EP1568794A1 - Superalliage a cristal unique a base de ni - Google Patents

Superalliage a cristal unique a base de ni Download PDF

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EP1568794A1
EP1568794A1 EP03777308A EP03777308A EP1568794A1 EP 1568794 A1 EP1568794 A1 EP 1568794A1 EP 03777308 A EP03777308 A EP 03777308A EP 03777308 A EP03777308 A EP 03777308A EP 1568794 A1 EP1568794 A1 EP 1568794A1
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single crystal
based single
crystal super
super alloy
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EP1568794A4 (fr
EP1568794B1 (fr
Inventor
T. National Institute for Mat. Science KOBAYASHI
Y. National Institute for Mat. Science KOIZUMI
T. National Institute for Mat. Science YOKOKAWA
H. National Institute for Mat. Science HARADA
Y. Ishikawajima-Harima Heavy Ind. Co. Ltd. AOKI
M. Ishikawajima-Harima Heavy Ind. Co. Ltd. ARAI
S. Ishikawajima-Harima Heavy Ind. Co. Ltd MASAKI
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Independent Administrative Institution National In
IHI Corp
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National Institute for Materials Science
Ishikawajima Harima Heavy Industries Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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

  • the present invention relates to a Ni-based single crystal super alloy, and more particularly, to a technology employed for improving the creep characteristics of Ni-besed single crystal super alloy.
  • Ni-based single crystal super alloys after performing solution treatment at a prescribed temperature, aging treatment is performed to obtain an Ni-based single crystal super alloy.
  • This alloy is referred to as a so-called precipitation hardened alloy, and has a from in which the precipitation phase in the form of a ⁇ ' phase is precipitated in a matrix in the form of a ⁇ phase.
  • CMSX-2 Cannon-Muskegon, US Patent No. 4,582,548
  • CMSX-4 Cannon-Muskegon, US Patent No. 4,643,782
  • Rene'N6 General Electric, US Patent No. 5,455,120
  • CMSX-10K Canon-Muskegon, US Patent No. 5,366,695
  • 3B General Electric, US Patent No. 5,151,249 is a fourth-generation alloy.
  • CMSX-2 which is a first-generation alloy
  • CMSX-4 which is a second-generation alloy
  • their creep strength is inferior to third-generation alloys.
  • the third-generation alloys of ReneN6 and CMSX-10 are alloys designed to have improved creep strength at high temperatures in comparison with second-generation alloys, since the composite ratio of Re (5 wt% or more) exceeds the amount of Re that dissolves into the matrix ( ⁇ phase), the excess Re compounds with other elements and as a result, a so-called TCP (topologically close packed) phase precipitates at high temperatures causing the problem of decreased creep strength.
  • the object of the present invention is to provide a Ni-based single crystal super alloy that makes it possible to improve strength by preventing precipitation of the TCP phase at high temperatures.
  • the Ni-based single crystal super alloy of the present invention is characterized by having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% ofW, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co and 4.1-14.0 wt% of Ru in terms of its weight ratio, with the remainder consisting of Ni and unavoidable impurities.
  • the Ni-based single crystal super alloy of the present invention is characterized by having a composition comprising 5.0-7.0 wt% of Al, 4.0-6.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, and 4.1-14.0 wt% of Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities.
  • the Ni-based single crystal super alloy of the present invention is characterized by having a composition comprising 5.0-7.0 wt% of Al, 4.0-6.0 wt% of Ta, 2.9-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co and 4.1-14.0 wt% of Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities.
  • the Ni-based single crystal super alloy of the present invention is preferably having a composition comprising 5.9 wt% of Al, 5.9 wt% of Ta, 3.9 wt% of Mo, 5.9 wt% of W, 4.9 wt% of Re, 0.10 wt% of Hf, 2.9 wt% of Cr, 5.9 wt% of Co and 5.0 wt% of Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities, in the Ni-based single crystal super alloys previously described.
  • the creep endurance temperature at 137 MPa and 1000 hours can be made to be 1344 K (1071°C).
  • the Ni-based single crystal super alloy of the present invention is preferably having a composition comprising 5.8 wt% of Co, 2.9 wt% of Cr, 3.1 wt% of Mo, 5.8 wt% of W, 5.8 wt% of Al, 5.6 wt% of Ta, 5.0 wt% of Ru, 4.9 wt% of Re and 0.10 wt% of Hf in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities, in the Ni-based single crystal super alloys previously described.
