priority to BE148914A priority patent/BE820362A/xx
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Publication of US3890816A publication Critical patent/US3890816A/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides

Definitions

  • BACKGROUND OF THE INVENTION from atomized powder may exhibit preferential positioning of carbides in a definite spatial array.
  • the morphology of this array suggests that the carbide particles are located in the consolidated solid on interfaces which were external surfaces of the powder prior to compaction.
  • Carbide segregation to prior particle boundaries generally is undesirable because it reducesworkability and mechanical properties. For example, in extrusions such segregations are aligned in the extrusion direction resulting in serious impairment of transverse properties.
  • longitudinal properties of a powder metallurgical compact for example of a nickel-base superalloy
  • transverse strength properties, particularly ductility have been found to be very low.
  • the transverse ductility at 1400F as measured by percent elongation was only 1% while longitudinal elongation was 16%, although both the ultimate tensile and the yield strengths were substantially the same in both directions.
  • Another object is to provide an improved article having a structure including essentially carbides of the MC-type, predominantly in the size range of about 0.2 to about 1 micron, and further characterized by the absence of M C carbide and the absence of carbide segalloy powder of appropriate size for use in powder metallurigical techniques and comprising 0.03 to less than 0.3 weight C, no more than about 3.6 atomic of the m,-,C carbide formers Mo and W, and at least about 0.3 at. of the strong MC carbide formers Cb, Ta, Hf and metallurgical
  • the alloy powder is further characterized by the substantial absence of M C carbide.
  • the powder consists essentially of, by M38% Al, 2-8% Ti, 430% Cr; 0.03 ,to less than 0.3% C, at least one of the elements Mo and W with Mo, when selected, being up to 6% and W, when selected, being up to 12% (provided no more than 3.6 at. of the two are present), up to 10% Ta, up to 10% Cb, up to 8% Hf, up to 5% V, up to 1% Zr, up to 1% B, up to 30% Co, with the balance essentially Ni and incidental impurities.
  • One form of the article provided by the present invention includes the, alloy powder composition and is characterized by the absence of carbide segregation to prior particle boundaries, the substantial absence of M C carbide and the carbide which is present being predominantly MC-type carbide in the 0.2-1 micron size range.
  • FIG. 1 is a photomicrograph at magnification of an alloy displaying carbide segregation to prior particle boundaries
  • FIG. 2 is a photomicrograph at 100 magnification of an alloy displaying no carbide segregation to prior particle boundaries.
  • This invention recognizes that control of and coordipowder'by inert gas atomization.
  • the powder was then sized for use in making test specimens by screening to -60 +325 mesh size.
  • the powder was placed in deformable containers, in this case.
  • metal containers of nation between the amounts of the groups of elements 5 stainless steel, which were evacuated to about 1015 which tend to form, respectively, the desirable and the microns pressure prior to their being sealed.
  • the billets undesirable types of carbides can provide an improved were then extruded to square bars in the temperature article made with a pow y a m h hi h avoids range of about 1850-2250F.
  • the alloy mcludes l5 lations of the volume percent of carbides and atomic at least about 0.3 at. of eleme Selected from Ch, percent of critical elements included in the alloy com- T a Whlch are the strfmg formers of the position.
  • Table 11 presents certain of sirable and stable MC type carbide.
  • the powder metalthese data, lurgy consohdated article which results from use of th1s controlled type of nickel-base alloy powder is charac- 20 TABLE II terized by a structure which has substantially no M C carbide, the balance of the carbide being essentially carbides MC in the size range of about 0.2 to about 1 micron, b Ta with no carbide segregation to prior particle bound- (Vol- Hf w aries, and any small amounts of M C carbide being in- 25 Alloy MGC Mzac MC (at sufficient to result in such carbide segregation.
