CN116380892A - Method for checking and controlling production quality of Ti60 titanium alloy blisk - Google Patents
Method for checking and controlling production quality of Ti60 titanium alloy blisk Download PDFInfo
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- CN116380892A CN116380892A CN202310154936.9A CN202310154936A CN116380892A CN 116380892 A CN116380892 A CN 116380892A CN 202310154936 A CN202310154936 A CN 202310154936A CN 116380892 A CN116380892 A CN 116380892A
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- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 47
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 46
- 238000000034 method Methods 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 238000005242 forging Methods 0.000 claims abstract description 57
- 238000010438 heat treatment Methods 0.000 claims abstract description 19
- 230000008569 process Effects 0.000 claims abstract description 16
- 238000007689 inspection Methods 0.000 claims abstract description 9
- 230000032683 aging Effects 0.000 claims abstract description 7
- 230000003287 optical effect Effects 0.000 claims abstract description 7
- 238000005520 cutting process Methods 0.000 claims abstract description 3
- 238000007781 pre-processing Methods 0.000 claims abstract description 3
- 230000007704 transition Effects 0.000 claims description 11
- 239000000243 solution Substances 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 6
- 239000006104 solid solution Substances 0.000 claims description 6
- 239000011159 matrix material Substances 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 230000035882 stress Effects 0.000 claims description 3
- 230000007812 deficiency Effects 0.000 claims description 2
- 230000009467 reduction Effects 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000001514 detection method Methods 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000012490 blank solution Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010275 isothermal forging Methods 0.000 description 1
- 238000003908 quality control method Methods 0.000 description 1
- 238000011002 quantification Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000011179 visual inspection Methods 0.000 description 1
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- 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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N1/00—Sampling; Preparing specimens for investigation
- G01N1/28—Preparing specimens for investigation including physical details of (bio-)chemical methods covered elsewhere, e.g. G01N33/50, C12Q
- G01N1/286—Preparing specimens for investigation including physical details of (bio-)chemical methods covered elsewhere, e.g. G01N33/50, C12Q involving mechanical work, e.g. chopping, disintegrating, compacting, homogenising
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- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N1/00—Sampling; Preparing specimens for investigation
- G01N1/28—Preparing specimens for investigation including physical details of (bio-)chemical methods covered elsewhere, e.g. G01N33/50, C12Q
- G01N1/32—Polishing; Etching
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- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N21/00—Investigating or analysing materials by the use of optical means, i.e. using sub-millimetre waves, infrared, visible or ultraviolet light
- G01N21/84—Systems specially adapted for particular applications
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N1/00—Sampling; Preparing specimens for investigation
- G01N1/28—Preparing specimens for investigation including physical details of (bio-)chemical methods covered elsewhere, e.g. G01N33/50, C12Q
- G01N1/286—Preparing specimens for investigation including physical details of (bio-)chemical methods covered elsewhere, e.g. G01N33/50, C12Q involving mechanical work, e.g. chopping, disintegrating, compacting, homogenising
- G01N2001/2866—Grinding or homogeneising
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N21/00—Investigating or analysing materials by the use of optical means, i.e. using sub-millimetre waves, infrared, visible or ultraviolet light
- G01N21/84—Systems specially adapted for particular applications
- G01N2021/8477—Investigating crystals, e.g. liquid crystals
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- General Health & Medical Sciences (AREA)
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- Health & Medical Sciences (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Forging (AREA)
- Sampling And Sample Adjustment (AREA)
Abstract
The invention relates to a method for checking and controlling the production quality of Ti60 titanium alloy blisk, belonging to the technical field of manufacturing of key materials and parts of aeroengines, comprising the steps of performing die forging process treatment, solution heat treatment and aging heat treatment on a plurality of blanks, and forming a blisk forge piece of the Ti60 titanium alloy blisk; extracting 1 forging piece from each batch of leaf disc forging pieces, and dissecting along the radial and axial directions of the forging pieces; respectively cutting microstructure samples with different sizes at least at the positions of the blade, the rim, the web plate and the hub; preprocessing each microstructure sample to prepare a surface to be tested; and carrying out microscopic structure test on each inspection surface by adopting optical microscopes with different multiples, and analyzing whether the parameter characteristics of the beta grains and the alpha grains are qualified or not, and meeting preset conditions. The invention improves the production quality efficiency of the Ti60 titanium alloy blisk.
