CN112593122A - Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy - Google Patents
Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy Download PDFInfo
- Publication number
- CN112593122A CN112593122A CN202011449792.2A CN202011449792A CN112593122A CN 112593122 A CN112593122 A CN 112593122A CN 202011449792 A CN202011449792 A CN 202011449792A CN 112593122 A CN112593122 A CN 112593122A
- Authority
- CN
- China
- Prior art keywords
- alloy
- single crystal
- less
- equal
- long
- 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.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
Abstract
The invention discloses a long-life high-strength hot corrosion resistant single crystal superalloy, and belongs to the technical field of nickel-based single crystal superalloys. The alloy comprises the following chemical components (wt.%): cr: 10-12%, Co: 4-6%, Mo: 0-0.5%, W: 5-7%, Ta: 6-8%, Al: 3.5-4.5%, Ti: 3.5-4.5%, C: 0-0.1%, Hf: 0 to 0.2%, and the balance of Ni, wherein Ta/(W +2Mo) is 1 to 1.1. The alloy not only has excellent dynamic and static structure stability, but also has better heat-resisting corrosion resistance and oxidation resistance, and higher high-temperature mechanical property. The high-temperature component can be suitable for high-temperature components of gas turbines used on the ground and in ships, and can also be suitable for high-temperature components of aircraft engines in service in offshore and oceanic environments.
Description
Technical Field
The invention belongs to the technical field of nickel-based single crystal superalloy, and particularly relates to a long-life high-strength hot corrosion resistant single crystal superalloy, which is mainly suitable for long-life single crystal superalloy components serving in a high-temperature hot corrosion environment.
Background
The development of the scientific and technological fields of offshore long-life aircraft engines, next-generation ship gas turbines, ground gas turbines and the like requires that high-temperature alloy materials used for turbine blades of engines have excellent high-temperature structure stability and good heat corrosion resistance. Meanwhile, the high-temperature mechanical property of the alloy is required to be obviously superior to that of the first generation single crystal high-temperature alloy. However, it should be noted that the space for designing the composition of such an alloy is extremely narrow.
At present, the hot corrosion resistant nickel-based single crystal superalloy developed in China mainly comprises DD8, DD10 and the like, and the alloys have good hot corrosion resistant performance, but the strength of the alloys can not reach the level of the second generation single crystal superalloy at home and abroad. In addition, the second generation high-strength nickel-based single crystal superalloy developed in China mainly comprises DD6, DD5 and the like, but the alloys have high cost (containing 2-3% of Re), and relatively poor long-term structure stability and hot corrosion resistance. Therefore, at present, the types of hot corrosion resistant single crystal alloys having a long life and high strength are very few in China.
Against the background, it is desired to obtain a Re-free long-life high-strength hot-corrosion-resistant single crystal superalloy having good hot corrosion resistance, high-temperature mechanical properties, and excellent dynamic and static structure stability.
Disclosure of Invention
The invention aims to provide a long-life high-strength hot corrosion resistant single crystal superalloy which has good hot corrosion resistance and long-term structure stability and also has mechanical properties obviously superior to those of a typical first-generation hot corrosion resistant single crystal superalloy.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
the long-life high-strength hot corrosion resistant single crystal high temperature alloy comprises the following chemical components in percentage by weight:
cr: 10-12%, Co: 4-6%, Mo: 0-0.5%, W: 5-7%, Ta: 6-8%, Al: 3.5-4.5%, Ti: 3.5-4.5%, C: 0-0.1%, Hf: 0-0.2%, and the balance of Ni.
The long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy provided by the invention comprises the following preferred alloy components in percentage by weight:
cr: 11.2-11.8%, Co: 4.5-5.5%, Mo: 0.2-0.4%, W: 5.7-6.3%, Ta: 6.7-7.3%, Al: 3.8-4.2%, Ti: 3.8-4.2%, C: 0.04-0.08%, Hf: 0.05-0.15% and the balance of Ni.
