CN115466881A - Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof - Google Patents
Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof Download PDFInfo
- Publication number
- CN115466881A CN115466881A CN202211220099.7A CN202211220099A CN115466881A CN 115466881 A CN115466881 A CN 115466881A CN 202211220099 A CN202211220099 A CN 202211220099A CN 115466881 A CN115466881 A CN 115466881A
- Authority
- CN
- China
- Prior art keywords
- single crystal
- alloy
- temperature
- based single
- crystal superalloy
- 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.)
- Pending
Links
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 79
- 239000013078 crystal Substances 0.000 title claims abstract description 59
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 35
- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 33
- 238000002360 preparation method Methods 0.000 title claims abstract description 5
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 70
- 239000000956 alloy Substances 0.000 claims abstract description 70
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 13
- 230000002045 lasting effect Effects 0.000 claims abstract description 3
- 230000015572 biosynthetic process Effects 0.000 claims description 17
- 238000001816 cooling Methods 0.000 claims description 15
- 230000032683 aging Effects 0.000 claims description 14
- 238000003723 Smelting Methods 0.000 claims description 12
- 238000010438 heat treatment Methods 0.000 claims description 12
- 239000002994 raw material Substances 0.000 claims description 8
- 239000000126 substance Substances 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 6
- 230000006698 induction Effects 0.000 claims description 6
- 230000002401 inhibitory effect Effects 0.000 claims description 6
- 238000010187 selection method Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 5
- 238000007711 solidification Methods 0.000 claims description 5
- 230000008023 solidification Effects 0.000 claims description 5
- 238000005303 weighing Methods 0.000 claims description 5
- 230000001737 promoting effect Effects 0.000 claims description 4
- 238000001556 precipitation Methods 0.000 description 11
- 238000005728 strengthening Methods 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 229910052702 rhenium Inorganic materials 0.000 description 5
- 229910052707 ruthenium Inorganic materials 0.000 description 5
- 229910000995 CMSX-10 Inorganic materials 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 230000003647 oxidation Effects 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 229910001012 TMS-138 Inorganic materials 0.000 description 3
- 238000004220 aggregation Methods 0.000 description 3
- 230000002776 aggregation Effects 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical group [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 2
- 230000002195 synergetic effect Effects 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- 206010014970 Ephelides Diseases 0.000 description 1
- 208000003351 Melanosis Diseases 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000002815 nickel Chemical class 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
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%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Abstract
The invention discloses a fourth generation nickel-based single crystal superalloy with high structure stability. After the microscopic structure is aged for 1000 hours at the high temperature of 1100 ℃ for a long time, the content of precipitated TCP phase is less than 0.5 percent (area fraction). Due to good structure stability, the alloy has a lasting life of more than 450h in the environment of 1100 ℃/137MPa, and has excellent high-temperature performance. The components by weight are as follows: co:7 to 12%, al:5.5 to 6.5 percent, cr:1.8 to 3.3%, W:5.5 to 6.5%, mo:1.7 to 3.2%, re:3.8 to 5%, ta:5.5 to 7 percent, hf:0.1 to 0.3%, ru:1.5 to 2.7 percent, and the balance of Ni. The invention also discloses a preparation method of the alloy, which is relatively easy to implement.
Description
Technical Field
The invention belongs to the field of component design of nickel-based single crystal superalloy, and particularly relates to a fourth-generation nickel-based single crystal superalloy with high structure stability, which is mainly suitable for manufacturing hot-end high-temperature components in the fields of aviation, aerospace and energy.
Technical Field
The nickel-based single crystal superalloy is a main material of turbine blades in aircraft aeroengines in China, and has excellent creep resistance, thermal corrosion resistance, fatigue resistance and the like. These excellent properties result from a homogeneous gamma/gamma prime two-phase structure in the alloy. However, in a long-term service environment, a brittle and hard topological close-packed phase, referred to as a TCP phase for short, is often precipitated in the alloy structure. The TCP phase is harmful in two aspects, one is that its formation consumes a large amount of refractory elements (such as Re, W, mo, cr, etc.), greatly reducing the solid solution strengthening effect; secondly, because it is hard and brittle, and a gamma-phase depletion region is often formed around the TCP phase, the complete gamma/gamma' structure is destroyed, so that the local strength of the alloy is reduced, and the alloy is easy to become the starting point of crack initiation.