Description
Technical Field
The invention belongs to the technical field of aeroengine key material and part manufacturing, and particularly relates to a method for checking and controlling production quality of a Ti60 titanium alloy blisk.
Background
The Ti60 titanium alloy is a high-temperature titanium alloy which is independently designed and developed in China and can work at 600 ℃ for a long time. The alloy is a multi-element composite reinforced near alpha-type titanium alloy, and has high heat resistance, specific strength and good fatigue performance at the high temperature of 500-600 ℃. The alloy is suitable for manufacturing key parts such as integral vane disks, casing and the like of the gas compressor.
The integral vane disk of the air compressor is a structure adopted for improving the performance and reducing the weight of the advanced aeroengine. The blisk combines the traditional wheel disc and blade separation structure into a whole, so that the number of parts can be greatly reduced, the weight of the structure is reduced, and the pneumatic efficiency and the working reliability of the compressor are improved. The integral vane disk of the air compressor has high work load and complex stress state, and has very strict requirements on the performance of materials. When the Ti60 titanium alloy is adopted to manufacture the blisk, the performance control needs to be considered at different positions such as the blade, the rim and the disk body. The Ti60 titanium alloy is required to have good vibration fatigue resistance and thermal stability at the blade part of the blisk, excellent durable creep resistance at the rim part, and good low cycle fatigue resistance at the disk part.
The thermal processing parameters of the Ti60 titanium alloy blisk have important influences on the microstructure and mechanical properties of the blisk, are influenced by a forging process and a heat treatment process, and when the process parameters fluctuate excessively, the abnormal structure of the Ti60 titanium alloy blisk is easily caused, the mechanical properties of the blisk are correspondingly caused to exceed the standard, and the use of the blisk for a loader is risked.
Disclosure of Invention
In view of the above, the invention provides a method for checking and controlling the production quality of the Ti60 titanium alloy blisk, which can judge the rationality and the parameter stability of the hot working process after the microstructure of the Ti60 titanium alloy blisk is checked, ensure that each mechanical property of the blisk meets the use requirement and improve the production efficiency of the Ti60 titanium alloy blisk.
A method for checking and controlling the production quality of a Ti60 titanium alloy blisk is provided, the method comprising:
carrying out die forging process treatment, solution heat treatment and aging heat treatment on a plurality of batches of blanks, and forming a blisk forging of the Ti60 titanium alloy;
extracting 1 forging piece from each batch of leaf disc forging pieces, and dissecting along the radial and axial directions of the forging pieces;
respectively cutting microstructure samples with different sizes at least at the positions of the blade, the rim, the web plate and the hub;
preprocessing each microstructure sample to prepare a surface to be tested;
and carrying out microscopic structural test on each inspection surface by adopting optical microscopes with different multiples, and analyzing whether the parameter characteristics of the beta grains and the alpha grains are qualified or not, wherein the requirements are satisfied:
a) The microstructure should be a structure formed by processing an alpha+beta two-phase region, namely, a low-aspect ratio primary alpha phase is uniformly distributed on a matrix of a beta transition structure;
b) The microstructure has no flat continuous and coarse network grain boundary alpha phase, and the size of the original beta grains is between 0.05 and 0.4 mm;
c) The content of primary alpha phase in the microstructure is between 5 and 35 percent;
d) When the aspect ratio of the primary alpha phase is more than 3, the length of the primary alpha phase is less than 0.5mm;
e) When the primary alpha phase is in the form of a block, its largest dimension is less than 0.25mm.