  • the creep endurance temperature at 137 MPa and 1000 hours can be made to be 1366 K (1093°C).
  • the Ni-based single crystal super alloy of the present invention is preferably having a composition comprising 5.8 wt% of Co, 2.9 wt% of Cr, 3.9 wt% of Mo, 5.8 wt% of W, 5.8 wt% of Al, 5.8 wt% (5.82 wt%) or 5.6 wt% of Ta, 6.0 wt% of Ru, 4.9 wt% of, Re and 0.10 wt% of Hf in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities, in the Ni-based single crystal super alloys previously described.
  • the creep endurance temperature at 137 MPa and 1000 hours can be made to be 1375 K (1102°C) or 1379 K (1106°C).
  • 0-2.0 wt% of Ti in terms of weight ratio can be included in the Ni-based single crystal super alloys previously described.
  • Ni-based single crystal super alloys previously described.
  • At least one of elements selected from B, C, Si, Y, La, Ce, V and Zr can be included in the Ni-based single crystal super alloys previously described
  • 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr in terms of weight ratio are included in the alloys.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 10.0-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less ofY, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.8-7.0 wt% of Al, 4.0-5.6 wt% of Ta, 3.3-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 29-4.3 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less ofB, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% ofAl, 4.0-10.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.9-5.0 wt% of Cr, 0-9.9 wt% of Co, 6.5-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less ofB, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-6.0 wt% of Ta, 3.3-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-5.6 wt% of Ta, 3.3-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hi, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 3.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 0.05 wt% or less ofB, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.8-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 3.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less ofB, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 3.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.9-4.3 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% of Ru, 4.0 wt% or less of Nb, 2.0 wt% or less of Ti, 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less ofY, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the above described Ni-based single crystal super alloy is more preferably having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta+Nb+Ti, 3.3-4.5 wt% of Mo, 4.0-10.0 wt% ofW, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co, 4.1-14.0 wt% ofRu, 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr.
  • the Ni-based single crystal super alloy of the present invention is characterized by a2 ⁇ 0.999a1 when the lattice constant of the matrix is taken to be a1 and the lattice constant of the precipitation phase is taken to be a2 in the Ni-based single crystal super alloys previously described.
  • the relationship between a1 and a2 is such that a2 ⁇ 0.999a1 when the lattice constant of the matrix is taken to be a1 and the lattice constant of the precipitation phase is taken to be a2, and since the lattice constant a2 of the precipitation phase is -0.1% or less of the lattice constant a1 of the matrix, the precipitation phase that precipitates in the matrix precipitates so as to extend continuously in the direction perpendicular to the direction of the load.
  • strength at high temperatures can be enhanced without dislocation defects moving within the alloy structure under stress.
  • the lattice constant of the crystals of the precipitation phase a2 is 0.9965 or less of the lattice constant of the crystals of the matrix a1
  • Ni-based single crystal super alloy of the present invention is characterized by comprising the feature that the dislocation space of the alloy is 40 nm or less.
  • the Ni-based single crystal super alloy of the present invention is an alloy comprised of Al, Ta, Mo, W, Re, Hf, Cr, Co, Ru, Ni (remainder) and unavoidable impurities.
  • the above Ni-based single crystal super alloy is an alloy having a composition comprising 5.0-7.0 wt% of Al, 4.0-10.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co and 4.1-14.0 wt% of Ru, with the remainder consisting of Ni and unavoidable impurities.
  • the above Ni-based single crystal super alloy is an alloy having a composition comprising 5.0-7.0 wt% of Al, 4.0-6.0 wt% of Ta, 1.1-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co and 4.1-14.0 wt% of Ru, with the remainder consisting of Ni and unavoidable impurities.
  • the above Ni-based single crystal super alloy is an alloy having a composition comprising 5.0-7.0 wt% of Al, 4.0-6.0 wt% of Ta, 2.9-4.5 wt% of Mo, 4.0-10.0 wt% of W, 3.1-8.0 wt% of Re, 0-0.50 wt% of Hf, 2.0-5.0 wt% of Cr, 0-9.9 wt% of Co and 4.1-14.0 wt% of Ru, with the remainder consisting of Ni and unavoidable impurities.
  • All of the above alloys have an austenite phase in the form of a ⁇ phase (matrix) and an intermediate regular phase in the form of a ⁇ ' phase (precipitation phase) that is dispersed and precipitated in the matrix.
  • the ⁇ ' phase is mainly composed of an intermetallic compound represented by Ni 3 Al, and the strength of the Ni-based single crystal super alloy at high temperatures is improved by this ⁇ ' phase.
  • the composite ratio of Cr is preferably within the range of 20 wt% or more to 5.0 wt% or less, and more preferably 2.9 wt%. This ratio is more preferably within the range of 2.9 wt% or more to 5.0 wt% or less, more preferably within the range of 2.9 wt% or more to 4.3 wt% or less, and most preferably 2.9 wt%. If the composite ratio of Cr is less than 2.0 wt%, the desired high-temperature corrosion resistance cannot be secured, thereby making this undesirable. If the composite ratio of Cr exceeds 5.0 wt%, in addition to precipitation of the ⁇ ' phase being inhibited, harmful phases such as a ⁇ phase or ⁇ phase form that cause a decrease in strength at high temperatures, thereby making this undesirable.
  • Mo In addition to improving strength at high temperatures by dissolving into the matrix in the form of the ⁇ phase in the presence of W and Ta, Mo also improves strength at high temperatures due to precipitation hardening. Furthermore, Mo also improves the aftermentioned lattice misfit and dislocation networks of the alloy which relate characteristics of this alloy.
  • the composite ratio of Mo is preferably within the range of 1.1 wt% or more to 4.5 wt% or less, more preferably within the range of 2.9 wt% or more to 4.5 wt% or less. This ratio is more preferably within the range of 3.1 wt% or more to 4.5 wt% or less, more preferably within the range of 3.3wt% or more to 4.5 wt% or less, and most preferably 3.1 wt% or 3.9 wt%. If the composite ratio of Mo is less than 1.1 wt%, strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. If the composite ratio of Mo exceeds 4.5 wt%, strength at high temperatures decreases, and corrosion resistance at high temperatures also decreases, thereby making this undesirable.
  • W improves strength at high temperatures due to the actions of solution hardening and precipitation hardening in the presence of Mo and Ta as previously mentioned.
  • the composite ratio of W is preferably within the range of 4.0 wt% or more to 10.0 wt% or less, and most preferably 5.9 wt% or 5.8 wt%. If the composite ratio of W is less than 4.0 wt%, strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. If the composite ratio of W exceeds 10.0 wt%, high-temperature corrosion resistance decreases, thereby making this undesirable.
  • Ta improves strength at high temperatures due to the actions of solution hardening and precipitation hardening in the presence of Mo and W as previously mentioned, and also improves strength at high temperatures as a result of a portion of the Ta undergoing precipitation hardening relative to the ⁇ ' phase.
  • the composite ratio of Ta is preferably within the range of 4.0 wt% or more to 10.0 wt% or less, more preferably within the range of 4.0 wt% or more to 6.0 wt% or less. This ratio is more preferably within the range of 4.0 wt% or more to 5.6 wt% or less, and most preferably 5.6 wt% or 5.82 wt%.
  • the composite ratio of Ta is less than 4.0 wt%, strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. If the composite ratio of Ta exceeds 10.0 wt%, the ⁇ phase and ⁇ phase form that cause a decrease in strength at high temperatures, thereby making this undesirable.
  • Al improves strength at high temperatures by compounding with Ni to form an intermetallic compound represented by Ni 3 Al, which composes the ⁇ ' phase that finely and uniformly disperses and precipitates in the matrix, at a ratio of 60-70% in terms of volume percent.
  • the composite ratio of Al is preferably within the range of 5.0 wt% or more to 7.0 wt% or less. This ratio is more preferably within the range of 5.8 wt% or more to 7.0 wt% or less, and most preferably 5.9 wt% or 5.8 wt%. If the composite ratio of Al is less than 5.0 wt%, the precipitated amount of the ⁇ ' phase becomes insufficient, and strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable.
  • the composite ratio of Al exceeds 7.0 wt%, a large amount of a coarse ⁇ phase referred to as the eutectic ⁇ ' phase is formed, and this eutectic ⁇ ' phase prevents solution treatment and makes it impossible to maintain strength at high temperatures at a high level, thereby making this undesirable.
  • Hf is an element that segregates at the grain boundary and improves strength at high temperatures by strengthening the grain boundary as a result of being segregated at the grain boundary between the ⁇ phase and ⁇ ' phase.
  • the composite ratio of Hf is preferably within the range of 0.01 wt% or more to 0.50 wt% or less, and most preferably 0.10 wt%. If the composite ratio of Hf is less than 0.01 wt%, the precipitated amount of the ⁇ ' phase becomes insufficient and strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. However, the composite ratio of Hf may be within the range of 0 wt% or more to less than 0.01 wt% if necessary. Furthermore, if the composite ratio of Hf exceeds 0.50 wt%, local melting is induced which results in the risk of decreased strength at high temperatures, thereby making this undesirable.
  • Co improves strength at high temperatures by increasing the solution limit at high temperatures relative to the matrix such as Al and Ta, and dispersing and precipitating a fine ⁇ ' phase by heat treatment
  • the composite ratio of Co is preferably within the range of 0.1 wt% or more to 9.9 wt% or less, and most preferably 5.8 wt%. If the composite ratio of Co is less than 0.1 wt%, the precipitated amount of the ⁇ ' phase becomes insufficient and the strength at high temperatures cannot be maintained, thereby making this undesirable. However, the composite ratio of Co may be within the range of 0 wt% or more to less than 0.1 wt%, if necessary.
  • the composite ratio of Co exceeds 9.9 wt%, the balance with other elements such as Al, Ta, Mo, W, Hf and Cr is disturbed resulting in the precipitation of harmful phases that cause a decrease in strength at high temperatures, thereby making this undesirable.
  • the composite ratio of Re is preferably within the range of 3.1 wt% or more to 8.0 wt% or less, and most preferably 4.9 wt%. If the composite ratio of Re is less than 3.1 wt%, solution strengthening of the ⁇ phase becomes insufficient and strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. If the composite ratio of Re exceeds 8.0 wt%, the TCP phase precipitates at high temperatures and strength at high temperatures cannot be maintained at a high level, thereby making this undesirable.
  • the composite ratio of Ru is preferably within the range of 4.1 wt% or more to 14.0 wt% or less. This ratio is more preferably within the range of 10.0 wt% or more to 14.0 wt% or less, or preferably within the range of 6.5 wt% or more to 14.0 wt% or less, and most preferably 5.0 wt%, 6.0 wt% or 7.0 wt%. If the composite ratio of Ru is less than 1.0 wt%, the TCP phase precipitates at high temperatures and strength at high temperatures cannot be maintained at a high level, thereby making this undesirable.
  • the composite ratio of Ru is less than 4.1 wt%, strength at high temperatures decreases compared to the case when the composite ratio of Ru is 4.1 wt% or more. Furthermore, if the composite ratio of Ru exceeds 14.0 wt%, the ⁇ phase precipitates and strength at high temperatures deceases which is also undesirable.
  • the composite ratios of Al, Ta, Mo, W, Hf, Cr, Co and Ni to the optimum ratios, together with improving strength at high temperatures by setting the aftermentioned lattice misfit and dislocation networks of the alloy which are calculated from the lattice constant of the ⁇ phase and the lattice constant of the ⁇ ' phase within their optimum ranges, and precipitation of the TCP phase can be inhibited by adding Ru.
  • the composite ratios of Al, Cr, Ta and Mo to the aforementioned ratios, the production cost for the alloy can be decreased.
  • relative strength of the alloy can be increased and the lattice misfit and dislocation networks of the alloy can be adjusted to the optimum value.
  • lattice constant a2 of the crystals of the precipitation phase is preferably -0.1% or less lattice constant a1 of the crystals of the matrix.
  • the lattice constant of the crystals of the precipitation phase a2 is 0.9965 or less of the lattice constant of the crystals of the matrix a1.
  • the above-described relationship between a1 and a2 becomes a2 ⁇ 0.9965a1.
  • the percentage of the lattice constant a2 relative to the lattice constant a1 is called "lattice misfit".
  • the composition of the composite elements that compose the Ni-based single crystal super alloy is suitably adjusted.
  • FIG. 1 shows a relationship between the lattice misfit of the alloy and the time until the alloy demonstrates creep rupture (creep rupture life).
  • the preferable value of the lattice misfit is determined to - 0.35 or lower.
  • the composition of Mo is maintained to a high level, and the composition of the other composite elements is suitably adjusted.
  • Ti can be further included in the above Ni-based super crystal super alloy.
  • the composite ratio of Ta is preferably within the range of 0 wt% or more to 2.0 wt% or less. If the composite ratio of Ti exceeds 2.0 wt%, the harmful phase precipitates and the strength at high temperatures cannot be maintained, thereby making this undesirable.
  • Nb can be further included in the above Ni-based super crystal super alloy,
  • the composite ratio of Nb is preferably within the range of 0 wt% or more to 4.0 wt% or less. If the composite ratio of Nb exceeds 4.0 wt%, the harmful phase precipitates and the strength at high temperatures cannot be maintained, thereby making this undesirable.
  • strength at high temperatures can be improved by adjusting the total composite ratio of Ta, Nb and Ti (Ta+Nb+Ti) within the range of 4.0 wt% or more to 10.0 wt% or less.
  • B, C, Si, Y, La, Ce, V and Zr and the like can be included in the above Ni-based super crystal super alloy, for example.
  • the composite ratio of each element is preferably 0.05 wt% or less of B, 0.15 wt% or less of C, 0.1 wt% or less of Si, 0.1 wt% or less of Y, 0.1 wt% or less of La, 0.1 wt% or less of Ce, 1 wt% or less of V and 0.1 wt% or less of Zr. If the composite ratio of each element exceeds the above range, the harmful phase precipitates and the strength at high temperatures cannot be maintained, thereby making this undesirable.
  • a dislocation space of the alloy is 40 nm or less.
  • the reticulated dislocation (displacement of atoms which are connected as a line) in the alloy is called dislocation networks, and a space between adjacent reticulations is called "dislocation space".
  • FIG. 2 shows a relationship between the dislocation space of the alloy and the time until the alloy demonstrates creep rupture (creep rupture life).
  • the preferable value of the dislocation space is determined to 40 nm or lower.
  • the composition of Mo is maintained to a high level, and the composition of the other composite elements is suitably adjusted.
  • FTG. 3 is a transmission electron microgram of the Ni-based single crystal super alloy showing an embodiment (aftermentioned embodiment 3) of the dislocation networks and dislocation space of the Ni-based single crystal super alloy of the present invention. As shown in FIG. 3, in case of the Ni-based single crystal super alloy of the present invention, the dislocation space is 40 nm or lower.
  • Ni-based single crystal super alloys may cause reverse partitioning, however, in Ni-based single crystal super alloy of the present invention does not cause reverse partitioning.
  • solution treatment and aging treatment were performed on the alloy ingots followed by observation of the state of the alloy structure with a scanning electron microscope (SEM).
  • Solution treatment consisted of holding for 1 hour at 1573K (1300°C) followed by heating to 1613K (1340°C) and holding for 5 hours.
  • aging treatment consisted of consecutively performing primary aging treatment consisting of holding for 4 hours at 1273K-1423K (1000°C -1150°C) and secondary aging treatment consisting of holding for 20 hours at 1143K (870°C).
  • reference example 5 having a composition of 4.0 wt% ofRu
  • embodiments 1, 2, 4, 9, 10 and 11 having a composition approximately 5.0 wt% ofRu
  • embodiments 3, 12 and 13 having a composition of 6.0 wt% of Ru
  • embodiment 14 having a composition of 7,0 wt% of Ru, were determined to have high strength at high temperature.
  • samples of reference examples 1-6 and embodiments 1-14 were determined to have a high withstand temperature (1356K (1083°C)) equal to or greater than the alloys of the prior art (comparative Examples 1-5).
  • samples of reference example 1-6 and embodiments 1-14 were determined to have a high withstand temperature (embodiment 1: 1344K (1071°C), embodiment 2:1366K (1093°C), embodiment 3:1375K (1102°C), embodiment 4:1372K (1099°C), embodiment 5:1379K (1106°C), embodiment 6: 1379K (1106°C), embodiment 7:1379K (1106°C), embodiment 8: 1363K (1090°C), embodiment 9:1358K (1085°C), embodiment 10:1362K (1089°C), embodiment 11:1361K (1088°C), embodiment 12: 1363K (1090°C), embodiment 13: 1366K (1093°C) and embodiment 14:1384K (1111°C)).
  • this alloy bas a higher heat resistance temperature than Ni-based single crystal super alloys of the prior art, and was determined to have high strength even at high temperatures.
  • the composite ratio of Ru is preferably be determined to a range so as to keep the balance against the composition of the other composite elements is suitably adjusted (4.1 wt% or more to 14.0 wt% or less, for example).