Along with the continuous improvement of the generation of nickel-based single crystal superalloy, the temperature bearing capacity of the alloy is continuously improved. But with increasing refractory element content in the alloy (e.g., re, W, mo and Ta), as exemplified by the CMSX series, from 14.6wt.% for the first generation to 20.7wt.% for the third generation, this results in a significantly increased tendency for TCP phase precipitation in the alloy. In order to stabilize the structure and inhibit the precipitation of the TCP phase, the fourth generation nickel-based single crystal superalloy has good effect of inhibiting the TCP phase by adding platinum group elements such as Ru, but the density and the cost of the alloy are greatly improved by adding Ru. The invention designs a novel nickel-based single crystal superalloy with high Co content, which improves the structural stability and reduces the use of Ru while maintaining the performance, thereby being beneficial to the low-cost and low-density design of the alloy.
Disclosure of Invention
The invention aims to provide a fourth generation nickel-based single crystal superalloy with small tendency of TCP phase precipitation and high structure stability, which is based on the double inhibition effect of Co and Ru on the TCP phase and combines the strengthening effect of refractory elements such as Re, W, cr, ta and the like, thereby ensuring good creep resistance, fatigue resistance and other properties and ensuring good structure stability of the alloy at high temperature.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
a fourth generation nickel base single crystal superalloy with high structure stability comprises the following chemical components in percentage by weight: co:7 to 12%, al:5.5 to 6.5 percent, cr:1.8 to 3.3%, W:5.5 to 6.5%, mo:1.7 to 3.2%, re:3.8 to 5%, ta:5.5 to 7 percent, hf:0.1 to 0.3%, ru:1.5 to 2.7 percent, and the balance of Ni.
In the nickel-based single crystal superalloy, the content of Cr + Re + W + Mo which is an element promoting formation of a TCP phase is more than or equal to 16wt.%, and the content of Co + Ru which is an element inhibiting formation of the TCP phase is more than or equal to 8.5wt.%.
After the nickel-based single crystal superalloy is subjected to thermal exposure for 1000 hours at the medium temperature of 970 ℃ and the high temperature of 1100 ℃, the area fraction of a TCP phase precipitated in the alloy is less than or equal to 0.5 percent.
The preferable nickel-based single crystal superalloy has the lasting life of more than or equal to 450h under the conditions of 1100 ℃ and 137 MPa.
The preparation method of the nickel-based single crystal superalloy comprises the following steps:
1) Smelting a master alloy: weighing the raw materials according to the weight percentage of the raw materials in the claim 2, then smelting in a vacuum induction smelting furnace, and then casting into a master alloy;
2) Preparing a single crystal: remelting mother alloy by utilizing directional solidification equipment, and preparing a single crystal rod by adopting a spiral crystal selection method, wherein the temperature gradient is 40-70K/cm and the drawing speed is 50-150 mu m/s.