  • the only other phase in the Ni 2 8 8 -i matrix in addition to borides and carbides is gamma 2 0 0 prime because the composition is controlled to elimi- 7 0 0 1.7 1.2 3.4 nate tendency to form such phases as eta, mu, sigma, 30 :3 8 g v 16 0 0 018 115 3.4
  • a 17 0 8 -3 large number of alloys were prepared in powder form $3 8 0 8 1:2 and consolidated into shapes for further evaluation. 23 0 0 1.5 2.8 3.3
  • Table I gives the composition of some of 35 g; g 8 ⁇ 2 8-2 13 these alloys.
  • Table 11 has been divided into three groupings of alloys depending on their tendency for carbide segregation to prior particle boundaries.
  • Group I lists alloys the structure of which. includes neither M C nor M C carbides but only MC carbide. Of these alloys in Group 1, none showed carbide segregration to prior particle boundaries.
  • Alloy E is a commercially available nickel-base superalloy used for manufacture of wrought products but not, prior to the present invention, for use in powder metallurgical compaction. It should be noted that the elements Mo and W, which tend to result in the formation of M C carbide, are maintained within the range of the present invention of a maximum of 3.6 'at. In addition, the strong MC forrn-ers "of Cb, Ta, l-lf and Zr are included within the range of the present invention of at least about 0.3 at.
  • alloys of Group 11 all were found to have carbidesegregation in prior particle boundaries. All of such Group 11 alloys, except for Alley 21, which will he discussed later, included M C carbide within their structure. Except for Alloy 21, the absence of the above-listed strong MC carbide formers should be noted. Alloys A, B, C and D all are commercially available nickel-base superalloys. Alloy 21 is included in Group II of Table I] as an alloy having a tendency toward carbide segregation to prior particle boundaries because of its 0.3 wt. carbon content. It
  • the present invention is defined as including an alloy having less than 0.3
  • the lower limit for C has been defined as about 0.03 wt. because alloys including less than that amount have insufficient C to form carbides which would create such segregation problems.
  • any presence of the M C -type carbide is detrimenml to the present invention. It has been found that the complete absence of M C-type carbide is not quite as critical. Depending on the composition of the alloy, small amounts of M C-type carbide can be tolerated. Typical examples of alloys which can or cannot tolerate M C-type carbide in respect to the tendency to carbide segregation in prior particle boundaries are shown in Group III of Table 11. Evaluation has shown that Alloy 4 does not show such carbide segregation in prior particle boundaries whereas Alloys l0, l2 and 15 do result in such detrimental carbide segregation. Therefore, the present invention defines the alloy as including a total content of no more than 3.6 at. of the sum of Mo and W to limit the formation of M C-type carbide and thus further limit the tendency of the alloy to carbide segregation in prior particle boundaries.
  • the volume percent ofcarb ides were cal- Mo and W are greater than or equal to 3.5 at. the excess above that amount forms M C; if the, sum of Cb, Ta, Hf and Zr are greater than or equal to 0.3 at. the carbon forms MC; and if the sum of Cb, Ta, Hf and Zr is less than 0.3 at. half of C forms M C and half forms MC.
  • the present invention involves an alloy having a controlled and coordinated composition for a number of reasons, an important one of which is the avoidance of carbide segregation to prior particle boundaries.
  • other elements in the composition are limited for a variety of reasons:
  • Al which is preferably included within the range of 3-7 wt. is limited to no more than about 8% because greater than that amount would lead to too much gamma prime or to a eutectic formation.
  • Ti is preferably included within the range of 2-6 wt. but should not exceed about 8 wt. %'because of the formation of too much gamma prime and the formation of eta phase.
  • Cr if included in amounts greater than 30 wt. leads to the formation of sigma phase whereas lessthan about 4 wt. results in corrosion problems.
  • the preferred range for Cr is 4-17 wt.
  • the elementsMo and W which provide an alloy with a tendency toward the formation of the less desirable M C carbide, are included in a total of no more than about 3.6 at.
  • individually Mo should not exceed about 6.2 wt. and W should not exceed about Both Ta and Cb in excessive amounts canlead to eta phase formation.
  • excessive Cb results in too much gamma prime for fabrication. Therefore, each of Ta and Cb should be limited to no more than about 10 wt.
