EP1262569B1 - Ni-based single crystal super alloy - Google Patents
Ni-based single crystal super alloy Download PDFInfo
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- EP1262569B1 EP1262569B1 EP02253782A EP02253782A EP1262569B1 EP 1262569 B1 EP1262569 B1 EP 1262569B1 EP 02253782 A EP02253782 A EP 02253782A EP 02253782 A EP02253782 A EP 02253782A EP 1262569 B1 EP1262569 B1 EP 1262569B1
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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-based single crystal super alloy.
- Ni-based single crystal super alloys after performing solution treatment at a prescribed tempetature, 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 (Canon-Muskegon, US Patent No. 4,582,548) is a first-generation alloy
- CMSX-4 Canon-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) are third-generation alloys
- 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 Rene'N6 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 elemems and as a result, a so-called TCP (topologically close packed) phase precipitates at high temperatures causing the problem of decreased creep strength.
- Japanese patent application publication no. 2000239771 discloses a Ni based super alloy, its production and gas turbine parts.
- the Ni based super alloy is intended to have high temperature corrosion resistance.
- FR2780983 provides a nickel based single crystal super alloy containing various alloying materials, intended to provide creep resistance at high temperature.
- the object of 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 present invention provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-8.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of its weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ⁇ 0.999a1.
- the present invention further provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 1.0-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co, and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ⁇ 0.999a1.
- the present invention further provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ⁇ 0.999a1.
- the lattice constant of the matrix ( ⁇ phase) and the lattice constant of the precipitation phase ( ⁇ ' phase) can be made to have optimum values. Consequently, strength at high temperatures can be enhanced.
- the Ni-based single crystal supper alloy ot the present invention preferably has a composition of 5.9 wt% Al, 5.9 wt% Ta, 2.9 wt% Mo, 5.9 wt% W, 4.9 wt% Re, 0.10 wt% Hf, 2.9 wt% Cr, 5.9 wt% Co and 2.0 wt% 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 tempetature at 137 MPa and 1000 hours can be made to be 1356 K (1083°C).
- 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 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 consisting of 5.0-7.0 wt% Al, 4.0-8.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- the above Ni-based single crystal super alloy is an alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 1.0-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- the above Ni-based single crystal super alloy is an alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- All of the above alloys have an austenite phase in the form ⁇ 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 2.0 wt% or more to 5.0 wt% or less, and more 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 y phase in the presence of W and Ta, Mo also improves strength at high temperatures due to precipitation hardening.
- the composite ratio of Mo is preferably within the range of 1.0 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, and most preferably 2.9 wt%. If the composite ratio of Mo is less than 1.0 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 8.0 wt% or less, and most preferably 5.9 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 8.0 wt%, high-temperature corrosion resistance decreases, thereby making this undesirable.
- Ta improves high-temperature strength due to the actions of solution hardening and precipitation hardening in the presence of Mo and W as previously mentioned, and also improves high-temperature strength 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 8.0 wt% or less, more preferably within the range of 4.0 wt% or more to 6.0 wt% or less, and most preferably 5.9 wt%. If 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 8.0 wt%, the ⁇ phase and ⁇ phase fonn that cause a decrease in strength at high temperatures, thereby making this undesirable.
- Al improves high-temperature strength 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, and most preferably 5.9 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 high-temperature strength 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 0.10wt%. 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. 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 within the range of 0.1 wt% and 5.9 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. If the composite ratio of Co excecds 5.9 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 3.0 wt% or more to 6.0 wt% or less, and most preferably 4.9 wt%. If the composite ratio of Re is less than 3.0 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 6.0 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 1.0 wt% or more to 4.0 wt% or less, and most preferably 2.0 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. If the composite ratio of Ru exceeds 4.0 wt%, the cost increases which is also undesirable.
- lattice constant a2 of the crystals of the precipitation phase is 00.1% or less lattice constant a1 of the crystals of the matrix.