The alloy comprises the chemical components of 1-1.1 weight percent of Ta/(W +2Mo) and Nv≤2.4。
In the chemical components of the long-life high-strength thermal corrosion resistant single crystal superalloy provided by the invention, the mass percentage of impurity elements meets the following requirements: o is less than or equal to 0.001, N is less than or equal to 0.001, S is less than or equal to 0.001, Zr is less than or equal to 0.0075, Mn is less than or equal to 0.01, Si is less than or equal to 0.1, P is less than or equal to 0.005, Cu is less than or equal to 0.05, Mg is less than or equal to 0.008, Se is less than or equal to 0.0003, Pb is less than or equal to 0.0002, Te is less than or equal to 0.00005, Bi is less than or.
The chemical composition design of the alloy (alloy brand is named as DD413M) is mainly based on the following reasons:
the most obvious feature of hot corrosion resistant nickel-based single crystal superalloys is that they contain relatively high Cr (typically greater than 12 wt.%) to ensure excellent hot corrosion resistance. Under the condition of hot corrosion, Cr is oxidized to form Cr2O3And the alloy matrix is protected from being corroded by molten salt. In addition, Cr can capture sulfur entering the alloy matrix to generate solid CrS, prevent the sulfur from further diffusing into the matrix or generate liquid nickel sulfide. However, the solid solution strengthening effect of Cr is small, and the addition of other solid solution strengthening elements (W, Mo, Ta, Re and the like) is limited by the high Cr content, otherwise, TCP harmful phases can appear in the alloy to cause performance deterioration. Therefore, the high-strength heat-corrosion-resistant single crystal alloy needs to reduce the Cr content properly in the aspect of component design, and the Cr content is 10-12%.
Mo and W are the most important solid solution strengthening elements in the high-temperature alloy, but both of them are elements for promoting the formation of a TCP phase, and are very disadvantageous to the structural stability of the alloy. W, Mo is easy to form volatile oxide in high temperature oxidation environment, and is difficult to form dense oxide film in the presence of Na2SO4In the environment of (2), acid melting reaction is easily caused, severe hot corrosion is generated, and particularly, catastrophic corrosion often occurs on high-Mo alloy. Therefore, the content of Mo in the high-strength heat-corrosion-resistant single crystal alloy is 0-0.5%, and the content of W in the high-strength heat-corrosion-resistant single crystal alloy is 5-7%.
Ta can effectively improve the hot corrosion resistance of the alloy. This is because the increase in Ta content promotes the alloy solid NaTaO3Generation of liquid Na is suppressed2(Mo,W)O4The formation of the alloy and the occurrence of the alloy melting reaction prolong the hot corrosion incubation period of the alloy. In addition, increasing the Ta content also promotes solid TaS2The method can inhibit the generation of liquid NiSx, further replace Cr to play a role in fixing S, and obviously improve the hot corrosion resistance of the alloy. Therefore, the Ta content of the high-strength heat-corrosion-resistant single crystal alloy is 6-8%. In addition, researches show that when Ta/(W +2Mo) ═ 1-1.1, the strength of a gamma ' phase in the alloy is high, the gamma ' phase morphology with good cubic degree can be obtained through high-temperature aging, and the alloy has low mismatching degree in a service temperature range, so that the degradation rate of the gamma ' phase is low. Therefore, long-life, high-strength, and hot-corrosion-resistant single crystal alloys require 1 to 1.1 Ta/(W +2 Mo).
Co and Ni can be completely dissolved mutually, and the stacking fault energy of the matrix is also obviously reduced, so that the cross slip of screw dislocation becomes very difficult. However, recent studies have found that high Co alloys also promote TCP phase precipitation. Too high a Co content also lowers the solution temperature, resulting in a reduction in the high temperature performance of the alloy. Therefore, in order to ensure the addition of refractory elements, the Co content of the high-strength heat-corrosion-resistant single crystal alloy is controlled to be 4-6%.
Al is the most predominant precipitation-strengthening γ' phase-forming element in superalloys. Al can also obviously improve the oxidation resistance of the alloy, but the Al can also obviously improve the oxidation resistance of the alloy to liquid Na2SO4The protective properties of (a) are extremely poor. Therefore, the Al content of the high-strength heat-corrosion-resistant single crystal alloy is 3.5-4.5%.
