EP2218798B1 - Lower cost high strength single crystal superalloys with reduced Re and Ru content - Google Patents

Lower cost high strength single crystal superalloys with reduced Re and Ru content Download PDF

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EP2218798B1
EP2218798B1 EP09252708.4A EP09252708A EP2218798B1 EP 2218798 B1 EP2218798 B1 EP 2218798B1 EP 09252708 A EP09252708 A EP 09252708A EP 2218798 B1 EP2218798 B1 EP 2218798B1
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alloy
alloys
single crystal
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pwa
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EP2218798A2 (en
EP2218798A3 (en
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Alan D. Cetel
Dilip M. Shah
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RTX Corp
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United Technologies Corp
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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
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%

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  • All second and higher generation nickel-base directionally solidified and single crystal superalloy compositions contain additions of rhenium of at least 3 wt% (for example see EP 1571297 and EP 1057899 ).
  • Fourth generation and higher single crystal alloys contain some percentage of the element ruthenium.
  • Nickel-base superalloy single crystals are primarily used for high temperature turbine components, such as blades and vanes, where temperature capability is typically assessed by its high temperature creep resistance. Simplistically, it is well understood that to improve creep resistance, additions of refractory elements with high melting point is desirable.
  • Such elements include almost all Group IVA to VIIIA transition metals, especially Ti, Nb, Ta, Mo, W, Re, and Ru with melting points in excess of 4082°F (2250°C).
  • Ti, Nb, and Ta are known to almost exclusively replace Al in the ordered precipitate phase ⁇ '(Ni 3 Al), whereas Re and Ru are known to exclusively partition to the nickel base solid solution ⁇ -matrix.
  • W is known to partition evenly between the ⁇ -matrix and ⁇ ' phase.
  • the concentration at which such phases will form can be approximately predicted by calculating, what is called an electron vacancy number or Nv number for the ⁇ -matrix. This calculation is based on a weighed average of Nv assigned to each element. It is an industry wide practice to use such calculations, but it is known that it is not completely accurate and there are exceptions to the rule.
  • the present invention can be seen to provide a lower cost high strength nickel based alloy that consists of 3.0 to 5.2 wt% chromium, from 1.5 to 3.0 wt% molybdenum, from 6.0 to 12.5 wt% tungsten, from 5.0 to 11 wt% tantalum, from 5.5 to 6.5 wt% aluminum, from 11 to 14 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium, up to 3.0 wt% ruthenium, and the balance nickel and unavoidable impurities.
  • the best known equiaxed and columnar grain alloys were based on Mar M200, which contain 12.5 weight% of W. Also the alloy contained 2.0 weight % Ti. Development of PWA 1480 was marked by the addition of 12 weight% Ta. Subsequent development of second generation single crystal alloys such as PWA 1484 all had a marked absence of Ti. An improved second generation DS alloy, PWA 1426, was developed with Re additions similar to PWA 1484.
  • the fourth generation of single crystal alloys such as PWA 1497 have an increase in Re concentration concurrent with Ru additions. As can be seen in Fig. 1 , these alloys do not overlap in the Ta, W, (Re + Ru) space. In these higher strength alloys, the concentration of Ta never decreased below 4 wt% and W never increased beyond 6.0 wt%.
  • FIGS. 1 and 2 Useful alloys are listed in Table I and are also depicted in FIGS. 1 and 2 .
  • Fig. 1 clearly depicts that in Ta weight % vs. W weight % plots, current production alloys are outside the alloy space.