The invention has the beneficial effects that:
1) The content, morphology and size of primary alpha phase in the microstructure of the Ti60 titanium alloy blisk are mainly influenced by the forging process and the heat treatment process. The microstructure inspection result provided by the invention can well reflect the rationality of the Ti60 titanium alloy blisk forging and heat treatment process and the accuracy of parameter control.
2) The content, morphology and size of the primary alpha phase in the microstructure of the Ti60 titanium alloy blisk can influence the mechanical properties of the blisk to a great extent. The invention provides an optimal control range of the Ti60 titanium alloy blisk microstructure, and when the microstructure does not meet the requirements provided by the invention, the mechanical property of the microstructure is difficult to meet the requirements of acceptance indexes. Therefore, the invention can control the comprehensive mechanical property of the Ti60 blisk to a great extent.
3) Compared with mechanical property inspection such as strength, toughness, fatigue, creep and the like, the microscopic structure inspection has the advantages of low cost, short period, visual inspection result and the like, so the method provided by the invention is suitable for quality control in the whole She Panpi quantification and engineering production process of the Ti60 titanium alloy.
4) The microstructure control method provided by the invention can ensure that the mechanical properties of the Ti60 titanium alloy blisk reach the following indexes to a great extent: tensile Strength Sigma at room temperature b Not less than 950MPa, yield strength sigma 0.2 Not less than 880MPa, and extensibility delta 5 More than or equal to 6 percent, the reduction of area psi is more than or equal to 15 percent, and K is at room temperature t Intensity deficiency ratio sigma when=3 bH /σ b Not less than 1.25 and room temperature fracture toughness K IC ≥35MPa·m 1/2 And a test stress (. Sigma.) at 600 ℃ of 150MPa and a test time (. Tau.) of 100h p ) And a thermal stability elongation delta of less than or equal to 0.2% after heating at 600 ℃ for 100 hours 5 More than or equal to 3 percent, and the area shrinkage psi is more than or equal to 6 percent.
5) The microstructure control method provided by the invention can reflect whether the thermal processing range of the blisk forging blank is in a reasonable range to a great extent, for example: the metal temperature of each part of the blank in the die forging process is at the phase transition temperature T β In the range of 40-70 ℃, the forging deformation of different parts of the blank is controlled within the range of 35-70%. The temperature of the forging solid solution treatment is at the phase transition temperature T β The temperature is 15-30 ℃ below, and the heat preservation time is 2-4 h.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present disclosure, the drawings that are needed in the embodiments will be briefly described below, and it is obvious that the drawings in the following description are only some embodiments of the present disclosure, and other drawings may be obtained according to these drawings without inventive effort to a person of ordinary skill in the art.
FIG. 1 is a schematic diagram of a microstructure inspection sampling position of a Ti60 titanium alloy monolithic forging;
FIG. 2 is a typical microstructure of a blade in a Ti60 titanium alloy monolithic forging;
FIG. 3 is a typical microstructure of a rim in a Ti60 titanium alloy monolithic forging;
FIG. 4 is a typical microstructure of a web in a Ti60 titanium alloy monolithic forging;
FIG. 5 is a typical microstructure of a hub in a Ti60 titanium alloy monolithic forging;
FIG. 6 is a microstructure of a blade in a Ti60 titanium alloy monolithic forging of the present invention;
FIG. 7 is a microstructure of the rim in the Ti60 titanium alloy monolithic forging of the present invention;
FIG. 8 is a microstructure of a web in a Ti60 titanium alloy monolithic forging of the present invention;
FIG. 9 is a microstructure of a hub in a Ti60 titanium alloy monolithic forging of the present invention;
FIG. 10 is a microstructure of the rim of comparative example 1;
FIG. 11 is a microstructure of the web of comparative example 1;
an excessively high forging temperature in comparative example 2 of fig. 12 resulted in a microstructure in which the content of primary alpha phase was excessively small and the grain boundary alpha phase was flat and coarse.
