EP3141623B1 - 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

Info

Publication number
EP3141623B1
EP3141623B1 EP16181107.0A EP16181107A EP3141623B1 EP 3141623 B1 EP3141623 B1 EP 3141623B1 EP 16181107 A EP16181107 A EP 16181107A EP 3141623 B1 EP3141623 B1 EP 3141623B1
Authority
EP
European Patent Office
Prior art keywords
pwa
alloy
alloys
single crystal
bubble
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP16181107.0A
Other languages
German (de)
French (fr)
Other versions
EP3141623A1 (en
Inventor
Alan D. Cetel
Dilip M. Shah
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
RTX Corp
Original Assignee
United Technologies Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=42048327&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP3141623(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by United Technologies Corp filed Critical United Technologies Corp
Publication of EP3141623A1 publication Critical patent/EP3141623A1/en
Application granted granted Critical
Publication of EP3141623B1 publication Critical patent/EP3141623B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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%

Definitions

  • All second and higher generation nickel-base directionally solidified and single crystal superalloy compositions contain additions of rhenium of at least 3 wt%.
  • 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.
  • EP 1057899 A2 discloses compositions and single-crystal articles of hafnium-modified and/or zirconium modified nickel-based alloys.
  • the present invention can be seen to provide a lower cost high strength nickel based alloy broadly comprising 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, up to 3.0 wt% ruthenium, and the balance nickel.
  • 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%.
  • Re is also thought to reduce the coarsening rate of the ⁇ ' phase, contributing to improving creep strength.
  • 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 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 second 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.

Landscapes

  • 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%. 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.
  • EP 1057899 A2 discloses compositions and single-crystal articles of hafnium-modified and/or zirconium modified nickel-based alloys.
  • 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 broadly comprising 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, up to 3.0 wt% ruthenium, and the balance nickel.
  • 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. TABLE I
    Alloy Cr Mo W Ta Al Co Re Ru Hf P Density Creep Life Nv38 Stability COMMENTS
    Single Crystal
    1a 4 2 11 6 6 12.5 0 0 48.5 0.322 PWA 1484 2.07 S Creep = 1484 No Re/Ru
    1b 5 2 9 6 6 12.5 0 3 48.5 0.318 PWA 1484 2.07 S Creep = 1484 No Re (3Ru)
    1c 4 2 9 6 6 12.5 1.5 0 48.5 0.32 PWA 1484 2.04 S
    2a 2 1.75 11.5 6 6 12.5 3 3 58 0.331 PWA 1497 2.02 S Creep = 1497 with 3Re. 3Ru
    2b 2 1 12.5 6 6 12.5 3 0 55.75 0.331 1497-15F 2.02 S Creep - 1497 with 3Re 0Ru
    3a 2 1.75 15.5 6 6 12.5 0 3 58 0.334 PWA 1497 2.09 S Creep = 1497 with 0Re. 3Ru
    3b 2 2 13.5 6 6 12.5 1.5 0 55.25 0.331 1497-20F 2.08 S creep < 1497 with 1.5Re. 0Ru
    3c 2 2 15 6 6 12.5 0 0 54.5 0.331 1497-25F 2.08 S creep < 1497 with 0Re. 0Ru
    PWA 1484 5 1.9 5.9 8.7 5.65 10 3 0 48 0.323 2.08
    PWA 1497 2 1.8 6 8.25 5.65 16.5 6 3 56 0.331
    DS
    PWA 1426 6.4 1.7 6.4 4 5.9 12.5 3 0 1.5 44.9 0.316 Base 2.07 S
    PWA 1426a 6.4 1.7 8.4 4 5.9 12 5 1.5 0 1.5 44.9 0.318 Base 2.11 S creep = 1426 1.5Re
    PWA 1426b 6.4 1.7 10.4 4 5.9 12.5 0 0 1.5 44.9 0.322 Base 2.24 Mg creep = 1426 0Re
  • 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 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 second 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 may 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 scope of the appended claims.

Claims (6)

  1. A nickel based alloy consisting of 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, up to 3.0 wt% ruthenium, and the balance nickel.
  2. The nickel based alloy of claim 1, wherein said chromium is present in an amount from 1.5 to 2.5 wt%, said molybdenum is present in an amount from 0.5 to 1.5 wt%.
  3. The nickel based alloy of claim 1 or 2, wherein said tungsten is present in an amount from 11.5 to 13.5 wt%.
  4. The nickel based alloy of claim 1, 2 or 3, wherein said tantalum is present in an amount from 5.0 to 7.0 wt%, said aluminum is present in an amount from 5.8 to 6.25 wt%, and said cobalt is present in an amount from 11.5 to 13.5 wt%.
  5. The nickel based alloy of any of claims 1 to 4, wherein said rhenium is present in amount from 2.5 to 3.5 wt%, said hafnium is present in an amount from 0.2 to 0.4 wt%, and said yttrium is present in an amount of from 0.001 to 0.01 wt%.
  6. The nickel based alloy of any of claims 1 to 5, wherein the total ruthenium and rhenium content is no greater than 6.0 wt%.
EP16181107.0A 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced re and ru content Active EP3141623B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US11871408P 2008-12-01 2008-12-01
EP09252708.4A EP2218798B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content

Related Parent Applications (2)

Application Number Title Priority Date Filing Date
EP09252708.4A Division EP2218798B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content
EP09252708.4A Division-Into EP2218798B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content

Publications (2)

Publication Number Publication Date
EP3141623A1 EP3141623A1 (en) 2017-03-15
EP3141623B1 true EP3141623B1 (en) 2019-05-29

Family

ID=42048327

Family Applications (2)

Application Number Title Priority Date Filing Date
EP16181107.0A Active EP3141623B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced re and ru content
EP09252708.4A Active EP2218798B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP09252708.4A Active EP2218798B1 (en) 2008-12-01 2009-12-01 Lower cost high strength single crystal superalloys with reduced Re and Ru content

Country Status (2)

Country Link
US (1) US20100135846A1 (en)
EP (2) EP3141623B1 (en)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
US20110076180A1 (en) * 2009-09-30 2011-03-31 General Electric Company Nickel-Based Superalloys and Articles
US20110076181A1 (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
ES2682362T3 (en) 2015-05-05 2018-09-20 MTU Aero Engines AG Super-alloy of rhenium-free nickel with low density

Family Cites Families (14)

* 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
US4765850A (en) 1984-01-10 1988-08-23 Allied-Signal Inc. Single crystal nickel-base super alloy
CA1315572C (en) 1986-05-13 1993-04-06 Xuan Nguyen-Dinh Phase stable single crystal materials
AU630623B2 (en) * 1988-10-03 1992-11-05 General Electric Company An improved article and alloy therefor
DE59904846D1 (en) 1999-05-20 2003-05-08 Alstom Switzerland Ltd Nickel-based superalloy
US6444057B1 (en) * 1999-05-26 2002-09-03 General Electric Company Compositions and single-crystal articles of hafnium-modified and/or zirconium-modified nickel-base superalloys
EP1184473B1 (en) * 2000-08-30 2005-01-05 Kabushiki Kaisha Toshiba Nickel-base single-crystal superalloys, method of manufacturing same and gas turbine high temperature parts made thereof
JP3840555B2 (en) 2001-05-30 2006-11-01 独立行政法人物質・材料研究機構 Ni-based single crystal superalloy
US20030041930A1 (en) 2001-08-30 2003-03-06 Deluca Daniel P. Modified advanced high strength single crystal superalloy composition
CA2440573C (en) 2002-12-16 2013-06-18 Howmet Research Corporation Nickel base superalloy
US7338259B2 (en) * 2004-03-02 2008-03-04 United Technologies Corporation High modulus metallic component for high vibratory operation
US6989174B2 (en) * 2004-03-16 2006-01-24 General Electric Company Method for aluminide coating a hollow article
WO2007037277A1 (en) * 2005-09-27 2007-04-05 National Institute For Materials Science Nickel-base superalloy with excellent unsusceptibility to oxidation
CN100430500C (en) 2005-11-18 2008-11-05 中国科学院金属研究所 Third nickel-base high-temperature single crystal alloy in low cost

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
US20100135846A1 (en) 2010-06-03
EP3141623A1 (en) 2017-03-15
EP2218798A2 (en) 2010-08-18
EP2218798B1 (en) 2016-09-14
EP2218798A3 (en) 2011-11-23

Similar Documents

Publication Publication Date Title
EP3141623B1 (en) Lower cost high strength single crystal superalloys with reduced re and ru content
US7169241B2 (en) Ni-based superalloy having high oxidation resistance and gas turbine part
EP2503013B1 (en) Heat-resistant superalloy
JP2003193161A (en) High temperature resistant structural member
EP1433865B1 (en) High-strength Ni-base superalloy and gas turbine blades
JP6788605B2 (en) Nickel-based alloy
KR20070091350A (en) A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy
EP2612935B1 (en) Low rhenium single crystal superalloy for turbine blades and vane applications
PT2467505E (en) Nickel-based superalloy and articles made from said alloy
EP1927669B1 (en) Low-density directionally solidified single-crystal superalloys
WO2010119709A1 (en) Nickel-base single-crystal superalloy and turbine wing using same
US20080240926A1 (en) Cobalt-Free Ni-Base Superalloy
US20060057018A1 (en) Composition of matter
JP2018526530A (en) Nickel base alloy
US20050139295A1 (en) Method for selecting a reduced-tantalum superalloy composition of matter and article made therefrom
US9580774B2 (en) Creep-resistant, rhenium-free nickel base superalloy
US20170051382A1 (en) Optimized nickel-based superalloy
EP1715068B1 (en) Nickel-based super-heat-resistant alloy and gas turbine component using same
EP2449140B1 (en) Nickel base superalloy compositions and articles thereof
KR20120105693A (en) Ni base single crystal superalloy with enhanced creep property
US20110256018A1 (en) Ni-Based Single Crystal Superalloy with Good Creep Property
RU2803779C1 (en) Cast corrosion-resistant nickel-based polycrystalline superalloy
CN113366132A (en) Nickel-based superalloys having high mechanical and environmental strength at high temperatures and low densities
EP2703507B1 (en) Ni base alloy and gas turbine blade and gas turbine utilizing the same
US20220098705A1 (en) Nickel-based superalloy having high mechanical strength at a high temperature

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

AC Divisional application: reference to earlier application

Ref document number: 2218798

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

17P Request for examination filed

Effective date: 20170223

RBV Designated contracting states (corrected)

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20170802

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20181207

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AC Divisional application: reference to earlier application

Ref document number: 2218798

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1138297

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190615

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602009058589

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20190529

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190829

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190930

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190830

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190829

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1138297

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602009058589

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

26N No opposition filed

Effective date: 20200303

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20191231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191201

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191231

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191231

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20191231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190929

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20091201

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20190529

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 602009058589

Country of ref document: DE

Owner name: RAYTHEON TECHNOLOGIES CORPORATION (N.D.GES.D.S, US

Free format text: FORMER OWNER: UNITED TECHNOLOGIES CORPORATION, FARMINGTON, CONN., US

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230520

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20231121

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20231122

Year of fee payment: 15

Ref country code: DE

Payment date: 20231121

Year of fee payment: 15