Ti is also the most predominant precipitation-strengthening γ' phase-forming element in superalloys. Ti can also improve the antiphase domain boundary energy of gamma' phase and the high-temperature strength of the alloy. Meanwhile, Ti can also obviously improve the hot corrosion resistance of the alloy. However, the Ti content is too high, the stability of the alloy structure is poor, the eutectic content is high, the heat treatment of the alloy is extremely difficult, and the Ti content is controlled to be 3.5-4.5% by combining the factors.
The addition of a proper amount of C can improve the processing property and the defect tolerance of the alloy. However, the addition of excessive C lowers the alloy properties, and therefore, the C content is controlled to 0 to 0.1%.
The addition of a proper amount of Hf can improve the plasticity and the adhesive force of an oxide film, obviously increase the cyclic oxidation resistance of the alloy and improve the compatibility of a coating and a matrix. Therefore, the Hf content is controlled to 0 to 0.2%.
The nickel-based single crystal superalloy provided by the invention is prepared by smelting pure Ni, Co, Cr, W, Mo, Ta, Ti, Al, C, Hf and other elements in a vacuum induction furnace (refining temperature: 1530 +/-10 ℃, refining time 30min, refining period vacuum degree less than or equal to 3Pa), casting into a mother alloy with chemical components meeting requirements, remelting by a directional solidification device (a high-speed solidification method or a liquid metal cooling method, casting at 1550 ℃, and directional solidification drawing rate of 4mm/min), and directionally solidifying into a single crystal test bar by using a spiral crystal selector or a seed crystal method. It is subjected to heat treatment before use. The heat treatment system is as follows: 1290 ℃/2h/AC +1315 ℃/6h/AC +1140 ℃/4h/AC +870 ℃/20h/AC (AC: air cooled).
Aiming at the background of the prior art, the invention develops the long-life high-strength hot corrosion resistant single crystal superalloy, the hot corrosion resistant performance of the long-life high-strength hot corrosion resistant single crystal superalloy is equivalent to that of the PWA1483 alloy, the mechanical property of the long-life high-strength hot corrosion resistant single crystal superalloy is obviously superior to that of the PWA1483 single crystal superalloy, and the long-life high-strength hot corrosion resistant single crystal superalloy has excellent static.
The advantages and beneficial effects of the invention are illustrated as follows:
(1) compared with other existing high-strength nickel-based single crystal high-temperature alloys, the alloy disclosed by the invention has excellent hot corrosion resistance, and the hot corrosion capacity at 900 ℃ is equivalent to that of PWA1483 alloy.
(2) The alloy of the invention does not contain a noble element Re, but the endurance quality of the alloy is obviously superior to PWA1483 single crystal high temperature alloy. The durable life is more than 120h at 980 ℃/248MPa and more than 70h at 1000 ℃/235MPa, and the alloy is a high-strength hot-corrosion-resistant single crystal superalloy.
(4) The alloy has stable structure after long-term thermal exposure at the temperature of 900-1000 ℃, and the mechanical property of the alloy is not deteriorated but obviously improved after long-term thermal exposure.
Drawings
FIG. 1 shows the 900 ℃ hot corrosion performance of the alloy of the present invention;
FIG. 2 is a graph comparing the Larson-Miller curves for the alloy of the present invention and a first generation single crystal superalloy PWA1483 of the prior art;
FIG. 3 is a graph showing creep performance of alloys of the present invention after various long term thermal exposures at 900 ℃.
Detailed Description
The following examples further illustrate the invention but are not intended to limit the invention thereto.
The following examples alloy specific preparation method requirements: smelting in a vacuum induction furnace, casting into a master alloy with chemical components meeting requirements, then preparing a single crystal test rod, and carrying out heat treatment before use.
Examples 1 to 5:
the chemical compositions of the nickel-based single crystal superalloy samples of the present invention are shown in table 1. For ease of comparison, the chemical composition of a typical first generation nickel-based single crystal superalloy PWA1483 is also listed in table 1.