3) Solution heat treatment: keeping the temperature at 1305-1320 ℃ for 2-4 h, then heating to 1325-1332 ℃ and keeping the temperature for 2-4 h, then heating to 1335-1345 ℃ and keeping the temperature for 10-16 h, and then air cooling to room temperature; high-temperature aging treatment:
preserving the heat for 3 to 6 hours at the temperature of 1080 to 1110 ℃, and then cooling the mixture to room temperature in air; and (3) low-temperature aging treatment: at 850-890 deg.C
Preserving the temperature for 15-20 h, and then cooling the mixture to room temperature in air;
the chemical composition design of the invention is mainly based on the following:
in order to increase the use temperature of the alloy and to increase the strength of the alloy at high temperatures, it is necessary to add certain solid solution strengthening elements such as Mo, W, and Re, and to ensure the oxidation resistance at high temperatures, it is necessary to contain certain Cr elements, which are also TCP phase-forming elements. However, although Cr can improve the hot corrosion resistance and oxidation resistance of the alloy, a large amount of Cr is added to easily destabilize the structure, so the amount is set to 1.8 to 3.3wt.%; mo can improve the mismatching degree between gamma/gamma', so that a dense dislocation network is formed in the alloy, and the creep resistance is increased, but the Mo belongs to a strong TCP phase forming element and is not suitable for being added in excess, so the Mo is set to be 1.7-3.2 wt%; w is also a solid solution strengthening element, but about half of W is distributed in a gamma' phase, so that a matrix and a strengthening phase can be simultaneously strengthened, and the high-temperature strength of the alloy is improved. Therefore, the content of Mo can be properly increased compared with Mo, and the content is set as follows: 5.5-6.5 wt.%. Re is used as a strong solid solution strengthening element, which not only strengthens a matrix in the alloy, but also drags the diffusion of other elements due to the extremely low diffusion coefficient, thereby effectively reducing the coarsening rate of a gamma' phase and greatly improving the creep resistance of the alloy. However, re is a strong TCP phase-forming element and is expensive (>2 ten thousand yuan/kg) and a higher density (21 g/cm) 3 ) Since it is not preferable to add it excessively, re: 3.8-5 wt.%.
As a fourth generation nickel-based single crystal superalloy, in order to guarantee the high-temperature durability of the alloy, the solid solution strengthening elements Cr + Re + W + Mo are more than or equal to 16 wt%, and are higher than the third generation nickel-based single crystal superalloy TMS-75, CMSX-10 and Ren N6. For example, in CMSX-10, cr + Re + W + Mo =13.4wt.%, which has caused the alloy to precipitate more than 1.5% (area fraction) of the TCP phase after 1000h ageing at 1050 ℃. Therefore, in order to stabilize the structure, the present alloy improves the structure stability by the synergistic action of Ru and Co, and reduces the tendency of TCP phase precipitation.
Ru is one of platinum group elements and serves as a marking element of the fourth generation nickel-based single crystal superalloy, and not only plays a certain role in solid solution strengthening, but also has a plurality of researches which show that Ru can reduce the aggregation degree of Re in a matrix through an 'inverse distribution' effect or increase the solubility of elements such as Re in the matrix, so that the Ru can reduce the aggregation degree of Re in the matrix or increase the solubility of Re and the likeThe purpose of reducing the tendency of TCP phase precipitation is achieved. However, ru is expensive at a price of up to 16 ten thousand yuan/kg and has a density of 12.2g/cm 3 Much higher than the matrix Ni and therefore should not be added in excess, so its content is set to Ru: 1.5-2.7 wt.%. According to a plurality of reports, like Ru, co can also reduce the aggregation degree of TCP phase forming elements such as Re, mo, W and Cr in a matrix through an 'inverse distribution' effect; meanwhile, other harmful TCP phase precipitation can be prevented by inhibiting sigma phase nucleation. Through the synergistic effect of Ru and Co, the nucleation energy and the critical nucleation radius of the TCP phase are increased from the thermodynamics and the kinetics, and the nucleation rate and the growth rate of the TCP are reduced, so that the precipitation content of the TCP phase is reduced, and the tissue stability is improved. Further, the density of Co was 8.9g/cm 3 Is slightly lower than the matrix Ni, which is beneficial to the light weight of the alloy; the price of Co is about 300 yuan/kg and is far lower than that of Ru, and the Co is used for replacing part of Ru, so that the cost is reduced. On the other hand, excessive addition of Co tends to lower the γ' phase dissolution temperature, and is detrimental to the high temperature performance of the alloy, and the amount of Co should be added in an amount sufficient to suppress the TCP phase, so that the Co content is set as follows: co: 7-12 wt.%. Therefore, the Co + Ru content is set to be more than or equal to 8.5wt.%, and the alloy can be ensured to have good structure stability at high temperature.
Al and Ta are main forming elements of a strengthening phase gamma 'phase, and the Al can ensure the content of the gamma' phase in the alloy and can increase the oxidation resistance of the alloy. Ta can not only strengthen the gamma 'phase and increase the content of the gamma' phase, but also can inhibit the formation of defects such as freckles and the like in the casting process of the alloy. In order to ensure that the content of the gamma' phase is 60-70% (volume fraction) and also consider factors such as a heat treatment window, structure stability and the like, the content of Al is set to be 5.5-6.5 wt.%, and the content of Ta is set to be 5.5-7 wt.%. In addition, to further improve the castability and oxidation resistance of the alloy, 0.1 to 0.3wt.% of Hf is added (excessive Hf tends to lower the initial melting temperature of the alloy).
The alloy is cast into mother alloy by adopting a vacuum induction melting furnace as a raw material, and then is prepared into single crystal by a spiral crystal selection method (the temperature gradient of a single crystal furnace is 40-70K/cm, the drawing speed is 50-150 mu m/s), and the alloy needs to be subjected to heat treatment before use.
The invention has the following beneficial effects:
(1) Compared with the third generation and other fourth generation nickel-based single crystal alloys, the alloy has higher structural stability, lower tendency of TCP phase precipitation, and less than or equal to 0.5 percent (area fraction) of the content of the precipitated TCP phase after 1000 hours of aging at 1100 ℃.
(2) Compared with other fourth generation nickel base single crystal alloys, the alloy has excellent durability, and the durable service life of the alloy reaches more than 450h at 1100 ℃/137 MPa.
(3) The invention has lower content of the noble metals Re and Ru and effectively reduces the cost of the alloy.
Drawings
FIG. 1 is a typical as-heat treated microstructure of a nickel-based single crystal superalloy according to example 1 of the present invention;
FIG. 2 shows the microstructure of the nickel-based single crystal superalloy of example 1 after aging at 1100 ℃ for 1000 hours.
FIG. 3 shows the microstructure of the nickel-based single crystal superalloy of example 2 of the present invention after aging at 1100 ℃ for 1000 hours.
FIG. 4 shows the microstructure of the nickel-based single crystal superalloy of example 3 after aging at 1100 ℃ for 1000 hours
FIG. 5 is the microstructure of the nickel-based single crystal superalloy of comparative example 2TMS-138 after aging for 1000 hours at 1100 ℃.
Detailed Description
The present invention is further illustrated by the following examples, which are not intended to limit the scope of the invention.
Example 1:
a fourth generation nickel-based single crystal superalloy with high structure stability comprises the following chemical components in percentage by weight: co:7%, al:6.1%, cr:2.9%, W:5.8%, mo:3.0%, re:4.4%, ta:6.0%, hf:0.15%, ru:2.0 percent and the balance of Ni. It has a content of elements inhibiting the formation of TCP phases Co + Ru =9%, it promotes a content of TCP phase forming elements Cr + Re + W + Mo =16.1%.
Example 1 alloy manufacturing method: weighing the raw materials according to the weight percentage of the alloy, smelting in a vacuum induction smelting furnace, and then casting to obtain a master alloy; preparing a single crystal: remelting mother alloy by utilizing directional solidification equipment, preparing a single crystal rod by adopting a spiral crystal selection method, and pulling the single crystal rod by adopting a temperature gradient of 45K/cm and a pulling speed of 60 mu m/s.
The pulled single crystal rod is subjected to the following heat treatment: 1310 ℃/2h +1328 ℃/4h +1345 ℃/14h + air cooling → 1110 ℃/5h + air cooling → 865 ℃/17h + air cooling.
FIG. 1 shows the microstructure of example 1 in a heat-treated state. As can be seen from fig. 1, after the above heat treatment procedure, a highly cubic, fine and uniformly distributed gamma' phase is obtained, which has a content of about 68.3% (volume fraction) in the dendrite dry region and a size of about 213nm. The good matching of the gamma' phase and the gamma phase is the key of the long-term performance of the alloy at high temperature.
As shown in FIG. 2, the microstructure of the alloy of example 1 after aging at 1100 ℃ for 1000h, the precipitated TCP phase content is about 0.3%, which is less than 0.5% of the claimed content.
Example 2:
a fourth generation nickel-based single crystal superalloy with high structure stability comprises the following chemical components in percentage by weight: co:8.0%, al:5.8%, cr:3.0%, W:6.1%, mo:2.6%, re:4.9%, ta:6.0%, hf:0.22%, ru:2.6 percent and the balance of Ni. The content of elements that inhibit the formation of the TCP phase Co + Ru =10.6%, and the content of elements that promote the formation of the TCP phase Cr + Re + W + Mo =16.6%.
Example 2 manner of manufacturing alloy: weighing the raw materials according to the weight percentage of the alloy, smelting in a vacuum induction smelting furnace, and then casting to obtain a master alloy; preparing a single crystal: remelting mother alloy by utilizing directional solidification equipment, preparing a single crystal rod by adopting a spiral crystal selection method, and pulling the single crystal rod by adopting a temperature gradient of 60K/cm and a pulling speed of 110 mu m/s.
The pulled single crystal rod is subjected to the following heat treatment: 1320 ℃/4h +1325 ℃/3h +1340 ℃/16h + air cooling → 1090 ℃/6h + air cooling → 880 ℃/18h + air cooling.
As shown in FIG. 3, the microstructure of the alloy of example 2 after aging for 1000h at 1100 ℃, no precipitated TCP phase is found in the structure, i.e. the precipitation of the TCP phase is further inhibited by the increase of the content of Co + Ru (element for inhibiting the precipitation of the TCP phase).
Example 3:
a fourth generation nickel-based single crystal superalloy with high structure stability comprises the following chemical components in percentage by weight: co:11.6%, al:5%, cr:3.2%, W:6.5%, mo:3.1%, re:5.0%, ta:6.5%, hf:0.3%, ru:1.7 percent and the balance of Ni. The content of elements that inhibit the formation of the TCP phase Co + Ru =13.3%, and the content of elements that promote the formation of the TCP phase Cr + Re + W + Mo =17.8%.
Example 3 alloy manufacturing method: weighing the raw materials according to the weight percentage of the alloy, smelting in a vacuum induction smelting furnace, and then casting into a master alloy; preparing a single crystal: remelting mother alloy by utilizing directional solidification equipment, preparing a single crystal rod by adopting a spiral crystal selection method, and pulling the single crystal rod by adopting a temperature gradient of 55K/cm and a pulling speed of 100 mu m/s.
The pulled single crystal rod is subjected to the following heat treatment: 1305 ℃/3h +1330 ℃/4h +1342 ℃/12h + air cooling → 1100 ℃/5h + air cooling → 870 ℃/20h + air cooling.
As shown in FIG. 4, which is the microstructure morphology of the alloy of example 3 after aging at 1100 ℃ for 1000 hours, no precipitation of TCP phase was observed in the structure, and although the content of the element promoting formation of TCP phase was increased and the content of Ru was decreased, the increase of Co content suppressed the TCP phase.
Comparative example 1:
the third generation nickel-based single crystal superalloy CMSX-10 comprises the following chemical components in percentage by weight: co:3%, al:5.7%, cr:2%, W:5.0%, mo:0.4%, re:6.0%, ta:8.0%, ti:0.2%, nb:0.1% and the balance Ni. It has a content of elements that inhibit the formation of the TCP phase Co + Ru =3%, and it has a content of elements that promote the formation of the TCP phase Cr + Re + W + Mo =13.4%.
Comparative example 2:
the fourth-generation nickel-based single crystal superalloy TMS-138 comprises the following chemical components in percentage by weight: co:5.8%, al:5.8%, cr:2.8%, W:6.1%, mo:2.9%, re:5.1%, ta:5.6%, hf:0.1%, ru:1.9% and the balance Ni. The content of elements that inhibit the formation of the TCP phase Co + Ru =7.7%, and the content of elements that promote the formation of the TCP phase Cr + Re + W + Mo =16.9%.
As shown in FIG. 5, in the microstructure of the alloy of comparative example 2 after aging at 1100 ℃ for 1000 hours, it was found that a large amount of TCP phase (about 3.5%) was precipitated from the microstructure, which was similar to example 2 in the content of the element promoting formation of the TCP phase, but the content of the TCP phase was much larger than that of example 2.