  • l-lf can have a significant effect on the incipient melting point of an alloy. Therefore, no more'than about 8 wt. Hf should be included in the alloy.
  • the element V is a carbide former and should be limited to no more than about 5 wt.
  • Co which has been widely described in the literature, generally is included for formability. It should not be included in amounts greater than about 30 wt.
  • Each of the elements Zr and B are included in amounts up to about 1% each. An excess of that amount will tend to lower the incipient melting point of the alloy.
  • one form of the alloy involved with the present invention in its broad range consists essentially of, by weight, 38% A], 28% Ti, 430% Cr, 0.03 to less than 0.3% C, up to 6% Mo, up to 12% W, up to 10% each ofTa and Cb, up to 8% l-lf, up to 5% V, up to 1% each of Zr and B, up to 30% Co with the balance'nickel and incidental impurities with the further condition that the sum of the elements Mo and W be no more than about 3.6 at. and that there be included at least about 0.3 at. elements selected from Cb, Ta, Hf and Zr.
  • A 38% A
  • Ti 430% Cr, 0.03 to less than 0.3% C
  • up to 6% Mo up to 12%
  • W up to 10% each ofTa and Cb
  • up to 8% l-lf up to 5%
  • Zr and B up to 30% Co with the further condition that the sum of the elements Mo and W be no more than about 3.6 at. and that there be
  • 7 more preferred range of such alloy is 3-7% Al, 2-6% Ti, 4-l7% Cr, 0.05-0.2% C, up to 6% Mo, up to 9% W, up to 6% Ta, up to 4% Cb, up to l-lf, up to 3% V, up to 0.1% each of Zr and B, 5-20% Co with the balance essentially nickel and incidental impurities.
  • the method associated with the present invention for making a nickel-base alloy article by powder metallurgy consolidation includes the steps of enclosing the powder in a deformable container, such as a metal, which is then evacuated prior to working into an article shape.
  • a deformable container such as a metal
  • the term article is intended'to include within its meaning rods, bars, billets, etc.,as well as more finished article shapes such as gas turbine wheels, blading members, etc.
  • the article which results can be distinguished from articles manufactured by conventional non-powder metallurgical techniques by the size of the carbides in the microstructure.
  • the article which results from the present invention has carbides which exist predominantly in the size range of about 0.2 to about 1 micron.
  • conventional practice such as forging from a cast billet, generally results in the generation of carbides predominantly at least about 5 microns or larger in size.
  • FIGS. 1 and 2 A comparison of consolidated alloy specimens which display carbide segregation to prior particle boundaries and those which do not are shown in FIGS. 1 and 2.
  • FIG. 1 is a photomicrograph at 100 magnifications of Alloy D displaying the circular evidence of carbide segregation to prior particle boundaries after having been processed by hot isostatic pressing at 2175F and 15,000 psi.
  • FIG. 2 is a photomicrograph at 100 magnifications showing Alloy E displaying no carbide segregation to prior particle boundaries after having been processed under the same conditions. Only the irregularly shaped grains are seen.
  • a nickel-base alloy powder sized for use in making an article by powder metallurgical techniques, consisting essentially of:
  • the alloy being characterized by the substantial absence of M C carbide, the balance of the carbide being predominantly MC-type.
  • the carbides being predominantly in the size range of about 0.2-1 micron.
  • the alloy powder of claim 2 consisting essentially of, by weight, 37% Al; 2-6% Ti; 4-1 7% Cr; 0.05-0.2% C; Mo, when selected, up to 6%; W, when selected, up
  • alloy powder of claim 4 in which A1 is 3-5%; Ti is 3.5-5.5%; Cr is 7-l1%; C is 0.l50.2%, M0 is 2-3%; W is 57%; Ta is up to 4%; Cb is up to 2.5%; l-lf is up to 2%; B is 0.01-0.05% and Co is l0-l6%.