TABLE 1 tabulation of chemical composition (wt.%) of inventive alloys (examples 1-5) and DD413
| Alloy (I) | Cr | Co | W | Mo | Ta | Al | Ti | C | Hf | Ni |
| Example 1 | 11.4 | 5.5 | 5.9 | 0.4 | 6.8 | 3.9 | 4.1 | 0.07 | 0.09 | Surplus |
| Example 2 | 12 | 5.8 | 6.8 | 0.4 | 7.3 | 4.2 | 4.1 | 0.07 | 0.08 | Surplus |
| Example 3 | 10.2 | 4.3 | 5.2 | 0.3 | 6.1 | 3.6 | 3.8 | 0.05 | 0.08 | Surplus |
| Example 4 | 11.5 | 5.1 | 6 | 0.4 | 6.8 | 4.4 | 4.2 | 0.08 | 0.07 | Surplus |
| Example 5 | 11.3 | 5.3 | 6.1 | 0.1 | 6.4 | 4.2 | 4.2 | 0.05 | 0.09 | Surplus |
| PWA1483 | 12.0 | 9.0 | 4.0 | 1.9 | 5.0 | 3.4 | 4.0 | 0.06 | - | Surplus |
Note: the "remainder" in the column of Ni content in the table means "remainder".
The Larson-Miller curves of examples 1, 2 and 3 of the present invention and a typical first generation hot corrosion resistant nickel based single crystal superalloy PWA1483 are shown in FIG. 1. The endurance performance of the alloy of the invention is obviously higher than that of PWA1483 alloy.
The 900 ℃ hot corrosion performance of the alloy of example 4 of the invention is compared with that of the hot corrosion resistant alloy PWA1483 shown in FIG. 2. The hot corrosion performance of the alloy of the invention is equivalent to that of the hot corrosion resistant alloy PWA1483 alloy.
Creep performance of the alloy of example 5 of the invention after different long term thermal exposures at 900 c (figure 3). It was found that the performance of the alloy did not deteriorate after long term heat exposure, and the alloy had the best creep performance after 2000h heat exposure.
Claims (5)
1. A long-life high-strength hot corrosion resistant single crystal superalloy is characterized in that: the alloy comprises the following chemical components in percentage by weight:
cr: 10-12%, Co: 4-6%, Mo: 0-0.5%, W: 5-7%, Ta: 6-8%, Al: 3.5-4.5%, Ti: 3.5-4.5%, C: 0-0.1%, Hf: 0-0.2%, and the balance of Ni.
2. A long life high strength hot corrosion resistant single crystal superalloy as in claim 1, wherein: the alloy comprises the following chemical components in percentage by weight:
cr: 11.2-11.8%, Co: 4.5-5.5%, Mo: 0.2-0.4%, W: 5.7-6.3%, Ta: 6.7-7.3%, Al: 3.8-4.2%, Ti: 3.8-4.2%, C: 0.04-0.08%, Hf: 0.05-0.15% and the balance of Ni.
3. The long life high strength hot corrosion resistant single crystal superalloy as in claim 1 or 2, wherein: the alloy comprises the chemical components of 1-1.1% by weight of Ta/(W +2 Mo).
