CN115488277A - Preparation process of high-uniformity 650-DEG C high-temperature titanium alloy large-size fine-grain blisk - Google Patents
Preparation process of high-uniformity 650-DEG C high-temperature titanium alloy large-size fine-grain blisk Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
- B21J5/08—Upsetting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K1/00—Making machine elements
- B21K1/28—Making machine elements wheels; discs
- B21K1/36—Making machine elements wheels; discs with blades
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K29/00—Arrangements for heating or cooling during processing
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Abstract
The invention discloses a preparation process of a high-uniformity titanium alloy large-size fine-grain blisk with high temperature of 650 ℃, which comprises the steps of completing cogging and forging of an alloy cast ingot at 1150-1250 ℃, upsetting, drawing and deforming the obtained blank at 10-30 ℃ above a beta transformation point, cooling by water after forging, heating the blank to 850-870 ℃, preserving heat for 12-20 hours, heating to 990-1000 ℃ with a furnace, upsetting and drawing and deforming, heating the blank to 10-30 ℃ above the transformation point, upsetting, drawing and deforming, cooling by water after forging, heating the blank to 850-870 ℃, preserving heat for 12-20 hours, heating to 990-1000 ℃ with the furnace, upsetting, drawing and deforming the blank at 50-35 ℃ below the beta transformation point, and finally forming the blank at 50-40 ℃ below the beta transformation point to obtain a forged blank; and carrying out solid solution and aging heat treatment on the obtained forging stock to finally obtain the blisk forging blank. The process is suitable for preparing the blisk forge piece with the height of 600mm to 1000mm and the height of 60mm to 100mm, and the structure uniformity and the performance of the forge piece are superior to those of the traditional process.
Description
Technical Field
The invention belongs to the field of new material processing, and particularly relates to a preparation process of a high-uniformity large-size fine-grain blisk made of a high-temperature titanium alloy at 650 ℃.
Background
The high-temperature titanium alloy is a key material for an aeroengine. The dosage of titanium alloy of the aeroengine is one of the important marks of the advancement of the aeroengine. The demand of aero-engines draws the development of high-temperature titanium alloy, and the technical development of titanium alloy materials promotes the upgrading and updating of engines. The maximum service temperature of the existing mature high-temperature titanium alloy is 600 ℃. In order to meet the design requirement of higher thrust-weight ratio, the number of stages of a compressor disk of the next generation engine is continuously reduced, the rotating speed is continuously increased, the high-temperature section moves forwards, the requirement on medium and low temperature titanium alloy is weakened, and the urgent requirement on high temperature resistant titanium alloy is provided.
In order to reduce the structural weight of the air compressor, high-temperature titanium alloy with high temperature of 650 ℃ and high strength is urgently needed to replace high-temperature alloy for the blisk of the air compressor of the high-speed turbine engine so as to reduce the weight of parts of the air compressor and improve the efficiency and the thrust-weight ratio of the engine. After the high-temperature titanium alloy is developed to 600 ℃, the required composition design and hot working technology are close to the limit of the technical level of the current process. The high-temperature titanium alloy is developed from 550 ℃ to 600 ℃, the thermal stability is reduced by more than one time, the design bottom line is already approached, and the design of the service life and the safety and reliability of parts cannot be guaranteed by breaking through the bottom line. Another problem is the technical problem of controlling the homogeneity of the microstructure of the material exposed by the dwell fatigue sensitivity. Similar microstructures are obtained by adopting the same forging and heat treatment processes, the alpha + beta type titanium alloy has low holding fatigue sensitivity, the near alpha type titanium alloy has high holding fatigue sensitivity, and more uniform microstructures are required to be obtained to meet the harsher performance control requirement. As the design use temperature rises, the requirements on the forging process technology are correspondingly increased. Therefore, the basic problems of component optimization design and microstructure control which restrict the technical development of the high-temperature titanium alloy with the temperature of more than 600 ℃ are fundamentally solved from the basic research of component design and hot working process, so that the technical bottleneck of the research and application of the high-temperature titanium alloy with the temperature of 650 ℃ is broken through, and the method has important material guarantee function and significance for the research of future advanced engines in China.