  • the V is up to 7%, the V is up to 1. 5%; the Zr is 0. 01-0. 1%; the Bis 0. 01-0. 1%

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
US400920A 1973-09-26 1973-09-26 Elimination of carbide segregation to prior particle boundaries Expired - Lifetime US3890816A (en)

Priority Applications (8)

Application Number Priority Date Filing Date Title
US400920A US3890816A (en) 1973-09-26 1973-09-26 Elimination of carbide segregation to prior particle boundaries
CA207,658A CA1088784A (en) 1973-09-26 1974-08-23 Elimination of carbide segregation to prior particle boundaries
IT27583/74A IT1022211B (it) 1973-09-26 1974-09-23 Eliminazione della segregazione di carburi in leghe a base di michel
DE2445462A DE2445462C3 (de) 1973-09-26 1974-09-24 Verwendung einer Nickellegierung
GB4171174A GB1452660A (en) 1973-09-26 1974-09-25 Nickel-base alloys
JP10962374A JPS572121B2 (enrdf_load_stackoverflow) 1973-09-26 1974-09-25
FR7432403A FR2244827B1 (enrdf_load_stackoverflow) 1973-09-26 1974-09-26
BE148914A BE820362A (fr) 1973-09-26 1974-09-26 Poudre d'alliage a base de nickel et produit obtenu

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JP (1) JPS572121B2 (enrdf_load_stackoverflow)
BE (1) BE820362A (enrdf_load_stackoverflow)
CA (1) CA1088784A (enrdf_load_stackoverflow)
DE (1) DE2445462C3 (enrdf_load_stackoverflow)
FR (1) FR2244827B1 (enrdf_load_stackoverflow)
GB (1) GB1452660A (enrdf_load_stackoverflow)
IT (1) IT1022211B (enrdf_load_stackoverflow)

Cited By (33)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4030946A (en) * 1976-04-13 1977-06-21 Carpenter Technology Corporation Eliminating prior particle boundary delineation
US4629521A (en) * 1984-12-10 1986-12-16 Special Metals Corporation Nickel base alloy
US4957567A (en) * 1988-12-13 1990-09-18 General Electric Company Fatigue crack growth resistant nickel-base article and alloy and method for making
US5108700A (en) * 1989-08-21 1992-04-28 Martin Marietta Energy Systems, Inc. Castable nickel aluminide alloys for structural applications
US5294239A (en) * 1990-05-07 1994-03-15 Pm Hochtemperatur-Metall Gmbh Nickel-base superalloy
US5413752A (en) * 1992-10-07 1995-05-09 General Electric Company Method for making fatigue crack growth-resistant nickel-base article
DE19525983A1 (de) * 1994-07-19 1996-02-01 Hitachi Metals Ltd Hochhitzebeständige Nickelbasislegierung und Verfahren zu ihrer Herstellung
US5808281A (en) * 1991-04-05 1998-09-15 The Boeing Company Multilayer susceptors for achieving thermal uniformity in induction processing of organic matrix composites or metals
US6632299B1 (en) 2000-09-15 2003-10-14 Cannon-Muskegon Corporation Nickel-base superalloy for high temperature, high strain application
US20040050158A1 (en) * 2002-09-18 2004-03-18 Webb R. Michael Liquid level sensing gauge assembly and method of installation
US20040076540A1 (en) * 2002-10-16 2004-04-22 Shinya Imano Welding material, gas turbine blade or nozzle and a method of repairing a gas turbine blade or nozzle
US20050120941A1 (en) * 2003-12-04 2005-06-09 Yiping Hu Methods for repair of single crystal superalloys by laser welding and products thereof
US20050167010A1 (en) * 2002-05-15 2005-08-04 Kabushiki Kaisha Toshiba Ni-cr alloy cutting tool
US20100008790A1 (en) * 2005-03-30 2010-01-14 United Technologies Corporation Superalloy compositions, articles, and methods of manufacture
US20100303666A1 (en) * 2009-05-29 2010-12-02 General Electric Company Nickel-base superalloys and components formed thereof
US20100303665A1 (en) * 2009-05-29 2010-12-02 General Electric Company Nickel-base superalloys and components formed thereof
US20100329876A1 (en) * 2009-06-30 2010-12-30 General Electric Company Nickel-base superalloys and components formed thereof
US20100329883A1 (en) * 2009-06-30 2010-12-30 General Electric Company Method of controlling and refining final grain size in supersolvus heat treated nickel-base superalloys
US20110165012A1 (en) * 2009-07-29 2011-07-07 Marco Innocenti Nickel-based superalloy, mechanical component made of the above mentioned super alloy, piece of turbomachinery which includes the above mentioned component and related methods
CN102444428A (zh) * 2010-08-31 2012-05-09 通用电气公司 粉末压块转子锻造预制件和锻造涡轮转子及其制造方法
US8961646B2 (en) 2010-11-10 2015-02-24 Honda Motor Co., Ltd. Nickel alloy
US9828658B2 (en) 2013-08-13 2017-11-28 Rolls-Royce Corporation Composite niobium-bearing superalloys
US20180002785A1 (en) * 2016-06-30 2018-01-04 General Electric Company Article and additive manufacturing method for making
CN107755668A (zh) * 2017-09-20 2018-03-06 上海交通大学 制备增强镍基高温合金复合材料单晶叶片的方法
US9938610B2 (en) 2013-09-20 2018-04-10 Rolls-Royce Corporation High temperature niobium-bearing superalloys
CN108845098A (zh) * 2013-05-21 2018-11-20 麻省理工学院 稳定的纳米晶有序合金体系及其鉴定方法
US10415121B2 (en) * 2016-08-05 2019-09-17 Onesubsea Ip Uk Limited Nickel alloy compositions for aggressive environments
US10577679B1 (en) 2018-12-04 2020-03-03 General Electric Company Gamma prime strengthened nickel superalloy for additive manufacturing
DE102018251722A1 (de) * 2018-12-27 2020-07-02 Siemens Aktiengesellschaft Nickelbasislegierung für additive Fertigung und Verfahren
CN112513301A (zh) * 2018-07-31 2021-03-16 赛峰集团 通过粉末成型制造零件的镍基超合金
EP3862448A1 (en) * 2020-02-07 2021-08-11 General Electric Company Nickel-based superalloys
US11650193B2 (en) 2012-03-12 2023-05-16 Massachusetts Institute Of Technology Stable binary nanocrystalline alloys and methods of identifying same
EP4357471A1 (en) * 2022-10-20 2024-04-24 Höganäs Germany GmbH Nickel-chrome alloys

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US4207098A (en) 1978-01-09 1980-06-10 The International Nickel Co., Inc. Nickel-base superalloys
JP3067416B2 (ja) * 1992-08-20 2000-07-17 三菱マテリアル株式会社 高温耐熱部品製造用Ｎｉ基合金粉末
WO2012047352A2 (en) * 2010-07-09 2012-04-12 General Electric Company Nickel-base alloy, processing therefor, and components formed thereof
US9573192B2 (en) * 2013-09-25 2017-02-21 Honeywell International Inc. Powder mixtures containing uniform dispersions of ceramic particles in superalloy particles and related methods
JP6850223B2 (ja) * 2017-08-30 2021-03-31 山陽特殊製鋼株式会社 積層造形用Ｎｉ基超合金粉末
JP7128916B2 (ja) * 2021-01-15 2022-08-31 山陽特殊製鋼株式会社 積層造形体

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Cited By (52)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4030946A (en) * 1976-04-13 1977-06-21 Carpenter Technology Corporation Eliminating prior particle boundary delineation
US4629521A (en) * 1984-12-10 1986-12-16 Special Metals Corporation Nickel base alloy
AU574538B2 (en) * 1984-12-10 1988-07-07 Societe National D'etude Et De Construction De Moteurs D'aviation Nickel & chromium base mo,w,co,al,ti,b,zr alloy
US4957567A (en) * 1988-12-13 1990-09-18 General Electric Company Fatigue crack growth resistant nickel-base article and alloy and method for making
US5108700A (en) * 1989-08-21 1992-04-28 Martin Marietta Energy Systems, Inc. Castable nickel aluminide alloys for structural applications
US5294239A (en) * 1990-05-07 1994-03-15 Pm Hochtemperatur-Metall Gmbh Nickel-base superalloy
US5808281A (en) * 1991-04-05 1998-09-15 The Boeing Company Multilayer susceptors for achieving thermal uniformity in induction processing of organic matrix composites or metals
US5413752A (en) * 1992-10-07 1995-05-09 General Electric Company Method for making fatigue crack growth-resistant nickel-base article
DE19525983A1 (de) * 1994-07-19 1996-02-01 Hitachi Metals Ltd Hochhitzebeständige Nickelbasislegierung und Verfahren zu ihrer Herstellung
US6632299B1 (en) 2000-09-15 2003-10-14 Cannon-Muskegon Corporation Nickel-base superalloy for high temperature, high strain application
US20080302449A1 (en) * 2002-05-15 2008-12-11 Kabushiki Kaisha Toshiba Cutter composed of ni-cr alloy
US7740719B2 (en) * 2002-05-15 2010-06-22 Kabushiki Kaisha Toshiba Cutter composed of Ni-Cr alloy
US20050167010A1 (en) * 2002-05-15 2005-08-04 Kabushiki Kaisha Toshiba Ni-cr alloy cutting tool
US7682474B2 (en) 2002-05-15 2010-03-23 Kabushiki Kaisha Toshiba Cutter composed of Ni-Cr-Al Alloy
US20040050158A1 (en) * 2002-09-18 2004-03-18 Webb R. Michael Liquid level sensing gauge assembly and method of installation
US7165325B2 (en) * 2002-10-16 2007-01-23 Hitachi, Ltd. Welding material, gas turbine blade or nozzle and a method of repairing a gas turbine blade or nozzle
US20070054147A1 (en) * 2002-10-16 2007-03-08 Shinya Imano Welding material, gas turbine blade or nozzle and a method of repairing a gas turbine blade or nozzle
US20040076540A1 (en) * 2002-10-16 2004-04-22 Shinya Imano Welding material, gas turbine blade or nozzle and a method of repairing a gas turbine blade or nozzle
US7250081B2 (en) 2003-12-04 2007-07-31 Honeywell International, Inc. Methods for repair of single crystal superalloys by laser welding and products thereof
US20050120941A1 (en) * 2003-12-04 2005-06-09 Yiping Hu Methods for repair of single crystal superalloys by laser welding and products thereof
US20100008790A1 (en) * 2005-03-30 2010-01-14 United Technologies Corporation Superalloy compositions, articles, and methods of manufacture
US20100158695A1 (en) * 2005-03-30 2010-06-24 United Technologies Corporation Superalloy Compositions, Articles, and Methods of Manufacture
US8147749B2 (en) 2005-03-30 2012-04-03 United Technologies Corporation Superalloy compositions, articles, and methods of manufacture
US8992700B2 (en) 2009-05-29 2015-03-31 General Electric Company Nickel-base superalloys and components formed thereof
US20100303666A1 (en) * 2009-05-29 2010-12-02 General Electric Company Nickel-base superalloys and components formed thereof
US20100303665A1 (en) * 2009-05-29 2010-12-02 General Electric Company Nickel-base superalloys and components formed thereof
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DE2445462B2 (de) 1979-04-12
BE820362A (fr) 1975-01-16
DE2445462C3 (de) 1979-12-06
GB1452660A (en) 1976-10-13
JPS572121B2 (enrdf_load_stackoverflow) 1982-01-14
CA1088784A (en) 1980-11-04
JPS5077203A (enrdf_load_stackoverflow) 1975-06-24
DE2445462A1 (de) 1975-03-27
IT1022211B (it) 1978-03-20
FR2244827B1 (enrdf_load_stackoverflow) 1978-10-13
FR2244827A1 (enrdf_load_stackoverflow) 1975-04-18

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