4. The long life high strength hot corrosion resistant single crystal superalloy as in claim 1 or 2, wherein: in the alloy, Nv≤2.4。
5. The long life high strength hot corrosion resistant single crystal superalloy as in claim 1 or 2, wherein: in the chemical components of the alloy, the weight percentage content of impurity elements meets the following requirements: o is less than or equal to 0.001, N is less than or equal to 0.001, S is less than or equal to 0.001, Zr is less than or equal to 0.0075, Mn is less than or equal to 0.01, Si is less than or equal to 0.1, P is less than or equal to 0.005, Cu is less than or equal to 0.05, Mg is less than or equal to 0.008, Se is less than or equal to 0.0003, Pb is less than or equal to 0.0002, Te is less than or equal to 0.00005, Bi is less than or.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011449792.2A CN112593122B (en) | 2020-12-09 | 2020-12-09 | Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011449792.2A CN112593122B (en) | 2020-12-09 | 2020-12-09 | Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112593122A true CN112593122A (en) | 2021-04-02 |
| CN112593122B CN112593122B (en) | 2023-02-03 |
Family
ID=75191982
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011449792.2A Active CN112593122B (en) | 2020-12-09 | 2020-12-09 | Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112593122B (en) |
Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4402772A (en) * | 1981-09-14 | 1983-09-06 | United Technologies Corporation | Superalloy single crystal articles |
| US4459160A (en) * | 1980-03-13 | 1984-07-10 | Rolls-Royce Limited | Single crystal castings |
| JPH01234540A (en) * | 1988-03-14 | 1989-09-19 | Mitsubishi Metal Corp | Ni-based single crystal super alloy having excellent high temperature corrosion resistance |
| JPH0559473A (en) * | 1986-03-27 | 1993-03-09 | General Electric Co <Ge> | Improved nickel-base super alloy with low angle intergranular resistance for producing single crystal product |
| EP0555124A1 (en) * | 1992-02-05 | 1993-08-11 | Office National D'etudes Et De Recherches Aerospatiales | Nickel base single crystal superalloy with improved oxydation resistance and process for producing it |
| JP2001294959A (en) * | 2000-04-17 | 2001-10-26 | Mitsubishi Heavy Ind Ltd | SINGLE CRYSTAL Ni HEAT RESISTANT ALLOY AND TURBINE BRADE |
| CN1886525A (en) * | 2003-11-27 | 2006-12-27 | 西门子公司 | High temperature resistant component |
| CN1954960A (en) * | 2005-10-28 | 2007-05-02 | 联合工艺公司 | Low temperature diffusion braze repair of single crystal components |
| CN103966671A (en) * | 2014-03-31 | 2014-08-06 | 中国科学院金属研究所 | High-strength hot-corrosion-resistant Ni-based single crystal superalloy and preparation method |
| JP2015030915A (en) * | 2013-08-07 | 2015-02-16 | 三菱日立パワーシステムズ株式会社 | Ni-BASED CASTING SUPER ALLOY AND CASTING MADE OF THE Ni-BASED CASTING SUPER ALLOY |
| CN105200521A (en) * | 2014-05-28 | 2015-12-30 | 中国科学院金属研究所 | Rhenium-free low-density high-performance nickel-based monocrystalline high-temperature alloy and heat treatment technology thereof |
| CN107675026A (en) * | 2017-09-30 | 2018-02-09 | 东方电气集团东方汽轮机有限公司 | A kind of low cost, the nickel-base high-temperature single crystal alloy of high comprehensive performance |
| CN107735502A (en) * | 2015-07-09 | 2018-02-23 | 三菱日立电力系统株式会社 | Ni base high strength thermal resistant alloys component, its manufacture method and gas turbine blades |
| CN111440967A (en) * | 2020-05-08 | 2020-07-24 | 中国科学院金属研究所 | High-thermal-stability high-strength Re-free nickel-based single crystal superalloy and preparation process thereof |
-
2020
- 2020-12-09 CN CN202011449792.2A patent/CN112593122B/en active Active
Patent Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4459160A (en) * | 1980-03-13 | 1984-07-10 | Rolls-Royce Limited | Single crystal castings |
| US4402772A (en) * | 1981-09-14 | 1983-09-06 | United Technologies Corporation | Superalloy single crystal articles |
| JPH0559473A (en) * | 1986-03-27 | 1993-03-09 | General Electric Co <Ge> | Improved nickel-base super alloy with low angle intergranular resistance for producing single crystal product |
| JPH01234540A (en) * | 1988-03-14 | 1989-09-19 | Mitsubishi Metal Corp | Ni-based single crystal super alloy having excellent high temperature corrosion resistance |