Disclosure of Invention
The invention aims to provide a preparation process of a high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk. Compared with the traditional process, the process is suitable for preparing the large-size blisk forge piece, and the structure uniformity and the metallurgical quality stability of the forge piece are remarkably improved compared with the traditional process. The method has the advantages of simple operation, short flow, high stability and suitability for industrial production.
The invention provides a preparation process of a high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk, which comprises the following specific steps:
step 1) firstly heating a 650 ℃ high-temperature titanium alloy ingot to 1150-1250 ℃, preserving heat for 10-30 h, discharging and forging to finish 1 upsetting and drawing deformation; then the blank is returned to the furnace and is kept warm for 1 to 2 hours, and then 1 upsetting and drawing deformation are completed to obtain the blank, and the pressing deformation speed is increased during each upsettingThe rate is 0.2s -1 ～0.08s -1 Performing single upsetting deformation of not less than 50%, and performing air cooling after forging to obtain a blank;
step 2) performing 1-time hot upsetting and drawing deformation on the blank obtained in the step 1) at the temperature of 20-50 ℃ above the beta transformation point, wherein the pressing deformation rate under upsetting is 0.2s -1 ～0.08s -1 The upsetting deformation is more than or equal to 50 percent, and water cooling is carried out after forging;
step 3) heating the blank to 850-870 ℃, preserving heat for 12-20 h, heating to 990-1000 ℃ along with the furnace, upsetting and drawing for deformation for 1 heating time, wherein the upsetting pressing rate is 0.05s -1 ～0.04s -1 The upsetting deformation is between 35 and 45 percent;
step 4) repeating the step 2) once;
step 5) repeating the step 3) once;
step 6) upsetting and drawing deformation are carried out on the blank for 6-8 times at 50-35 ℃ below the beta transformation point, and the upsetting rate of each time is required to be 0.05s -1 ～0.04s -1 Meanwhile, the pressing amount is between 30 and 50 percent, the accumulated forging ratio is more than or equal to 3.3, and the final forging temperature is not lower than 900 ℃;
step 7) placing the blank in T β Forming at 50-40 deg.c below the temperature required for forging stock to have deformation rate of 0.05s each time -1 ～0.04s -1 The pressing amount is between 30 and 45 percent to obtain a forging stock;
step 8) carrying out solid solution and aging heat treatment on the forged blank obtained in the step 7), wherein the solid solution heat treatment system is as follows: t is β Keeping the temperature for 1 to 3 hours at the temperature of between 15 and 25 ℃, and cooling the steel by water or oil after the steel is taken out of the furnace; the aging heat treatment comprises the following steps: keeping the temperature of 680-720 ℃ for 4-6 h, and then cooling in air.
The preferred scheme of the preparation process of the high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk is that a 650 ℃ high-temperature titanium alloy ingot is prepared from the following components in percentage by mass: 5.0% -6.3%, sn:3.0% -5.0%, zr:2.5% -4.0%, mo:0.2% -0.7%, si:0.25% -0.7%, nb:0.1% -0.6%, ta:0.5% -2.6%, W:0.3% -2.0%, C:0.02 to 0.10 percent, and the balance of Ti and other inevitable impurity elements.
The preferable scheme of the preparation process of the high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk is that in the step 3, in order to prevent cracking, the forging stock needs to be re-heated and kept warm for 2 hours after upsetting and then drawn out.