  • the Ta in production alloys is showed by the diamond points 10 on FIG. 1 and the space with the Ta in the alloys set forth herein are shown by the squares in the space 12.
  • the same information is plotted in FIG. 2 as a bubble chart, where the size of plotting points is proportional to the concentration of (Re + Ru).
  • FIG. 1 clearly depicts that in Ta weight % vs. W weight % plots, current production alloys are outside the alloy space.
  • the Ta in production alloys is showed by the diamond points 10 on FIG. 1 and the space with the Ta in the alloys set forth herein are shown by the squares in the space 12.
  • the same information is plotted in FIG. 2 as a bubble chart, where the size of plotting points is proportional to the
  • bubble 20 is alloy PWA 1422
  • bubble 22 is alloy PWA 1480
  • bubble 24 is alloy PWA 1497
  • bubble 26 is alloy PWA 1484
  • bubble 28 is alloy 2a in Table I
  • bubble 30 is alloy 2b in Table I
  • bubble 32 is alloy 1a in Table I
  • bubble 34 is alloy 1b in Table I
  • bubble 36 is alloy 3a in Table I
  • bubble 38 is alloy 3b in Table I
  • bubble 40 is alloy 3c in Table I
  • bubble 42 is alloy PWA 1426
  • bubble 44 is alloy PWA 1426a
  • bubble 46 is alloy PWA 1426b.
  • Table I Listed in Table I are baseline compositions of the second and fourth generation single crystal alloys PWA 1484 and PWA 1497, respectively, and the second generation columnar grain (DS) alloy PWA 1426. It can be seen from FIG. 2 that using the useful alloys described herein, one can achieve the same level of creep resistance as PWA 1426, for reducing Re-containing alloys (PWA 1426a and PWA 1426b), by increasing the W content of these alloys.
  • One embodiment of a useful alloy contains from 3.0 to 5.2 wt% chromium, from 1.5 to 3.0 wt% molybdenum, from 6.0 to 12.5 wt% tungsten, from 5.0 to 11 wt% tantalum, from 5.5 to 6.5 wt% aluminum, from 11 to 14 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium, and the balance nickel.
  • Table II is a comparison of alloys having compositions within the aforesaid range with Rene N5.
  • the data shows the alloys described herein to have higher density, an equivalent or better life, better yield strength, and equivalent or better ultimate tensile strength than Rene N5.
  • a second embodiment of a useful alloy contains from 4.0 to 5.0 wt% chromium, from 1.7 to 2.3 wt% molybdenum, from 7.0 to 12.5 wt% tungsten, from 5.5 to 10 wt% tantalum, from 5.6 to 6.25 wt% aluminum, from 11.5 to 13.5 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.4 wt% hafnium, from 0.001 to 0.01 wt% yttrium, and the balance nickel.
  • a third embodiment of a useful alloy contains from 1.0 to 3.0 wt% chromium, up to 2.5 wt% molybdenum, from 11 to 16 wt% tungsten, from 4.0 to 8.0 tantalum, from 5.7 to 6.5 wt% aluminum, from 11 to 15 wt% cobalt, from 2.0 to 4.0 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium and the balance nickel.
  • a fourth embodiment of a useful alloy contains from 1.5 to 2.5 wt% chromium, from 0.5 to 1.5 wt% molybdenum, from 11.5 to 13.5 wt% tungsten, from 5.0 to 7.0 tantalum, from 5.8 to 6.25 wt% aluminum, from 11.5 to 13.5 wt% cobalt, from 2.5 to 3.5 wt% rhenium, from 0.2 to 0.4 wt% hafnium, from 0.001 to 0.01 wt% yttrium, and the balance nickel.
  • the above alloys may contain up to 3.0 wt% ruthenium.
  • the total rhenium and ruthenium content of each of the alloys may be no greater than 6.0 wt%.
  • Oxidation resistance can be maintained by the addition of at least 15 - 30 ppm yttrium or other equivalent active elements such as Ca, Mg, and other rare earth elements.
  • yttrium and other rare earth additions have not been added to alloys containing elevated levels of W, i.e. greater than 6.0 weight%.
  • the alloys described herein can fulfill the low cost requirements. Since Re and Ru raw material prices have risen in the last few years, reducing their concentration in new alloys by 50% or more (compared to existing second generation and higher alloys) will have a significant effect on master heat cost.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)