Detailed Description
Embodiments of the present disclosure are described in detail below with reference to the accompanying drawings.
Other advantages and effects of the present disclosure will become readily apparent to those skilled in the art from the following disclosure, which describes embodiments of the present disclosure by way of specific examples. It will be apparent that the described embodiments are merely some, but not all embodiments of the present disclosure. The disclosure may be embodied or practiced in other different specific embodiments, and details within the subject specification may be modified or changed from various points of view and applications without departing from the spirit of the disclosure. It should be noted that the following embodiments and features in the embodiments may be combined with each other without conflict. All other embodiments, which can be made by one of ordinary skill in the art without inventive effort, based on the embodiments in this disclosure are intended to be within the scope of this disclosure.
It is noted that various aspects of the embodiments are described below within the scope of the following claims. It should be apparent that the aspects described herein may be embodied in a wide variety of forms and that any specific structure and/or function described herein is merely illustrative. Based on the present disclosure, one skilled in the art will appreciate that one aspect described herein may be implemented independently of any other aspect, and that two or more of these aspects may be combined in various ways. For example, an apparatus may be implemented and/or a method practiced using any number of the aspects set forth herein. In addition, such apparatus may be implemented and/or such methods practiced using other structure and/or functionality in addition to one or more of the aspects set forth herein.
The method for checking and controlling the production quality of the Ti60 titanium alloy blisk shown in FIG. 1 is preferably suitable for detecting or controlling the blisk with the primary alpha phase of the Ti60 titanium alloy between 5% and 35%, and comprises the following steps:
s101: the multiple batches of blanks are subjected to die forging process treatment, solution heat treatment and aging heat treatment, and the integral blisk forgings of the Ti60 titanium alloy are formed, for example:
die forging process treatment, wherein the metal temperature of each part of the blank is controlled at a phase transition temperature T β In the range of 40-70 ℃, the forging deformation of different parts of the blank is controlled in the range of 35-75%;
solution heat treatment, wherein the temperature of blank solution treatment is 15-30 ℃ below the phase transition temperature Tbeta, the heat preservation time is 2-4 h, and the cooling mode is air cooling;
and (3) aging heat treatment, namely adopting the process treatment in the prior art.
S102: 1 piece of forging is extracted from each batch of impeller forgings, and is dissected along the radial direction, at least the parts of the blade 1, the rim 2, the web 3 and the hub 4 are respectively cut into microstructure samples with different sizes, for example, at least the four different parts of the blade, the rim, the web and the hub are respectively cut into microstructure samples with phi 30mm multiplied by 20mm or 20mm multiplied by 20 mm;
s103: each microstructure sample is preprocessed to prepare a surface to be detected, for example, an optical microscope with the magnification of 100 times and 200 times is adopted to carry out microstructure test on each detection surface, so that the detection precision is improved;
s104: and carrying out microscopic structural tests on each test surface by adopting optical microscopes with different multiples, and analyzing whether the parameter characteristics of the beta grains and the alpha grains are qualified or not, wherein the primary alpha range of the Ti60 titanium alloy is within the range of 5-35%, and the requirements are satisfied:
a) The microstructure should be a structure formed by processing an alpha+beta two-phase region, namely, a low-aspect ratio primary alpha phase is uniformly distributed on a matrix of a beta transition structure;
b) The microstructure has no flat continuous and coarse network grain boundary alpha phase, and the size of the original beta grains is between 0.05 and 0.4 mm;
c) The content of the primary alpha phase in the microstructure is between 5% and 35%, that is, when the content of the primary alpha phase is lower than the range, the high cycle fatigue performance and plasticity (elongation and section shrinkage) of the Ti60 alloy are difficult to meet the index requirements and the use requirements. When the content of the primary alpha phase is higher than this range, creep property and fracture toughness of the Ti60 alloy will hardly meet the index requirements and the use requirements;
d) When the aspect ratio of the primary alpha phase is greater than 3, its length should be less than 0.5mm. When exceeding the range, the high cycle fatigue property of the Ti60 titanium alloy will not meet the index requirements and the use requirements;
e) When the primary alpha phase is in the form of a block, its largest dimension is less than 0.25mm. When the range is exceeded, the heat stability and low cycle fatigue properties of the Ti60 titanium alloy are severely degraded.