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP03777308A 2002-12-06 2003-12-05 Superalliage a cristal unique a base de ni Expired - Lifetime EP1568794B1 (fr)

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EP1760164A1 (fr) * 2005-09-01 2007-03-07 General Electric Company Superalliage de nickel
EP1990434A1 (fr) * 2006-12-13 2008-11-12 United Technologies Corporation Alliages de cristal simple à densité modérée, faible et extrêmement faible pour applications AN2 élevées
EP1930455A4 (fr) * 2005-09-27 2010-01-13 Nat Inst For Materials Science Superalliage a base de nickel ne presentant pas de tendance a l'oxydation
WO2010111200A1 (fr) * 2009-03-24 2010-09-30 General Electric Company Superalliage à base de nickel superrésistant à l'oxydation et à un endommagement cyclique et articles formés à partir de celui-ci
WO2011041183A1 (fr) * 2009-09-30 2011-04-07 General Electric Company Superalliage à base de nickel résistant à la superoxydation et à un endommagement cyclique et articles formés à partir de celui-ci
EP1997923A4 (fr) * 2006-03-20 2012-02-01 Nat Inst For Materials Science SUPERALLIAGE A BASE DE Ni, SON PROCEDE DE PRODUCTION ET COMPOSANT DE LAME DE TURBINE OU DE PALETTE DE TURBINE
EP2006402A4 (fr) * 2006-03-31 2012-02-01 Nat Inst For Materials Science SUPERALLIAGE À BASE DE Ni ET SON PROCÉDÉ DE FABRICATION

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JP5467307B2 (ja) * 2008-06-26 2014-04-09 独立行政法人物質・材料研究機構 Ｎｉ基単結晶超合金とそれよりえられた合金部材
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CN109797433B (zh) * 2019-01-23 2021-05-25 深圳市万泽中南研究院有限公司 单晶高温合金、热端部件及设备
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CN113913942A (zh) * 2021-01-13 2022-01-11 中国航发北京航空材料研究院 镍基单晶合金、用途和热处理方法
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Publication number Priority date Publication date Assignee Title
EP1498503A4 (fr) * 2002-03-27 2006-01-25 Nat Inst For Materials Science Superalliage a base de ni solidifie de maniere directionnelle et superalliage a cristal unique a base de ni
EP1760164A1 (fr) * 2005-09-01 2007-03-07 General Electric Company Superalliage de nickel
EP1930455A4 (fr) * 2005-09-27 2010-01-13 Nat Inst For Materials Science Superalliage a base de nickel ne presentant pas de tendance a l'oxydation
EP1997923A4 (fr) * 2006-03-20 2012-02-01 Nat Inst For Materials Science SUPERALLIAGE A BASE DE Ni, SON PROCEDE DE PRODUCTION ET COMPOSANT DE LAME DE TURBINE OU DE PALETTE DE TURBINE
EP2006402A4 (fr) * 2006-03-31 2012-02-01 Nat Inst For Materials Science SUPERALLIAGE À BASE DE Ni ET SON PROCÉDÉ DE FABRICATION
EP1990434A1 (fr) * 2006-12-13 2008-11-12 United Technologies Corporation Alliages de cristal simple à densité modérée, faible et extrêmement faible pour applications AN2 élevées
US7704332B2 (en) 2006-12-13 2010-04-27 United Technologies Corporation Moderate density, low density, and extremely low density single crystal alloys for high AN2 applications
US8366838B2 (en) 2006-12-13 2013-02-05 United Technologies Corporation Moderate density, low density, and extremely low density single crystal alloys for high AN2 applications
WO2010111200A1 (fr) * 2009-03-24 2010-09-30 General Electric Company Superalliage à base de nickel superrésistant à l'oxydation et à un endommagement cyclique et articles formés à partir de celui-ci
WO2011041183A1 (fr) * 2009-09-30 2011-04-07 General Electric Company Superalliage à base de nickel résistant à la superoxydation et à un endommagement cyclique et articles formés à partir de celui-ci

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CA2508698C (fr) 2012-05-15
CA2508698A1 (fr) 2004-06-24
CN100357467C (zh) 2007-12-26
EP1568794A4 (fr) 2006-11-02
AU2003289214A8 (en) 2004-06-30
CN1745186A (zh) 2006-03-08
AU2003289214A1 (en) 2004-06-30
WO2004053177A1 (fr) 2004-06-24
EP1568794B1 (fr) 2009-02-04
US20060011271A1 (en) 2006-01-19
JP3814662B2 (ja) 2006-08-30
JPWO2004053177A1 (ja) 2006-04-13
DE60326083D1 (de) 2009-03-19

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