The preferable scheme of the preparation process of the high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk is that the forming mode adopted in the step 6) is an isothermal or near isothermal forming process; when the isothermal or near isothermal die forging forming process is adopted, the die is heated to 0-60 ℃ below the heating temperature of the blank, and the deformation rate is 0.005s -1 ～0.05s -1 。
The invention has the beneficial effects that:
1) The diameter of the blisk forge piece prepared by the method is 600 mm-1100 mm, the height of the blisk forge piece is 60 mm-130 mm, all parts of the forge piece are uniform in structure, and the performance is stable;
2) The tensile strength at room temperature of any part of the forging is not lower than 1070Mpa, the yield strength is not lower than 940Mpa, the elongation is not lower than 10.0%, and the face shrinkage is not lower than 15%. The elongation of the sample after being exposed for 100 hours at 650 ℃ is not less than 3.0 percent, and the face shrinkage is not less than 6 percent. The tensile strength at 650 ℃ is not lower than 830Mpa, the yield is not lower than 750Mpa, the elongation is not lower than 20.0 percent, and the area shrinkage is not lower than 40 percent;
3) The invention relates to a novel heat-resistant titanium alloy and a processing and manufacturing method and application thereof in the prior patent technology (publication number: CN 104018027A), key technologies such as obdurability matching, structure uniformity, mechanical property consistency and stability control of a 650 ℃ high-temperature titanium alloy large-size blisk forging are solved through process optimization, and a method for controlling strength, orientation uniformity and high-temperature long-time structure stability of the large-size blisk forging is mastered; the 650 ℃ high-temperature titanium alloy and blisk forging preparation technology developed by the invention can also be popularized and applied to other engine improvements, replaces part of high-temperature alloy, reduces the structural weight of the engine, and improves the fuel economy and the thrust-weight ratio of the engine.
Drawings
FIG. 1 is a high magnification organization picture near the surface of a forging stock prepared in example 1;
FIG. 2 is a photograph of a high magnification microstructure of the center of the forging stock prepared in example 1;
FIG. 3 is a photograph of a high magnification texture near the surface of a forging stock prepared in example 2;
FIG. 4 is a photograph of a high magnification texture of the center of the forging prepared in example 2;
FIG. 5 is a schematic view of a die forging of embodiments 3 and 4;
FIG. 6 is a high magnification microstructure picture of the rim of the die forged part prepared in example 3;
FIG. 7 is a high magnification organization picture of a spoke plate of the die forging prepared in example 3;
FIG. 8 is a high power texture picture of the die forging hub prepared in example 3;
FIG. 9 is a high power texture picture of the rim of the die forged part prepared in example 3;
FIG. 10 is a high magnification organization picture of a spoke plate of the die forging prepared in example 3;
FIG. 11 is a high magnification organization chart of the die forging hub prepared in example 3.
Detailed Description
Example 1:
the size of the high-temperature titanium alloy ingot used at 650 ℃ in the embodiment is 600mm in diameter and 1200mm in length, and the high-temperature titanium alloy ingot comprises the following chemical components: 5.71Al-0.60Mo-3.26Zr-3.81Sn-0.92W-0.44Si-1.00 Ta-0.41 Nb-0.03C, beta transition temperature 1035 ℃.