Example 1
Examples: ti60 titanium alloy blisk forging with good comprehensive mechanical properties
The Ti60 titanium alloy blisk forging is made of bars with the diameter of 300 mm.
The bars are subjected to near-isothermal die forging and solid solution aging heat treatment according to the control range provided by the invention after forging, and then the compressor blisk forging is prepared. The forging was dissected, and microstructure samples were cut at the blade 1, rim 2, web 3, and hub 4 as shown in fig. 1, and denoted as blade-site grain size test sample 5, rim-site grain size test sample 6, web-site grain size test sample 7, and hub-site grain size test sample 8. The microstructure samples were polished, etched and analyzed under a 100-fold optical microscope, as shown in fig. 2-4, and expressed as standard or typical microstructural maps for 4 sites with 5%, 15%, 25% and 35% primary α, respectively. The 4 parts are microstructures formed by processing an alpha+beta two-phase region, and the equiaxed or elliptic primary alpha phases are uniformly distributed on a matrix of the beta transformation structure. Although the grain boundary alpha phase in the microstructure is relatively obvious, the grain boundary alpha phase is curved and discontinuously distributed. The size of the original beta grains is between more than 0.08mm and 0.2 mm.
The method of the invention is controlled, for example, the primary alpha phase content of the blade 1 and the rim 2 is 18% (see fig. 6 and 7), the primary alpha phase content of the web 3 is 20% (see fig. 8), and the primary alpha phase content of the hub 4 is 23% (see fig. 9). The web 3 and the hub 4 have a small amount of oval primary alpha phase with an aspect ratio exceeding 3, which is not fully spheroidized, but the maximum length of the oval primary alpha phase is not more than 0.15mm. No blocky primary alpha phase with the size of 0.25mm exists in the microstructure of each part.
The properties after the above test are shown in Table 1, as follows:
TABLE 1
Table 1 shows the comprehensive mechanical properties of the blisk, and the microstructure of the blisk forging is good according to various parameters, and the comprehensive mechanical properties of the forging are good after mechanical property inspection, wherein the microstructure inspection control requirements provided by the invention are met.
Comparative example 1:
near isothermal forging is performed in the control range proposed by the present invention. The solid solution temperature of the forging is T β The solid solution time is 2 hours at 45 ℃ below, and the cooling mode is oil cooling. And (5) carrying out aging heat treatment on the forging after solid solution to prepare the compressor blisk forging. The forging was dissected, and the microstructure samples were cut out from the blade 1, rim 2, web 3 and hub 4 shown in fig. 1, and the microstructure photographs of the web and rim portions were shown in fig. 10 and 11, respectively, and analyzed under a microscope at a magnification of 100. The primary alpha phase content at the rim 2 portion is 43% (see fig. 10), and the primary alpha phase content at the web 3 portion is 57% (see fig. 11). Because the temperature of the solution treatment is too low, the content of primary alpha phase in each part of the Ti60 titanium alloy blisk forging is higher. The mechanical properties of the forgings were tested for poor fracture toughness and high temperature creep properties, and the test results are shown in Table 2 (mechanical properties of blisks with too high content of primary alpha phase).