- lattice constant a2 of the crystals of the precipitation phase should be -0.5% or more of lattice constant a1 of the crystals of the matrix.
- lattice constant a1 of the crystals of the matrix since both of the lattice constants are in the above relationship, since the precipitation phase precipitates so as to extend continuously in the direction perpendicular to the direction of the load when the precipitation phase precipitates in the matrix due to heat treatment, creep strength can be enhanced without movement of dislocation defects in the alloy structure in the presence of stress.
- the composition of the composite elements that compose the Ni-based single crystal super alloy is suitably adjusted.
- 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 1150°C and secondary aging treatment consisting of holding for 20 hours at 870°C.
- the sample of the present embodiment was determined to have high strength even under high temperature conditions of 1273K (1000°C).
- the sample of the present embodiment was determined to have a high withstand temperature (1356K (1083°C)) equal to or greater than Comparative Examples 1 through 5.
- this alloy has 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 fatigue strength were compared for the alloys of the Comparative Example 2 shown in Table 1 (CMSX-4) and the sample of the present embodiment shown in Table 2 (TMS-138).
- HCF high cycle fatigue strength
- LCF low cycle fatigue strength
- the max stress at high temperature of 1373K (1100°C) were measured by controlling a load, and the number of fatigue fracture cycle (Nf) were determined as 10 6 and 10 7 .
- the alternative peseudostress at high temperature of 1073K (800°C) were measured by controlling the distortion, and the number of fatigue fracture cycle (Nf) were determined as 10 3 and 10 4 .
- the alloy of the present invention (TMS-138) was determined to have a high fatigue strength in addition to the Creep strength at high temperature compared to the conventional Ni-based single crystal super alloy.
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Description
- 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-based single crystal super alloy.
- An example of the typical composition of Ni-based single crystal super alloy developed for use as a material for moving and stationary blades subject to high temperatures such as those in aircraft and gas turbines is shown in Table 1.
Alloy name Elements (wt%) Al Ti Ta Nb Mo W Re C Zr Hf Cr Co Ru Ni CMSX-2 6.0 1.0 6.0 - 1.0 8.0 - - - - 8.0 5.0 - Rem CMSX-4 5.6 1.0 6.5 - 0.6 6.0 3.0 - - - 6.5 9.0 - Rem Rene'N6 6.0 - 7.0 0.3 1.0 6.0 5.0 - - 0.2 4.0 13.0 - Rem CMSX-10K 5.7 0.3 8.4 0.1 0.4 5.5 6.3 - - 0.03 2.3 3.3 - Rem 3B 5.7 0.5 8.0 - - 5.5 6.0 0.05 - 0.15 5.0 12.5 3.0 Rem - In the above-mentioned Ni-based single crystal super alloys, after performing solution treatment at a prescribed tempetature, 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 γ' phase is precipitated in a matrix in the form of a γ phase.
- Among the alloys listed in Table 1, CMSX-2 (Canon-Muskegon, US Patent No. 4,582,548) is a first-generation alloy, CMSX-4 (Canon-Muskegon, US Patent No. 4,643,782) is a second-generation alloy, Rene'N6 (General Electric, US Patent No. 5,455,120) and CMSX-10K (Canon-Muskegon, US Patent No. 5,366,695) are third-generation alloys, and 3B (General Electric, US Patent No. 5,151,249) is a fourth-generation alloy.
- Although the above-mentioned CMSX-2, which is a first-generation alloy, and CMSX-4, which is a second-generation alloy, have comparable creep strength at low temperatures, since a large amount of the eutectic γ' phase remains following high-temperature solution treatment, their creep strength is inferior to third-generation alloys.
- In addition, although the third-generation alloys of Rene'N6 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 (γ phase), the excess Re compounds with other elemems and as a result, a so-called TCP (topologically close packed) phase precipitates at high temperatures causing the problem of decreased creep strength.
- In addition, making the lattice constant of the precipitation phase (γ' phase) slightly smaller than the lattice constant of the matrix (γ phase) is effective in improving the creep stength of Ni-based single crystal super alloys. However, since the lattice constant of each phase fluctuates greatly fluctuated according to the composite ratios of the composite elements of the alloy, it is difficult to make fine adjustments in the lattice constant and as a result, there is the problem of considerable difficulty in improving creep strength.
- Japanese patent application publication no. 2000239771 discloses a Ni based super alloy, its production and gas turbine parts. The Ni based super alloy is intended to have high temperature corrosion resistance.
- FR2780983 provides a nickel based single crystal super alloy containing various alloying materials, intended to provide creep resistance at high temperature.
- In consideration of the above circumstances, the object of 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 following constitution is employed in the present invention in order to achieve the above object.
- The present invention provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-8.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of its weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ≤ 0.999a1.
- The present invention further provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 1.0-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co, and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ≤ 0.999a1.
- The present invention further provides an Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ≤ 0.999a1.
- According to the above Ni-based single crystal super alloy, precipitation of the TCP phase, which causes a decrease in creep strength, during use at high temperatures is inhibited by the addition of Ru. In addition, by setting the composite ratios of other composite elements within their optimum ranges, the lattice constant of the matrix (γ phase) and the lattice constant of the precipitation phase (γ' phase) can be made to have optimum values. Consequently, strength at high temperatures can be enhanced.
- In addition, the Ni-based single crystal supper alloy ot the present invention preferably has a composition of 5.9 wt% Al, 5.9 wt% Ta, 2.9 wt% Mo, 5.9 wt% W, 4.9 wt% Re, 0.10 wt% Hf, 2.9 wt% Cr, 5.9 wt% Co and 2.0 wt% 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.
- According to an Ni-based single crystal super alloy having this composition, the creep endurance tempetature at 137 MPa and 1000 hours can be made to be 1356 K (1083°C).
- According to the Ni-based single crystal super alloy of the invention, 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. As a result, strength at high temperatures can be enhanced without dislocation defects moving within the alloy structure under stress.
- The following provides a detailed explanation for carrying out the present invention.
- 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 consisting of 5.0-7.0 wt% Al, 4.0-8.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- In addition, the above Ni-based single crystal super alloy is an alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 1.0-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- Moreover, the above Ni-based single crystal super alloy is an alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.5 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru, with the remainder consisting of Ni and unavoidable impurities.
- All of the above alloys have an austenite phase in the form γ phase (matrix) and an intermediate regular phase in the form of a γ' phase (precipitation phase) that is dispersed and precipitated in the matrix. The γ' phase is mainly composed of an intermetallic compound represented by Ni3Al, and the strength of the Ni-based single crystal super alloy at high temperatures is improved by this γ' phase.
- Cr is an element that has superior oxidation resistance and improves the high-temperature corrosion resistance of the Ni-based single crystal super alloy. The composite ratio of Cr is preferably within the range of 2.0 wt% or more to 5.0 wt% or less, and more 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 γ' phase being inhibited, harmful phases such as a σ phase or µ phase form that cause a decrease in strength at high temperatures, thereby making this undesirable.
- In addition to improving strength at high temperatures by dissolving into the matrix in the form of the y phase in the presence of W and Ta, Mo also improves strength at high temperatures due to precipitation hardening. The composite ratio of Mo is preferably within the range of 1.0 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, and most preferably 2.9 wt%. If the composite ratio of Mo is less than 1.0 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 8.0 wt% or less, and most preferably 5.9 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 8.0 wt%, high-temperature corrosion resistance decreases, thereby making this undesirable.
- Ta improves high-temperature strength due to the actions of solution hardening and precipitation hardening in the presence of Mo and W as previously mentioned, and also improves high-temperature strength as a result of a portion of the Ta undergoing precipitation hardening relative to the γ' phase. The composite ratio of Ta is preferably within the range of 4.0 wt% or more to 8.0 wt% or less, more preferably within the range of 4.0 wt% or more to 6.0 wt% or less, and most preferably 5.9 wt%. If 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 8.0 wt%, the σ phase and µ phase fonn that cause a decrease in strength at high temperatures, thereby making this undesirable.