Step 1) firstly heating the ingot to 1150 ℃, preserving heat for 24 hours, and then discharging from a furnace for forging to finish 1-time upsetting and drawing deformation; then the blank is returned to the furnace and is kept warm for 2 hours, and then 1 upsetting and drawing deformation are finished, and the pressing deformation rate of each upsetting is 0.1s -1 The single upsetting deformation is 50 percent, and air cooling is carried out after forging to obtain a blank;
step 2) upsetting and drawing deformation are carried out on the blank obtained in the step 1 for 1 heating time at 1060 ℃, and the upsetting pressing rate is 0.1s -1 The deformation is 52 percent, the forging ratio is 3.8, and water cooling is carried out after forging;
step 3) heating the blank to 860 ℃, preserving heat for 15h, then raising the temperature to 990 ℃ along with the furnace for upsetting, then returning the blank to the furnace for supplementing heat for 2h, continuing to draw out, wherein the upsetting pressing rate is 0.05s -1 The deformation is 38 percent, and air cooling is carried out after forging;
step 4) repeating the process of the step 2) on the blank once;
step 5) repeating the process of the step 3) on the blank once;
step 6) heating the blank to 995 ℃ to perform 7-time upsetting and drawing deformation, wherein the upsetting deformation rate of each time is 0.04s -1 The pressing amount is between 37 and 40 percent, and the cumulative forging ratio is between 3.3 and 3.7;
step 7) blanking by a sawing machine according to the design size of the final forged piece, and forming the blank at 970 ℃ with the deformation rate of 0.04s -1 Forming and pressing the forging stock with the deformation amount of 40 percent to obtain a forging stock;
and 8) performing solid solution and aging heat treatment on the forged blank finally, wherein the solid solution heat treatment system is as follows: 1023 ℃, preserving heat for 3 hours, and cooling by water after discharging; the aging heat treatment comprises the following steps: keeping the temperature at 700 ℃ for 6h and then cooling in air. And finally, polishing the surface to obtain a forged piece with the diameter of 800mm and the height of 100 mm.
Example 2
This example is a comparative example of example 1, and the ingot size, chemical composition, and β transus temperature selected were exactly the same as those of example 1.
In the embodiment, the forging stock is directly heated to 990 ℃ in the steps 3 and 5 to be subjected to upsetting and drawing deformation, and other steps are completely the same as those in the embodiment 1, so that the forging with the diameter of 800mm and the height of 100mm is finally obtained.
The forgings of example 1 and example 2 were compared for structural and mechanical property analysis: the high-power structure of the forging in the embodiment 1 is a two-state structure, the primary alpha content is about 12%, the primary alpha and primary beta crystal grains at each position of the forging are similar in size and are distributed uniformly, and the consistency is good (fig. 1 and fig. 2). The room-temperature tensile property of the forge piece is not lower than 1070MPa, and the 650-DEG C tensile property is not lower than 835MPa; after the forge piece is exposed at 650 ℃/100 h/heat, the tensile strength at room temperature can reach 1080MPa, the tensile strength at 120 ℃ can reach more than 1060MPa, and the mechanical property difference of different parts is relatively small. The forging of the embodiment 2 has the same high power structure as a two-state structure, the primary alpha content is about 14%, the near-surface primary alpha size of the forging is small, the center position is relatively thick, the original beta grain size is not uniformly distributed, and different positions show different structure characteristics (fig. 3 and 4). The tensile properties of the forgings at different positions are greatly different, and the overall mechanical properties of the forgings are relatively poor compared with those of the forgings in example 1.
TABLE 1 tensile and KIC Properties of the forgings of example 1
Table 2 thermal stability in example 1
TABLE 3 tensile and KIC Properties of the forgings of example 2
Table 4 thermal stability of forgings in example 2
Example 3:
the size of the 650 ℃ high-temperature titanium alloy ingot used in the embodiment is 600mm in diameter and 1200mm in length, and the chemical components are as follows: 5.68Al-0.57Mo-3.31Zr-3.76Sn-0.89W-0.46Si-0.98 Ta-0.45 Nb-0.06C, beta transition temperature 1038 ℃.
Step 1) firstly heating an ingot to 1150 ℃, preserving heat for 24 hours, then discharging from a furnace and forging, and finishing 1-time upsetting and drawing deformation; then the forging and drawing deformation is finished for 1 time after the furnace is returned and the temperature is kept for 1.5 hours, and the pressing deformation rate of each upsetting is 0.1s -1 The single upset deformation was 52%. Air cooling is carried out after forging to obtain a blank;
step 2) upsetting and drawing deformation are carried out on the blank obtained in the step 1) for 1 heating time at 1073 ℃, and the upsetting pressing rate is 0.1s -1 The deformation is 51 percent, the forging ratio is 3.6, and water cooling is carried out after forging;
step 3) heating the blank to 865 ℃, preserving heat for 15h, then raising the temperature to 1000 ℃ along with the furnace for upsetting, then returning the blank to the furnace, preserving heat for 2h, and then drawing out, wherein the upsetting pressing rate is about 0.05s -1 The deformation amount was 55%. Air cooling after forging;
step 4) repeating the process of step 2) on the blank;
step 5) repeating the process of the step 3) on the blank;
step 6), heating the blank to 998 ℃, and then carrying out upsetting and drawing deformation for 7 times; the upsetting press-down rate per heat is 0.04s -1 The pressing amount is between 36 and 42 percent, the cumulative forging ratio is between 3.3 and 3.6, the finish forging temperature is 920 ℃, and air cooling is carried out after forging;
step 7) according to the design size of the forged piece, adopting a sawing machine for blanking, adopting a near isothermal forming process, heating the die to 953 ℃, heating the blank to 993 ℃, and enabling the deformation rate to be 0.01s -1 The deformation is 40%, and air cooling is carried out after forging to obtain a die forging blank;
step 8) carrying out solid solution and aging heat treatment on the forging blank, wherein the solid solution heat treatment system is as follows: keeping the temperature for 2h at 1025 ℃, and cooling by water after discharging; the aging heat treatment comprises the following steps: keeping the temperature at 700 ℃ for 8h, then air cooling, and finally polishing the surface to obtain a variable cross-section forging blank with the maximum diameter of 1000mm and the height of 80 mm.
Example 4:
the ingot size, chemical composition, and beta transus temperature selected for the comparative example of example 3 in this example were exactly the same as those of example 3.
This example changes the process to: the forging stock is directly heated to 1000 ℃ for upsetting and drawing deformation. The other steps are exactly the same as in example 3. Finally obtaining the variable cross-section forging blank with the maximum diameter of 1000mm and the height of 80 mm.
The forgings of example 3 and example 4 were compared for structural mechanical property analysis. Example 3 the high power structure of the forging is a two-state structure, the primary alpha content is about 14%, the primary alpha phase is distributed uniformly, the primary alpha phase sizes of different positions of the forging are similar, the primary alpha phase is distributed in a dispersion manner, the primary beta crystal grains are uniform and fine, and the high power structure of each position of the forging has no obvious difference (fig. 6-8). The mechanical test result shows that the room temperature tensile strength of the forging is not lower than 1070MPa, the 650 ℃ tensile strength is not lower than 830MPa, and the forging has good plasticity; the forging piece has good thermal stability, the tensile strength of the sample at room temperature to 120 ℃ is not reduced after the sample is exposed at 650 ℃/100h, and the whole forging piece has relatively good structural and performance consistency. The high-power structure of the forged piece in the embodiment 4 is a double-state structure, the primary alpha content is about 15%, the primary alpha contents of different positions of the forged piece are obviously different, and the original beta crystal grain size is not uniform. (FIGS. 9 to 11). The mechanical properties of different positions of the forged piece are greatly different, the strength of the spoke plate position is highest, the plasticity is lowest, and the strength of the hub and the rim position is lower and the plasticity is higher.
TABLE 5 tensile and KIC Properties of the forgings of example 3
TABLE 6 thermal stability of forgings in EXAMPLE 3
TABLE 7 tensile and KIC Properties of the forgings in example 4
TABLE 8 thermal stability of forgings in example 4
The above embodiments are merely illustrative of the technical ideas and features of the present invention, and the purpose thereof is to enable those skilled in the art to understand the contents of the present invention and implement the present invention, and not to limit the protection scope of the present invention. All equivalent changes and modifications made according to the spirit of the present invention should be covered within the protection scope of the present invention.
Claims (4)
1. A preparation process of a high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk is characterized by comprising the following specific steps:
step 1) firstly heating a 650 ℃ high-temperature titanium alloy cast ingot to 1150-1250 ℃, preserving heat for 10-30 h, and then discharging and forging to complete 1-time upsetting and drawing deformation; then the blank is returned to the furnace and is kept warm for 1 to 2 hours, and then 1 upsetting and drawing deformation are finished, and the pressing deformation rate of each upsetting is 0.2s -1 ～0.08s -1 Performing single upsetting deformation of not less than 50%, and performing air cooling after forging to obtain a blank;
step 2) performing 1-time hot upsetting and drawing deformation on the blank obtained in the step 1) at the temperature of 20-50 ℃ above the beta transformation point, wherein the pressing deformation rate under upsetting is 0.2s -1 ～0.08s -1 Upsetting deformation is more than or equal to 50%, and water cooling is carried out after forging;
step 3) heating the blank to 850-870 ℃, preserving heat for 12-20 h, then raising the temperature to 990-1000 ℃ along with the furnace, and carrying out upsetting and drawing deformation for 1 heating time, wherein the upsetting pressing rate is 0.05s -1 ～0.04s -1 The upsetting deformation is between 35 and 45 percent;
step 4) repeating the step 2) once;
step 5) repeating the step 2) once;
step 6) upsetting and drawing the blank at 50-35 ℃ below the beta transformation point for 6-8 times of heating deformation, wherein the upsetting rate of each heating is required to be 0.05s -1 ～0.04s -1 Meanwhile, the pressing amount is between 30 and 50 percent, the accumulated forging ratio is more than or equal to 3.3, and the final forging temperature is not lower than 900 ℃;
step 7) placing the blank in T β E, 50 ℃Forming at 40 deg.C, and requiring that the deformation rate of forging stock per heating is 0.05s -1 ～0.04s -1 The pressing amount is between 30 and 45 percent to obtain a forging stock;
step 8) carrying out solid solution and aging heat treatment on the forged blank obtained in the step 7), wherein the solid solution heat treatment system is as follows: t is β Keeping the temperature for 1 to 3 hours at the temperature of between 15 and 25 ℃, and cooling the steel by water or oil after the steel is taken out of the furnace; the aging heat treatment comprises the following steps: keeping the temperature of 680-720 ℃ for 4-6 h, and then cooling in air.
2. The process for preparing a high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk as claimed in claim 1, wherein: the 650 ℃ high-temperature titanium alloy ingot comprises the following components in percentage by weight: 5.0% -6.3%, sn:3.0% -5.0%, zr:2.5% -4.0%, mo:0.2% -0.7%, si:0.25% -0.7%, nb:0.1% -0.6%, ta:0.5% -2.6%, W:0.3% -2.0%, C: 0.02-0.10 percent of Ti and other inevitable impurity elements as the rest.
3. The process for preparing the high-uniformity 650 ℃ high-temperature titanium alloy large-size fine-grain blisk according to the claim 1, which is characterized in that: the forming mode adopted in the step 6) is an isothermal or near isothermal forming process; when the isothermal or near isothermal die forging forming process is adopted, the die is heated to 0-60 ℃ below the blank heating temperature, and the blank deformation rate is 0.005s -1 ～0.05s -1 。
4. A process for preparing a large size fine crystalline blisk of high temperature titanium alloy with high homogeneity at 650 ℃ according to claims 1-3, characterized in that: the blisk forge piece with the diameter of 600mm to 1000mm and the height of 60mm to 100mm can be prepared by adopting the process.
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| CN117900362A (en) * | 2024-02-02 | 2024-04-19 | 中国航发湖南动力机械研究所 | Ti2AlNb alloy centrifugal impeller and near-isothermal forging method thereof |
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| CN117900362A (en) * | 2024-02-02 | 2024-04-19 | 中国航发湖南动力机械研究所 | Ti2AlNb alloy centrifugal impeller and near-isothermal forging method thereof |
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