TABLE 2
Comparative example 2:
ti60 titanium alloyWhen the blisk blank is die forged at 990 ℃, the content of primary alpha phase in the forging is about 25%. As the temperature of the blank increases, the content of primary alpha phase in the forging is reduced, and the size is reduced. This is related to the phase transition during heating and deformation. When the temperature of the blank in the die forging process exceeds the phase transition point T β Below 10 ℃, the content of primary alpha phase in the forging after solution failure treatment is less than 5% and the grain boundary alpha phase is flat and coarse, as shown in fig. 12. The forging heat stability of this microstructure will be poor as shown in table 3 (heat stability of a microstructure with too little primary alpha phase content and a flat and coarse grain boundary alpha phase).
TABLE 3 Table 3
The above is merely a specific embodiment of the disclosure, but the protection scope of the disclosure is not limited thereto, and any changes or substitutions easily conceivable by those skilled in the art within the technical scope of the disclosure are intended to be covered in the protection scope of the disclosure. Therefore, the protection scope of the present disclosure shall be subject to the protection scope of the claims.
Claims (7)
1. A method for verifying and controlling production quality of a Ti60 titanium alloy blisk, the method comprising:
carrying out die forging process treatment, solution heat treatment and aging heat treatment on a plurality of batches of blanks, and forming a blisk forging of the Ti60 titanium alloy;
extracting 1 forging piece from each batch of leaf disc forging pieces, and dissecting along the radial and axial directions of the forging pieces;
respectively cutting microstructure samples with different sizes at least at the positions of the blade, the rim, the web plate and the hub;
preprocessing each microstructure sample to prepare a surface to be tested;
and carrying out microscopic structural test on each inspection surface by adopting optical microscopes with different multiples, and analyzing whether the parameter characteristics of the beta grains and the alpha grains are qualified or not, wherein the requirements are satisfied:
a) The microstructure should be a structure formed by processing an alpha+beta two-phase region, namely, a low-aspect ratio primary alpha phase is uniformly distributed on a matrix of a beta transition structure;
b) The microstructure has no flat continuous and coarse network grain boundary alpha phase, and the size of the original beta grains is between 0.05 and 0.4 mm;
c) The content of primary alpha phase in the microstructure is between 5 and 35 percent;
d) When the aspect ratio of the primary alpha phase is more than 3, the length of the primary alpha phase is less than 0.5mm;
e) When the primary alpha phase is in the form of a block, its largest dimension is less than 0.25mm.
2. The method of claim 1, wherein the swaging process comprises:
the metal temperature of each part of the blank is controlled to be the phase transition temperature T β In the range of 40-70 ℃, the forging deformation of different parts of the blank is controlled within the range of 35-75%.
3. The method of claim 1, wherein the solution heat treatment comprises:
the temperature of the blank solid solution treatment is within the range of 15-30 ℃ below the phase transition temperature Tbeta, the heat preservation time is within the range of 2-4 h, and the cooling mode is air cooling.
4. The method of claim 1, wherein microscopic tissue samples of Φ30mm x 20mm or 20mm x 20mm are cut at least at four different locations of the blade, rim, web, and hub, respectively.
5. The method of claim 1, wherein each of said test surfaces is subjected to a microstructural test using an optical microscope at a magnification of 100 and 200.
6. The method of claim 1, wherein the mechanical properties of the Ti60 titanium alloy blisk prepared satisfy:
tensile Strength Sigma at room temperature b Not less than 950MPa, yield strength sigma 0.2 Not less than 880MPa, and extensibility delta 5 Not less than 6%, the reduction of area psi not less than 15%, and K at room temperature t Intensity deficiency ratio sigma when=3 bH /σ b Not less than 1.25, room temperature fracture toughness K IC ≥35MPa·m 1/2 。
7. The method according to claim 6, wherein the prepared Ti60 titanium alloy blisk has a residual strain epsilon at 600 ℃ under a test stress sigma of 150MPa and a test time tau of 100h p And a thermal stability elongation delta of less than or equal to 0.2% after heating at 600 ℃ for 100 hours 5 More than or equal to 3 percent, and the area shrinkage psi is more than or equal to 6 percent.
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