Table 1 shows the endurance life of the alloys of the examples and comparative examples at 1100 deg.C/137 MPa.
| Alloy (I) | Long service life (hours) |
| Example 1 | 472 |
| Example 2 | 519 |
| Example 2 | 461 |
| Comparative example CMSX-10 | 220 |
| Comparative example No. two TMS-138 | 399 |
As shown in Table 1, the alloy of the invention has obviously improved endurance life at 1100 ℃/137MPa compared with the third generation, and has slightly improved endurance life compared with the same generation of alloy TMS-138. The invention is suitable for the application of hot end parts such as advanced thrust-weight ratio aero-engines and the like due to excellent structure stability and higher temperature bearing capacity.
Claims (3)
1. A fourth generation nickel base single crystal superalloy with high structure stability is characterized in that: the nickel-based single crystal superalloy has a lasting life of more than or equal to 450h in an environment of 1100 ℃/137 MPa. By weight, the content of elements Cr + Re + W + Mo for promoting the formation of the TCP phase is more than or equal to 16%, the content of elements Co + Ru for inhibiting the formation of the TCP phase is more than or equal to 8.5%, and the area fraction of the TCP phase precipitated in the alloy is less than or equal to 0.5% after the alloy is aged for 1000 hours at 1100 ℃.
2. A fourth generation nickel based single crystal superalloy with high structural stability according to claim 1, wherein: the alloy comprises the following chemical components in percentage by weight: co:7 to 12%, al:5.5 to 6.5 percent, cr:1.8 to 3.3%, W:5.5 to 6.5%, mo:1.7 to 3.2%, re:3.8 to 5%, ta:5.5 to 7 percent, hf:0.1 to 0.3%, ru:1.5 to 2.7 percent, and the balance of Ni.
3. A fourth generation nickel based single crystal superalloy with high structural stability according to claim 1 or 2, wherein: the preparation method of the nickel-based single crystal superalloy comprises the following steps:
1) Smelting a master alloy: weighing the raw materials according to the weight percentage of the raw materials in the claim 2, then smelting in a vacuum induction smelting furnace, and then casting into a master alloy;
2) Preparing a single crystal: remelting mother alloy by utilizing directional solidification equipment, and preparing a single crystal rod by adopting a spiral crystal selection method, wherein the temperature gradient is 40-70K/cm and the drawing speed is 50-150 mu m/s.
3) Solution heat treatment: preserving heat for 2-4 h at 1305-1320 ℃, then heating to 1325-1332 ℃, preserving heat for 2-4 h, then heating to 1335-1345 ℃, preserving heat for 10-16 h, and then air cooling to room temperature; high-temperature aging treatment: preserving the heat for 3 to 6 hours at the temperature of 1080 to 1110 ℃, and then cooling the mixture to room temperature in air; and (3) low-temperature aging treatment: keeping the temperature for 15 to 20 hours at 850 to 890 ℃, and then cooling the mixture to room temperature in air.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211220099.7A CN115466881A (en) | 2022-09-30 | 2022-09-30 | Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211220099.7A CN115466881A (en) | 2022-09-30 | 2022-09-30 | Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN115466881A true CN115466881A (en) | 2022-12-13 |
Family
ID=84335125
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202211220099.7A Pending CN115466881A (en) | 2022-09-30 | 2022-09-30 | Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115466881A (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050051242A1 (en) * | 2001-05-30 | 2005-03-10 | Yutaka Koizumi | Ni-based single crystal super alloy |
| WO2008111585A1 (en) * | 2007-03-12 | 2008-09-18 | Ihi Corporation | Ni-BASED SINGLE CRYSTAL SUPERALLOY AND TURBINE VANE USING THE SAME |
| CN106636759A (en) * | 2017-01-05 | 2017-05-10 | 中国科学院金属研究所 | Platinum group element reinforced high-thermal stability and high-strength nickel-based single-crystal high-temperature alloy |
| CN111961920A (en) * | 2020-08-09 | 2020-11-20 | 浙江大学 | Nickel-based single crystal superalloy with high temperature bearing capacity and preparation method thereof |
| CN114250518A (en) * | 2021-12-30 | 2022-03-29 | 苏州高晶新材料科技有限公司 | Nickel-based single crystal superalloy and preparation method thereof |
-
2022
- 2022-09-30 CN CN202211220099.7A patent/CN115466881A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050051242A1 (en) * | 2001-05-30 | 2005-03-10 | Yutaka Koizumi | Ni-based single crystal super alloy |
| WO2008111585A1 (en) * | 2007-03-12 | 2008-09-18 | Ihi Corporation | Ni-BASED SINGLE CRYSTAL SUPERALLOY AND TURBINE VANE USING THE SAME |
| CN106636759A (en) * | 2017-01-05 | 2017-05-10 | 中国科学院金属研究所 | Platinum group element reinforced high-thermal stability and high-strength nickel-based single-crystal high-temperature alloy |
| CN111961920A (en) * | 2020-08-09 | 2020-11-20 | 浙江大学 | Nickel-based single crystal superalloy with high temperature bearing capacity and preparation method thereof |
| CN114250518A (en) * | 2021-12-30 | 2022-03-29 | 苏州高晶新材料科技有限公司 | Nickel-based single crystal superalloy and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103382536A (en) | Fourth-generation single-crystal high temperature alloy with high strength and stable structure and preparation method thereof | |
| CN111455220B (en) | Third-generation nickel-based single crystal superalloy with stable structure and preparation method thereof | |
| CN106756249A (en) | A kind of nickel-base high-temperature single crystal alloy of high intensity and tissue stabilization and preparation method thereof | |
| CN106636759B (en) | A kind of high thermal stability high-strength nickel based single-crystal high-temperature alloy that platinum family element is strengthened | |
| CN106011540B (en) | Low-rhenium third-generation nickel-based single crystal alloy and preparation method thereof | |
| CN105506387A (en) | High-specific-creep-strength nickel base single crystal high-temperature alloy and preparation method and application thereof | |
| CN111961920B (en) | Nickel-based single crystal superalloy with high temperature bearing capacity and preparation method thereof | |
| CN100430500C (en) | Third nickel-base high-temperature single crystal alloy in low cost | |
| CN102418147A (en) | High strength and completely antioxidative third generation monocrystalline high temperature alloy and preparation method thereof | |
| CN114686731B (en) | Single crystal high temperature alloy and preparation method and application thereof | |
| CN103173865B (en) | A kind of Low-cost nickel-base single crystal high-temperature alloy and preparation method thereof | |
| CN109136654A (en) | A kind of low rhenium corrosion and heat resistant long-life high intensity second generation nickel-base high-temperature single crystal alloy and its heat treatment process | |
| CN105296809B (en) | A kind of high intensity precipitation strength cobalt-based single crystal super alloy and preparation method thereof | |
| CN112853156B (en) | High-structure-stability nickel-based high-temperature alloy and preparation method thereof | |
| CN114164356B (en) | High-strength nickel-based single crystal superalloy | |
| CN114164357B (en) | Low-cost low-density nickel-based single crystal superalloy | |
| CN104911407A (en) | Re/Ru-containing monocrystal nickel-based superalloy with high temperature resistant capability and high creep resistance | |
| CN115011844B (en) | Rhenium-containing tungsten-free low-specific gravity nickel-based single crystal superalloy and heat treatment process thereof | |
| CN111379028A (en) | Ni-Al binary single crystal alloy, Ni-Al binary model single crystal alloy and preparation method thereof | |
| CN115466881A (en) | Fourth-generation nickel-based single crystal superalloy with stable structure and preparation method thereof | |
| CN112176224A (en) | High-strength nickel-based single crystal superalloy with excellent comprehensive performance | |
| JP2000239771A (en) | Ni BASE SUPERALLOY, ITS PRODUCTION AND GAS TURBINE PARTS | |
| CN112746328B (en) | Single crystal high temperature alloy with low density and excellent hot corrosion resistance and preparation process thereof | |
| CN113913942A (en) | Nickel-based single crystal alloy, use and heat treatment method | |
| CN101008059A (en) | Rhenium-free nickel base single crystal high-temperature alloy material |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20221213 |