- Al improves high-temperature strength by compounding with Ni to form an intermetallic compound represented by Ni3Al, which composes the γ' 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, and most preferably 5.9 wt%. If the composite ratio of Al is less than 5.0 wt%, the precipitated amount of the γ' phase becomes insufficient, and strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. If the composite ratio of Al exceeds 7.0 wt%, a large amount of a coarse γ phase referred to as the eutectic γ' phase is formed, and this eutectic γ' 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 high-temperature strength by strengthening the grain boundary as a result of being segregated at the grain boundary between the γ phase and γ' 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 0.10wt%. If the composite ratio of Hf is less than 0.01 wt%, the precipitated amount of the γ' phase becomes insufficient and strength at high temperatures cannot be maintained at the desired level, thereby making this undesirable. 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 γ' phase by heat treatment. The composite ratio of Co is within the range of 0.1 wt% and 5.9 wt%. If the composite ratio of Co is less than 0.1 wt%, the precipitated amount of the γ' phase becomes insufficient and the strength at high temperatures cannot be maintained, thereby making this undesirable. If the composite ratio of Co excecds 5.9 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.
- Re improves high-temperature strength due to solution strengthening as a result of dissolving in the matrix in the form of the γ phase. On the other hand, if a large amount of Re is added, the harmful TCP phase precipitates at high temperatures, resulting in the risk of decreased strength at high temperatures. Thus, the composite ratio of Re is preferably within the range of 3.0 wt% or more to 6.0 wt% or less, and most preferably 4.9 wt%. If the composite ratio of Re is less than 3.0 wt%, solution strengthening of the γ 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 6.0 wt%, the TCP phase precipitates at high temperatures and strength at high temperatures cannot be maintained at a high level, thereby making this undesirable.
- Ru improves high-temperature strength by inhibiting precipiation of the TCP phase. The composite ratio of Ru is preferably within the range of 1.0 wt% or more to 4.0 wt% or less, and most preferably 2.0 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. If the composite ratio of Ru exceeds 4.0 wt%, the cost increases which is also undesirable.
- Particularly in the present invention, by adjusting 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 lattice constant of the γ phase and the lattice constant of the γ' phase within their optimum ranges, and precipitation of the TCP phase can be inhibited by adding Ru.
- In addition, in usage enviromnents at a high temperature from 1273 K(1000°C) to 1373K (1100°C), when the lattice constant of the crystals that compose the matrix in the form of the γ phase is taken to be a1, and the lattice constant of the crystals that compose the precipitation phase in the form of the γ' phase is taken to be a2 then the relationship between a1 and a2 is such that a2 ≤ 0.999a1. Namely, lattice constant a2 of the crystals of the precipitation phase is 00.1% or less lattice constant a1 of the crystals of the matrix.
- In addition, lattice constant a2 of the crystals of the precipitation phase should be -0.5% or more of lattice constant a1 of the crystals of the matrix. In the case both of the lattice constants are in the above relationship, since the precipitation phase precipitates so as to extend continuously in the direction perpendicular to the direction of the load when the precipitation phase precipitates in the matrix due to heat treatment, creep strength can be enhanced without movement of dislocation defects in the alloy structure in the presence of stress.
- In order to make the relationship between lattice constant a1 and lattice constant a2 such that a2 ≤ 0.999a1, the composition of the composite elements that compose the Ni-based single crystal super alloy is suitably adjusted.
- According to the above Ni-based super crystal super alloy, precipitation of the TCP phase, which causes decreased creep strength, during use at high temperatures is inhibited by addition of Ru. In addition, by setting the composite ratios of other composite elements to their optimum ranges, the lattice constant of the matrix (γ phase) and the lattice constant of the precipitation phase (γ' phase) can be made to have optimum values. As a result, creep strength at high temperatures can be improved.
- The effect of the present invention is shown using following embodiments.
- Melts of vaxious Ni-based single crystal super alloys were prepared using a vacuum melting furnace, and alloy ingots were cast using the alloy melts. The composite ratio of the alloy ingot of the present embodiment (TMS-138) is shown in Table 2.
Sample
(alloy name)Elements (wt%) Al Ti Ta Nb Mo W Re C Zr Hf Cr Co Ru Ni Embodiment
(TMS-138)5.9 5.9 2.9 5.9 4.9 0.1 2.9 5.9 2.0 Rem - Next, 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. In addition, aging treatment consisted of consecutively performing primary aging treatment consisting of holding for 4 hours at 1150°C and secondary aging treatment consisting of holding for 20 hours at 870°C.
- As a result, a TCP phase was unable to be confumed in the structure.
- Next, a creep test was performed on a sample of the present embodiment (TMS-138) that underwent solution treatment and aging treatment. The creep test consisted of measuring the time until the sample demonstrated creep rupture as the sample life under each of the temperature and stress conditions shown in Table 3.
Sample
(alloy name)Creep test conditions/rupture life (h) 1173K
(900°C)
392 MPa1273K
(1000°C)
245 MPa1373K
(1100°C)
137 MPa1423K
(1150°C)
98 Mpa1423K
(1150°C)
137 MPaEmbodiment
(TMS-138)986.88 380.50 412.30 343.25 81.47 - As is clear from Table 3, the sample of the present embodiment was determined to have high strength even under high temperature conditions of 1273K (1000°C).
- In addition, the creep rupture characteristics (withstand temperature) were compared for the alloys of the prior art shown in Table 1 (Comparative Examples 1 through 5) and the sample of the present embodiment shown in Table 2 (TMS-138). Creep rupture characteristics were determined either as a result of measuring the temperature until the sample ruptured under conditions of applying stress of 137 MPa for 1000 hours, or converting the rupture temperature of the sample under those conditions.
Sample (alloy name) Withstand temperature (°C) Comparative Example 1 (CMSX-2) 1289K (1016°C) Comparative Example 2 (CMSX-4) 1306K (1033°C) Comparative Example 3 (Rene'N6) 1320K (1047°C) Comparative Example 4 (CMSX-10K) 1345K (1072°C) Comparative Example 5 (3B) 1353K (1080°C) Embodiment (TMS-138) 1356K (1083°C) (Converted to 137 MPa, 1000 hours) - As is clear from Table 4, the sample of the present embodiment was determined to have a high withstand temperature (1356K (1083°C)) equal to or greater than Comparative Examples 1 through 5.
- Thus, this alloy has 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.
- Furthermore, the fatigue strength were compared for the alloys of the Comparative Example 2 shown in Table 1 (CMSX-4) and the sample of the present embodiment shown in Table 2 (TMS-138). In this case, the high cycle fatigue strength (HCF) and the low cycle fatigue strength (LCF) were measured as the fatigue strength. For measuring the high cycle fatigue strength, the max stress at high temperature of 1373K (1100°C) were measured by controlling a load, and the number of fatigue fracture cycle (Nf) were determined as 106 and 107. For measuring the low cycle fatigue strength, the alternative peseudostress at high temperature of 1073K (800°C) were measured by controlling the distortion, and the number of fatigue fracture cycle (Nf) were determined as 103 and 104.
HCF(1373K) LCF(1073K) Max Stress (Mpa) Alt. Pseudostress (Mpa) Nf=106 Nf=107 Nf=103 Nf=104 TMS-138 388 252 833 611 CMSX4 305 238 699 507 - As is clear from Table 5, the sample of the present embodiment was determined to have a fatigue strength greater than Comparative Example 2.
- Therefore, the alloy of the present invention (TMS-138) was determined to have a high fatigue strength in addition to the Creep strength at high temperature compared to the conventional Ni-based single crystal super alloy.
Claims (4)
- An Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-8.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf; 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of its weight ratio, with the remainder consisting ofNi and unavoidable impurities; and characterized in that, when the lattice constant of the matrix is taken to be a1 and t he lattice constant of the precipitation phase is taken to be a2, a2 ≤ 0.999a1.
- An Ni-based single crystal super alloy having a composition consisting of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 1.0-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co, and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities; and characterized in that, 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, a2 ≤ 0.999a1.
- An Ni-based single crystal super alloy according to claim 2, wherein the composition consists of 5.0-7.0 wt% Al, 4.0-6.0 wt% Ta, 2.9-4.5 wt% Mo, 4.0-8.0 wt% W, 3.0-6.0 wt% Re, 0.01-0.50 wt% Hf, 2.0-5.0 wt% Cr, 0.1-5.9 wt% Co and 1.0-4.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities.
- The Ni-based single crystal super alloy according to any of claims 1 through 3 that has a composition consisting of 5.9 wt% Al, 5.9 wt% Ta, 2.9 wt% Mo, 5.9 wt% W, 4.9 wt% Re, 0.10 wt% Hf, 2.9 wt% Cr, 5.9 wt% Co and 2.0 wt% Ru in terms of weight ratio, with the remainder consisting of Ni and unavoidable impurities.
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JP2001161919 | 2001-05-30 | ||
JP2001161919 | 2001-05-30 | ||
JP2002143572 | 2002-05-17 | ||
JP2002143572A JP3840555B2 (en) | 2001-05-30 | 2002-05-17 | Ni-based single crystal superalloy |
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EP1262569A1 EP1262569A1 (en) | 2002-12-04 |
EP1262569A8 EP1262569A8 (en) | 2003-05-21 |
EP1262569B1 true EP1262569B1 (en) | 2005-04-06 |
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US (1) | US20030075247A1 (en) |
EP (1) | EP1262569B1 (en) |
JP (1) | JP3840555B2 (en) |
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US6966956B2 (en) * | 2001-05-30 | 2005-11-22 | National Institute For Materials Science | Ni-based single crystal super alloy |
US8968643B2 (en) * | 2002-12-06 | 2015-03-03 | National Institute For Materials Science | Ni-based single crystal super alloy |
US7273662B2 (en) | 2003-05-16 | 2007-09-25 | Iowa State University Research Foundation, Inc. | High-temperature coatings with Pt metal modified γ-Ni+γ′-Ni3Al alloy compositions |
JP3944582B2 (en) * | 2003-09-22 | 2007-07-11 | 独立行政法人物質・材料研究機構 | Ni-base superalloy |
GB0412584D0 (en) * | 2004-06-05 | 2004-07-07 | Rolls Royce Plc | Composition of matter |
US8221901B2 (en) * | 2005-03-28 | 2012-07-17 | National Institute For Materials Science | Material for heat resistant component |
JP5344453B2 (en) * | 2005-09-27 | 2013-11-20 | 独立行政法人物質・材料研究機構 | Ni-base superalloy with excellent oxidation resistance |
US8123872B2 (en) * | 2006-02-22 | 2012-02-28 | General Electric Company | Carburization process for stabilizing nickel-based superalloys |
JP4773303B2 (en) * | 2006-08-22 | 2011-09-14 | 株式会社日立製作所 | Nickel-based single crystal superalloy excellent in strength, corrosion resistance, and oxidation resistance and method for producing the same |
EP2062990B1 (en) * | 2006-09-13 | 2016-01-13 | National Institute for Materials Science | Ni-BASE SINGLE CRYSTAL SUPERALLOY |
CN101680059B (en) * | 2007-03-12 | 2011-07-06 | 株式会社Ihi | Ni-based single crystal superalloy and turbine vane using the same |
JP5467307B2 (en) | 2008-06-26 | 2014-04-09 | 独立行政法人物質・材料研究機構 | Ni-based single crystal superalloy and alloy member obtained therefrom |
JP5467306B2 (en) | 2008-06-26 | 2014-04-09 | 独立行政法人物質・材料研究機構 | Ni-based single crystal superalloy and alloy member based thereon |
US8821654B2 (en) | 2008-07-15 | 2014-09-02 | Iowa State University Research Foundation, Inc. | Pt metal modified γ-Ni+γ′-Ni3Al alloy compositions for high temperature degradation resistant structural alloys |
US20100135846A1 (en) | 2008-12-01 | 2010-06-03 | United Technologies Corporation | Lower cost high strength single crystal superalloys with reduced re and ru content |
US20160214350A1 (en) | 2012-08-20 | 2016-07-28 | Pratt & Whitney Canada Corp. | Oxidation-Resistant Coated Superalloy |
US8858876B2 (en) | 2012-10-31 | 2014-10-14 | General Electric Company | Nickel-based superalloy and articles |
DE102016203724A1 (en) * | 2016-03-08 | 2017-09-14 | Siemens Aktiengesellschaft | SX-nickel alloy with improved TMF properties, raw material and component |
TWI663263B (en) * | 2016-11-25 | 2019-06-21 | 國家中山科學研究院 | High creep-resistant equiaxed grain nickel-based superalloy |
CN112522543A (en) * | 2020-11-18 | 2021-03-19 | 贵州工程应用技术学院 | High-concentration Re/Ru high-temperature-bearing-capacity high-creep-resistance nickel-based single crystal superalloy |
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US4719080A (en) * | 1985-06-10 | 1988-01-12 | United Technologies Corporation | Advanced high strength single crystal superalloy compositions |
CA1315572C (en) * | 1986-05-13 | 1993-04-06 | Xuan Nguyen-Dinh | Phase stable single crystal materials |
US5151249A (en) * | 1989-12-29 | 1992-09-29 | General Electric Company | Nickel-based single crystal superalloy and method of making |
US5482789A (en) * | 1994-01-03 | 1996-01-09 | General Electric Company | Nickel base superalloy and article |
US6007645A (en) * | 1996-12-11 | 1999-12-28 | United Technologies Corporation | Advanced high strength, highly oxidation resistant single crystal superalloy compositions having low chromium content |
JPH11256258A (en) * | 1998-03-13 | 1999-09-21 | Toshiba Corp | Ni base single crystal superalloy and gas turbine parts |
JPH11310839A (en) * | 1998-04-28 | 1999-11-09 | Hitachi Ltd | Grain-oriented solidification casting of high strength nickel-base superalloy |
FR2780983B1 (en) * | 1998-07-09 | 2000-08-04 | Snecma | SINGLE-CRYSTAL NICKEL-BASED SUPERALLOY WITH HIGHER TEMPERATURE RESISTANCE |
JP4028122B2 (en) * | 1999-02-25 | 2007-12-26 | 独立行政法人物質・材料研究機構 | Ni-base superalloy, manufacturing method thereof, and gas turbine component |
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 |
US6673308B2 (en) * | 2000-08-30 | 2004-01-06 | Kabushiki Kaisha Toshiba | Nickel-base single-crystal superalloys, method of manufacturing same and gas turbine high temperature parts made thereof |
-
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- 2002-05-17 JP JP2002143572A patent/JP3840555B2/en not_active Expired - Lifetime
- 2002-05-29 DE DE60203562T patent/DE60203562T2/en not_active Expired - Lifetime
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- 2002-05-29 EP EP02253782A patent/EP1262569B1/en not_active Expired - Lifetime
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JP3840555B2 (en) | 2006-11-01 |
EP1262569A8 (en) | 2003-05-21 |
EP1262569A1 (en) | 2002-12-04 |
JP2003049231A (en) | 2003-02-21 |
CA2387828C (en) | 2009-09-15 |
DE60203562T2 (en) | 2006-02-09 |
DE60203562D1 (en) | 2005-05-12 |
US20030075247A1 (en) | 2003-04-24 |
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