Description

  • Lower cost high strength single crystal superalloys with reduced rhenium and ruthenium content are described.
  • All second and higher generation nickel-base directionally solidified and single crystal superalloy compositions contain additions of rhenium of at least 3 wt% (for example see EP 1571297 and EP 1057899 ). Fourth generation and higher single crystal alloys contain some percentage of the element ruthenium. With the significant escalation of spot prices of these elements, there is an economic need for alternate alloy compositions with comparable levels of performance, but with reduced concentration of these expensive elements.
  • Nickel-base superalloy single crystals are primarily used for high temperature turbine components, such as blades and vanes, where temperature capability is typically assessed by its high temperature creep resistance. Simplistically, it is well understood that to improve creep resistance, additions of refractory elements with high melting point is desirable. Such elements include almost all Group IVA to VIIIA transition metals, especially Ti, Nb, Ta, Mo, W, Re, and Ru with melting points in excess of 4082°F (2250°C). Among these elements, Ti, Nb, and Ta are known to almost exclusively replace Al in the ordered precipitate phase γ'(Ni3Al), whereas Re and Ru are known to exclusively partition to the nickel base solid solution γ-matrix. W on the other hand is known to partition evenly between the γ-matrix and γ' phase.
  • There are of course limits to the extent to which these elements can be accommodated in the alloy. It is common knowledge that optimum mechanical properties are obtained when the volume fraction of the γ' phase is around 60 to 70%. Thus, individually or combined (Al + Nb + Ta + W/2) in atom % cannot exceed about 18%. Moreover, Al concentrations cannot be reduced below 10 atom% to preserve oxidation resistance. Similarly excessive addition of refractory elements in the γ-matrix is limited by the undesirable phases these elements can form after a long time exposure. The formation of so-called topologically closed packed (TCP) phases are undesirable as they reduce the creep resistance of the alloy. The concentration at which such phases will form can be approximately predicted by calculating, what is called an electron vacancy number or Nv number for the γ-matrix. This calculation is based on a weighed average of Nv assigned to each element. It is an industry wide practice to use such calculations, but it is known that it is not completely accurate and there are exceptions to the rule.
  • There is a need for a lower cost high strength nickel based superalloy.
  • Thus, the present invention can be seen to provide a lower cost high strength nickel based alloy that consists of 3.0 to 5.2 wt% chromium, from 1.5 to 3.0 wt% molybdenum, from 6.0 to 12.5 wt% tungsten, from 5.0 to 11 wt% tantalum, from 5.5 to 6.5 wt% aluminum, from 11 to 14 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium, up to 3.0 wt% ruthenium, and the balance nickel and unavoidable impurities.
  • Certain preferred embodiments of the lower cost high strength nickel based superalloys of the present invention will now be described in greater detail and by way of example only and with reference to the accompanying drawings, in which:
    • FIG. 1 is a plot of tantalum weight % vs. tungsten weight %; and
    • FIG. 2 is a bubble chart of Ta weight% vs. tungsten weight% with the bubble size proportional to (Re + Ru) weight %.
  • The combinations of compositions with the elements Ti, Nb, Ta, Mo, W, Re, and Ru along with primary elements Ni, Co, Cr, and Al, is so large that it is cost prohibitive to explore the entire alloy space. Traditionally, alloys are evolved based on prior experience and once the target performance benefit is realized, there is little motivation to visit the unexplored alloy compositional space. There is no simple quantitative way to map out a space bounded by a dozen elements and pinpoint the gaps. In a limited sense, a bubble plot of Ta weight % vs. W weight %, as shown in Figure 1, graphically represents maps out a desirable space. In this plot, the size of the bubble or plotting point for each alloy is proportional to the total concentration of (Re + Ru) in the alloys of interest.
  • Prior to the development of the first generation single crystal alloy PWA 1480, the best known equiaxed and columnar grain alloys were based on Mar M200, which contain 12.5 weight% of W. Also the alloy contained 2.0 weight % Ti. Development of PWA 1480 was marked by the addition of 12 weight% Ta. Subsequent development of second generation single crystal alloys such as PWA 1484 all had a marked absence of Ti. An improved second generation DS alloy, PWA 1426, was developed with Re additions similar to PWA 1484. The fourth generation of single crystal alloys such as PWA 1497 have an increase in Re concentration concurrent with Ru additions. As can be seen in Fig. 1, these alloys do not overlap in the Ta, W, (Re + Ru) space. In these higher strength alloys, the concentration of Ta never decreased below 4 wt% and W never increased beyond 6.0 wt%.
  • The successful development of second generation single crystal alloys has been attributed to Re additions and it is generally believed that Re makes the lattice misfit between the γ' precipitate and the γ-matrix become more negative. Re is also thought to reduce the coarsening rate of the γ' phase, contributing to improving creep strength.
  • Useful alloys are listed in Table I and are also depicted in FIGS. 1 and 2. Fig. 1 clearly depicts that in Ta weight % vs. W weight % plots, current production alloys are outside the alloy space. The Ta in production alloys is showed by the diamond points 10 on FIG. 1 and the space with the Ta in the alloys set forth herein are shown by the squares in the space 12. The same information is plotted in FIG. 2 as a bubble chart, where the size of plotting points is proportional to the concentration of (Re + Ru). In FIG. 2, bubble 20 is alloy PWA 1422, bubble 22 is alloy PWA 1480, bubble 24 is alloy PWA 1497, bubble 26 is alloy PWA 1484, bubble 28 is alloy 2a in Table I, bubble 30 is alloy 2b in Table I, bubble 32 is alloy 1a in Table I, bubble 34 is alloy 1b in Table I, bubble 36 is alloy 3a in Table I, bubble 38 is alloy 3b in Table I, bubble 40 is alloy 3c in Table I, bubble 42 is alloy PWA 1426; bubble 44 is alloy PWA 1426a, and bubble 46 is alloy PWA 1426b.
    Figure imgb0001
  • Listed in Table I are baseline compositions of the second and fourth generation single crystal alloys PWA 1484 and PWA 1497, respectively, and the second generation columnar grain (DS) alloy PWA 1426. It can be seen from FIG. 2 that using the useful alloys described herein, one can achieve the same level of creep resistance as PWA 1426, for reducing Re-containing alloys (PWA 1426a and PWA 1426b), by increasing the W content of these alloys.
  • One embodiment of a useful alloy contains from 3.0 to 5.2 wt% chromium, from 1.5 to 3.0 wt% molybdenum, from 6.0 to 12.5 wt% tungsten, from 5.0 to 11 wt% tantalum, from 5.5 to 6.5 wt% aluminum, from 11 to 14 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium, and the balance nickel.
  • Table II is a comparison of alloys having compositions within the aforesaid range with Rene N5. The data shows the alloys described herein to have higher density, an equivalent or better life, better yield strength, and equivalent or better ultimate tensile strength than Rene N5.
    Figure imgb0002
  • A second embodiment of a useful alloy contains from 4.0 to 5.0 wt% chromium, from 1.7 to 2.3 wt% molybdenum, from 7.0 to 12.5 wt% tungsten, from 5.5 to 10 wt% tantalum, from 5.6 to 6.25 wt% aluminum, from 11.5 to 13.5 wt% cobalt, from 0.001 to 1.75 wt% rhenium, from 0.2 to 0.4 wt% hafnium, from 0.001 to 0.01 wt% yttrium, and the balance nickel.
  • A third embodiment of a useful alloy contains from 1.0 to 3.0 wt% chromium, up to 2.5 wt% molybdenum, from 11 to 16 wt% tungsten, from 4.0 to 8.0 tantalum, from 5.7 to 6.5 wt% aluminum, from 11 to 15 wt% cobalt, from 2.0 to 4.0 wt% rhenium, from 0.2 to 0.6 wt% hafnium, up to 0.05 wt% yttrium and the balance nickel.
  • A fourth embodiment of a useful alloy contains from 1.5 to 2.5 wt% chromium, from 0.5 to 1.5 wt% molybdenum, from 11.5 to 13.5 wt% tungsten, from 5.0 to 7.0 tantalum, from 5.8 to 6.25 wt% aluminum, from 11.5 to 13.5 wt% cobalt, from 2.5 to 3.5 wt% rhenium, from 0.2 to 0.4 wt% hafnium, from 0.001 to 0.01 wt% yttrium, and the balance nickel.
  • The above alloys may contain up to 3.0 wt% ruthenium. The total rhenium and ruthenium content of each of the alloys may be no greater than 6.0 wt%.
  • Oxidation resistance can be maintained by the addition of at least 15 - 30 ppm yttrium or other equivalent active elements such as Ca, Mg, and other rare earth elements. Previously, yttrium and other rare earth additions have not been added to alloys containing elevated levels of W, i.e. greater than 6.0 weight%.
  • The alloys described herein can fulfill the low cost requirements. Since Re and Ru raw material prices have risen in the last few years, reducing their concentration in new alloys by 50% or more (compared to existing second generation and higher alloys) will have a significant effect on master heat cost.
  • It should be apparent that there has been provided in accordance with the present disclosure lower cost high strength single crystal superalloys with reduced rhenium and ruthenium content. While the superalloys have been described in the context of specific embodiments thereof, other unforeseeable alternatives, variations and modifications make become apparent to those skilled in the art having read the foregoing description. Accordingly, it is intended to embrace those alternatives, modifications, and variations as fall within the broad scope of the appended claims.

Claims (8)

  1. A nickel based alloy consisting of:
    from 3.0 to 5.2 wt% chromium,
    from 1.5 to 3.0 wt% molybdenum,
    from 6.0 to 12.5 wt% tungsten,
    from 5.0 to 11 wt% tantalum,
    from 5.5 to 6.5 wt% aluminum,
    from 11 to 14 wt% cobalt,
    up to 1.75 wt% rhenium,
    from 0.2 to 0.6 wt% hafnium,
    up to 0.05 wt% yttrium,
    up to 3.0 wt% ruthenium, and
    the balance nickel and unavoidable impurities.
  2. The nickel based alloy of claim 1, wherein said chromium is present in an amount from 4.0 to 5.0 wt%.
  3. The nickel based alloy of claim 1 or 2, wherein said molybdenum is present in an amount from 1.7 to 2.3 wt%.
  4. The nickel based alloy of claim 1, 2 or 3, wherein said tungsten is present in an amount from 7.0 to 12 wt%.
  5. The nickel based alloy of any preceding claim, wherein said tantalum is present in an amount from 5.5 to 10 wt%.
  6. The nickel based alloy of any preceding claim, wherein said aluminum is present in an amount from 5.6 to 6.25 wt%.
  7. The nickel based alloy of any preceding claim, wherein said cobalt is present in an amount from 11.5 to 13.5 wt%.
  8. The nickel based alloy of any preceding claim, wherein said rhenium is present in an amount from 0.001 to 1.75 wt%, said hafnium is present in an amount from 0.2 to 0.4 wt%, and said yttrium is present in an amount from 0.001 to 0.01 wt%.
EP09252708.4A 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content Active EP2218798B1 (en)

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US20100254822A1 (en) * 2009-03-24 2010-10-07 Brian Thomas Hazel Super oxidation and cyclic damage resistant nickel-base superalloy and articles formed therefrom
US20110076179A1 (en) * 2009-03-24 2011-03-31 O'hara Kevin Swayne Super oxidation and cyclic damage resistant nickel-base superalloy and articles formed therefrom
US20110076181A1 (en) * 2009-09-30 2011-03-31 General Electric Company Nickel-Based Superalloys and Articles
US20110076180A1 (en) * 2009-09-30 2011-03-31 General Electric Company Nickel-Based Superalloys and Articles
US9850765B2 (en) 2011-12-07 2017-12-26 MTU Aero Engines AG Rhenium-free or rhenium-reduced nickel-base superalloy
US9551049B2 (en) 2012-08-28 2017-01-24 United Technologies Corporation High elastic modulus shafts and method of manufacture
ES2625825T3 (en) * 2012-10-26 2017-07-20 MTU Aero Engines AG Super-alloy with rhenium-free and creep-resistant nickel
US8858876B2 (en) 2012-10-31 2014-10-14 General Electric Company Nickel-based superalloy and articles
WO2015183955A2 (en) 2014-05-27 2015-12-03 Questek Innovations Llc Highly processable single crystal nickel alloys
EP3091095B1 (en) 2015-05-05 2018-07-11 MTU Aero Engines GmbH Low density rhenium-free nickel base superalloy

Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4169742A (en) 1976-12-16 1979-10-02 General Electric Company Cast nickel-base alloy article
EP0150917A2 (en) 1984-01-10 1985-08-07 AlliedSignal Inc. Single crystal nickel-base alloy
EP0362661A1 (en) 1988-10-03 1990-04-11 General Electric Company Cast columnar grain hollow nickel base alloy article and alloy and heat treatment for making
US4935072A (en) 1986-05-13 1990-06-19 Allied-Signal, Inc. Phase stable single crystal materials
EP1057899A2 (en) 1999-05-26 2000-12-06 General Electric Company Compositions and single-crystal articles of hafnium-modified and/or zirconium-modified nickel-base superalloys
EP1184473A2 (en) 2000-08-30 2002-03-06 Kabushiki Kaisha Toshiba Nickel-base single-crystal superalloys, method of manufacturing same and gas turbine high temperature parts made thereof
US6419763B1 (en) 1999-05-20 2002-07-16 Alstom (Switzerland) Ltd Nickel-base superalloy
US20030041930A1 (en) 2001-08-30 2003-03-06 Deluca Daniel P. Modified advanced high strength single crystal superalloy composition
US20030075247A1 (en) 2001-05-30 2003-04-24 Yutaka Koizumi Ni-based single crystal super alloy
US20040229072A1 (en) 2002-12-16 2004-11-18 Murphy Kenneth S. Nickel base superalloy
EP1571297A2 (en) 2004-03-02 2005-09-07 United Technologies Corporation High elasticity modulus turbine metallic component for high vibratory operation
CN1966750A (en) 2005-11-18 2007-05-23 中国科学院金属研究所 Third nickel-base high-temperature single crystal alloy in low cost
EP1930455A1 (en) 2005-09-27 2008-06-11 National Institute for Materials Science Nickel-base superalloy with excellent unsusceptibility to oxidation

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6989174B2 (en) * 2004-03-16 2006-01-24 General Electric Company Method for aluminide coating a hollow article

Patent Citations (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4169742A (en) 1976-12-16 1979-10-02 General Electric Company Cast nickel-base alloy article
EP0150917A2 (en) 1984-01-10 1985-08-07 AlliedSignal Inc. Single crystal nickel-base alloy
US4935072A (en) 1986-05-13 1990-06-19 Allied-Signal, Inc. Phase stable single crystal materials
EP0362661A1 (en) 1988-10-03 1990-04-11 General Electric Company Cast columnar grain hollow nickel base alloy article and alloy and heat treatment for making
US6419763B1 (en) 1999-05-20 2002-07-16 Alstom (Switzerland) Ltd Nickel-base superalloy
EP1057899A2 (en) 1999-05-26 2000-12-06 General Electric Company Compositions and single-crystal articles of hafnium-modified and/or zirconium-modified nickel-base superalloys
EP1184473A2 (en) 2000-08-30 2002-03-06 Kabushiki Kaisha Toshiba Nickel-base single-crystal superalloys, method of manufacturing same and gas turbine high temperature parts made thereof
US20030075247A1 (en) 2001-05-30 2003-04-24 Yutaka Koizumi Ni-based single crystal super alloy
US20030041930A1 (en) 2001-08-30 2003-03-06 Deluca Daniel P. Modified advanced high strength single crystal superalloy composition
US20040229072A1 (en) 2002-12-16 2004-11-18 Murphy Kenneth S. Nickel base superalloy
EP1571297A2 (en) 2004-03-02 2005-09-07 United Technologies Corporation High elasticity modulus turbine metallic component for high vibratory operation
EP1930455A1 (en) 2005-09-27 2008-06-11 National Institute for Materials Science Nickel-base superalloy with excellent unsusceptibility to oxidation
CN1966750A (en) 2005-11-18 2007-05-23 中国科学院金属研究所 Third nickel-base high-temperature single crystal alloy in low cost

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EP3141623B1 (en) 2019-05-29
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US20100135846A1 (en) 2010-06-03
EP2218798A3 (en) 2011-11-23

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