| EP0555124A1 (en) * | 1992-02-05 | 1993-08-11 | Office National D'etudes Et De Recherches Aerospatiales | Nickel base single crystal superalloy with improved oxydation resistance and process for producing it |
| JP2001294959A (en) * | 2000-04-17 | 2001-10-26 | Mitsubishi Heavy Ind Ltd | SINGLE CRYSTAL Ni HEAT RESISTANT ALLOY AND TURBINE BRADE |
| CN1886525A (en) * | 2003-11-27 | 2006-12-27 | 西门子公司 | High temperature resistant component |
| CN1954960A (en) * | 2005-10-28 | 2007-05-02 | 联合工艺公司 | Low temperature diffusion braze repair of single crystal components |
| JP2015030915A (en) * | 2013-08-07 | 2015-02-16 | 三菱日立パワーシステムズ株式会社 | Ni-BASED CASTING SUPER ALLOY AND CASTING MADE OF THE Ni-BASED CASTING SUPER ALLOY |
| CN103966671A (en) * | 2014-03-31 | 2014-08-06 | 中国科学院金属研究所 | High-strength hot-corrosion-resistant Ni-based single crystal superalloy and preparation method |
| CN105200521A (en) * | 2014-05-28 | 2015-12-30 | 中国科学院金属研究所 | Rhenium-free low-density high-performance nickel-based monocrystalline high-temperature alloy and heat treatment technology thereof |
| CN107735502A (en) * | 2015-07-09 | 2018-02-23 | 三菱日立电力系统株式会社 | Ni base high strength thermal resistant alloys component, its manufacture method and gas turbine blades |
| CN107675026A (en) * | 2017-09-30 | 2018-02-09 | 东方电气集团东方汽轮机有限公司 | A kind of low cost, the nickel-base high-temperature single crystal alloy of high comprehensive performance |
| CN111440967A (en) * | 2020-05-08 | 2020-07-24 | 中国科学院金属研究所 | High-thermal-stability high-strength Re-free nickel-based single crystal superalloy and preparation process thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112593122B (en) | 2023-02-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5467306B2 (en) | Ni-based single crystal superalloy and alloy member based thereon | |
| JP5467307B2 (en) | Ni-based single crystal superalloy and alloy member obtained therefrom | |
| CN102653832B (en) | Directed nickel-base high temperature alloy | |
| CN103436739B (en) | A kind of rhenium-containing High-strength hot-corrosion-resistnickel-base nickel-base monocrystal high-temperature alloy | |
| CN114525430B (en) | Nickel-based high-temperature alloy and preparation method thereof | |
| JP2013108166A (en) | Rhenium-free single crystal superalloy for turbine blade and vane application | |
| CN107034387A (en) | A kind of low segregation nickel-base high-temperature single crystal alloy of high-strength corrosion and heat resistant | |
| WO2015180213A1 (en) | Rhenium-free low density high performance nickel-based single crystal superalloy and heat treatment process 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 | |
| JPH11131163A (en) | Ni-base single crystal alloy and its production | |
| CN102732750A (en) | Nickel base single crystal superalloy with low cost and low density | |
| WO2023197976A1 (en) | Single crystal superalloy, and preparation method therefor and application thereof | |
| CN103173865B (en) | A kind of Low-cost nickel-base single crystal high-temperature alloy and preparation method thereof | |
| CN112593121A (en) | High-strength high-temperature-oxidation-resistant rhenium-free second-generation nickel-based single crystal high-temperature alloy and heat treatment process thereof | |
| CN108866387B (en) | High-strength hot-corrosion-resistant nickel-based high-temperature alloy for gas turbine and preparation process and application thereof | |
| JP2015120976A (en) | Ni-BASED CASTING SUPERALLOY AND CAST ARTICLE THEREFROM | |
| KR20110106352A (en) | Ni-based single crystal superalloy | |
| CN112593122B (en) | Long-life high-strength hot-corrosion-resistant single crystal high-temperature alloy | |
| JP2023504562A (en) | Nickel-chromium-aluminum alloy with excellent workability, creep strength and corrosion resistance and its use | |
| JP5595495B2 (en) | Nickel-base superalloy | |
| CN115505790B (en) | Nickel-based superalloy with stable weld strength, and preparation method and application thereof | |
| RU2581339C1 (en) | Blade of gas-turbine unit made of heat-resistant nickel-based alloy and manufacturing method thereof | |
| CN114231767B (en) | Method for controlling sigma phase precipitation of hot corrosion resistant nickel-based superalloy | |
| CN112176224A (en) | High-strength nickel-based single crystal superalloy with excellent comprehensive performance | |
| KR20120105693A (en) | Ni base single crystal superalloy with enhanced creep property |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |