CN117026122A - Titanium alloy with tri-state structure and preparation method thereof - Google Patents
Titanium alloy with tri-state structure and preparation method thereof Download PDFInfo
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- CN117026122A CN117026122A CN202311026596.8A CN202311026596A CN117026122A CN 117026122 A CN117026122 A CN 117026122A CN 202311026596 A CN202311026596 A CN 202311026596A CN 117026122 A CN117026122 A CN 117026122A
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 56
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 238000011282 treatment Methods 0.000 claims abstract description 76
- 238000001816 cooling Methods 0.000 claims description 46
- 238000004321 preservation Methods 0.000 claims description 43
- 229910045601 alloy Inorganic materials 0.000 claims description 35
- 239000000956 alloy Substances 0.000 claims description 35
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 12
- 229910001040 Beta-titanium Inorganic materials 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 39
- 238000010438 heat treatment Methods 0.000 abstract description 33
- 230000008569 process Effects 0.000 abstract description 28
- 230000004888 barrier function Effects 0.000 abstract description 3
- 239000000463 material Substances 0.000 description 18
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 16
- 230000000052 comparative effect Effects 0.000 description 15
- 229910000734 martensite Inorganic materials 0.000 description 14
- 238000005265 energy consumption Methods 0.000 description 7
- 238000005096 rolling process Methods 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 230000001105 regulatory effect Effects 0.000 description 4
- 230000002195 synergetic effect Effects 0.000 description 4
- 238000010146 3D printing Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000009776 industrial production Methods 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 238000007639 printing Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000003814 drug Substances 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 230000000644 propagated effect Effects 0.000 description 1
- 230000035484 reaction time Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000007017 scission Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Classifications
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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
- C22F3/00—Changing the physical structure of non-ferrous metals or alloys by special physical methods, e.g. treatment with neutrons
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
Abstract
The invention provides a titanium alloy with tri-state structure and a preparation method thereof, comprising the following steps: the method uses pulse current treatment and conventional heat treatment to break the barrier that the tri-state structure forms the needed high-density dislocation, and can successfully prepare the tri-state structure in the titanium alloy by only two steps, thereby realizing the rapid preparation of the tri-state structure in a short process. The net shape of the sample obtained by the treatment of the invention is not changed, and the titanium alloy with tri-state structure is obtained under the condition that the net shape of the workpiece is not destroyed. The ternary-structure titanium alloy obtained by the invention has excellent strength and plasticity, wherein the tensile strength is 1100-1130MPa, and the elongation is 18.5-23%.
Description
Technical Field
The invention belongs to the technical field of microstructure regulation and control of metal materials, and particularly relates to a titanium alloy with a tri-state structure and a preparation method thereof.
Background
The titanium alloy has the advantages of high specific strength, good corrosion resistance, high temperature resistance, good biocompatibility and the like, and is a metal material widely applied to the fields of aerospace and medicine. The comprehensive mechanical properties of the titanium alloy are strongly correlated with the microstructure thereof. Titanium alloys currently mainly include five typical structures: equiaxed structure, basket structure, widmannstatted structure, bi-state structure and tri-state structure, wherein the tri-state structure composed of equiaxed alpha grains, layered alpha grains and martensitic grains integrates the advantages of equiaxed structure and basket structure. The titanium alloy sample with the tri-state structure has good strength, plasticity, excellent fatigue resistance and creep resistance.
The existing method for preparing titanium alloy with tri-state structure mainly comprises the steps of firstly, carrying out high-temperature deformation (such as isothermal compression, high-temperature rolling and the like) on conventional titanium alloy, and then carrying out multi-stage long-time high-temperature heat treatment; secondly, preparing the titanium alloy powder into a sample by using an additive manufacturing technology (such as selective laser melting), and then performing multi-step and long-time heat treatment. The first method requires introducing dislocations by deformation, will destroy the net shape of the workpiece, and cannot be applied to the shaped workpiece; the second method enables the preparation of a tri-state structure only for 3D printed titanium alloys with high dislocation density, whereas annealed titanium alloys (without high dislocation density) commonly used in industry cannot. In addition, both processes require long-time high-temperature treatment, and the high-temperature long-time heat treatment prolongs the production flow, increases the time cost and the energy consumption, and therefore limits the industrial production of titanium alloys with tri-state structures. At present, the realization of short-process preparation of titanium alloy with tri-state structure is a technical problem to be solved in industrial production under the conditions of ensuring the net shape of a workpiece and reducing energy consumption.
Disclosure of Invention
In order to solve the technical problems, the invention provides a titanium alloy with a tri-state structure, and the preparation method comprises the following steps:
cooling the titanium alloy after pulse current treatment, wherein the pulse current treatment is as follows: the frequency is 50-2000Hz, the voltage is 3-18V, and the current density is 1X 10 7 ～1×10 8 A/m 2 The processing time is 300ms-2s; and then carrying out heat preservation treatment and cooling to obtain the titanium alloy with the tri-state structure, wherein the heat preservation treatment comprises the following steps: temperature: 600-980 ℃, the treatment time is as follows: 0.5-3h.
Further, the titanium alloy in the step (1) is an alpha titanium alloy or an alpha+beta titanium alloy.
Further, the voltage in the step (1) is 4-15V.
Further, the current density in the step (1) is 3×10 7 ～7×10 7 A/m 2 。
Further, the processing time in the step (1) is 360ms-480ms.
Further, the pulse current in the step (1) is alternating current or direct current.
Further, the temperature of the heat preservation treatment in the step (2) is 850-960 ℃.
Further, the heat preservation treatment time in the step (2) is 1-2 h.
Further, the cooling process in the step (2) is water cooling or air cooling.
Compared with the prior art, the invention does not need to deform the sample or carry out special process (such as 3D printing) or high-temperature long-time heat treatment, does not influence the net shape of the sample, and does not cause the problem of cracking or failure caused by deformation treatment. Compared with 3D printed titanium alloy, the production cost of the invention is far lower than the cost consumed by 3D printed titanium alloy; in addition, the processing time required by the method is less than that of the prior art, and the short-flow rapid preparation of the tri-state tissue alloy is realized. In addition, compared with the prior art, the tri-state tissue alloy prepared by the method has more excellent performance. The specific advantages are as follows:
1. the three-state structure is successfully prepared in the titanium alloy by adopting a short-flow process through the synergistic effect of pulse current treatment, heat treatment and related parameters, so that the purpose of rapidly preparing the three-state structure in a short flow is achieved; the pulse current treatment process has the characteristics of low voltage, high stability, high power, small loss, low cost and the like, and can be continuously, stably and adjustably in the rated pulse current treatment range.
2. The conventional commercial alpha-type and alpha+beta-type titanium alloy cannot use a pure heat treatment process to generate a tri-state structure, mainly because the titanium alloy and the titanium alloy do not have a high-density dislocation structure generated after deformation treatment or 3D printing, the invention breaks through the barrier of high-density dislocation required by tri-state structure formation through the synergistic effect of a pulse current treatment technology, a heat treatment technology and related parameters, and the tri-state structure is generated by spheroidizing lamellar alpha grains and the volume fraction and the size of equiaxial alpha grains are regulated, so that the preparation of the tri-state structure can be realized under the condition that the net shape of a workpiece is not destroyed. The equiaxed grains are generated by cylindricization of lamellar grains, so that dispersed equiaxed alpha grains with smaller size can be obtained by adjusting the process and related parameters, in addition, different microstructures (martensite/secondary alpha grains) can be generated, the hardness difference between the martensite and the equiaxed alpha/lamellar alpha grains causes the phenomenon of strain distribution in the deformation process of the material, and finally, different requirements of remarkably improving the strength/plasticity of the sample are realized.
3. The prepared alloy with the tri-state structure has excellent performance through the synergistic effect of pulse current treatment and heat treatment technology and related parameters. The tensile strength of the titanium alloy prepared by the method is 1100-1130MPa, and the elongation is 18.5% -23%, which are respectively higher than the tensile strength and the elongation of the tri-state tissue alloy obtained by the prior art.
Drawings
FIG. 1 is a microstructure of a titanium alloy obtained in example 2.
Detailed Description
The invention will now be described in further detail with reference to the accompanying drawings in conjunction with specific embodiments, which are intended to illustrate, but not limit, the scope of the invention.
Example 1
The Ti-6.5Al-3.8V alloy was subjected to pulse current treatment. The pulse current treatment is as follows: the frequency is 100Hz, the voltage is 4.5V, and the current density is 3 multiplied by 10 7 A/m 2 The processing time is 420ms; after pulse current treatment, cooling the sample to room temperature by using water cooling, then placing the sample into a tube furnace for two-phase region heat preservation treatment, taking the heat preserved sample out of the furnace, and placing the sample into water for cooling to obtain titanium alloy 1, wherein the heat preservation treatment is as follows: the temperature is 940 ℃ and the treatment time is 1h. The volume fractions of equiaxed grains, lamellar grains and martensitic grains of the sample with a tri-state structure obtained after the treatment were 16%, 44% and 40%, respectively, the tensile strength was 1110MPa, and the elongation was 20%.
Example 2
Carrying out pulse current treatment on Ti-6Al-4V alloy, wherein the pulse current treatment is as follows: the frequency is 50Hz, the voltage is 5V, and the current density is 4.7X10 7 A/m 2 The processing time is 400ms; after pulse current treatment, cooling the sample to room temperature by using water cooling, then placing the sample into a tube furnace for two-phase region heat preservation treatment, taking the heat preserved sample out of the furnace, and placing the sample into water for cooling to obtain titanium alloy 1, wherein the heat preservation treatment is as follows:
the temperature is 950 ℃ and the treatment time is 2 hours. The tensile strength of the sample with the tri-state structure obtained after the treatment is 1130MPa, and the elongation is 23%.
FIG. 1 shows a Ti-6Al-4V alloy with a tri-state structure prepared by the process of example 2. It can be observed from FIG. 1 that the grains of the Ti-6Al-4V alloy treated by the process of example 2 consist of equiaxed alpha grains, lamellar alpha grains and martensitic grains. The volume fractions of equiaxed, lamellar and martensitic grains are about 25%, 35% and 40%. The tri-state structure alloy having this ratio has excellent strength (1130 MPa) and elongation (23%) due to the presence of equiaxed grains and the distribution of strain between alpha grains and martensite.
Example 3
Carrying out pulse current treatment on Ti-6Al-4V alloy, wherein the pulse current treatment is as follows: the frequency is 50Hz, the voltage is 4V, and the current density is 2.4X10 7 A/m 2 The processing time is 440ms; cooling the sample to room temperature by using water cooling after pulse current treatment, then placing the sample into a tube furnace for two-phase region heat preservation treatment, taking out the heat-preserved sample from the furnace, and placing the sample into a tube furnaceThe titanium alloy 1 is obtained after cooling in water, and the heat preservation treatment is as follows:
the temperature is 960 ℃, and the treatment time is 2.5 hours. The tensile strength of the sample with the tri-state structure obtained after the treatment is 1100MPa, and the elongation is 18.5%.
Comparative example 1
This comparative example was introduced from the paper The microstructure and tensileproperties of additively manufactured Ti-6Al-2Zr-1Mo-1V with a trimodalmicrostructure obtained by multiple annealing heat treatment, taught by Beijing university of science and technology Zhang Sheng, published in 2022 at Materials Science & Engineering A, cited in the range of pages 2-10. The method comprises the following specific steps:
(1) First-stage heat treatment
And (3) placing the Ti-6Al-2Zr-1Mo-1V alloy prepared by the 3D printing process into a heat treatment furnace for heat preservation treatment, and cooling to room temperature. The temperature of the heat preservation treatment is 970 ℃, the heat preservation time is 1.5h, and the cooling mode is air cooling.
(2) Two-stage heat treatment
And (3) placing the Ti-6Al-2Zr-1Mo-1V sample obtained in the step (1) into a heat treatment furnace for heat preservation treatment, and cooling to room temperature. The heat preservation treatment temperature is 930 ℃, the treatment time is 3 hours, and the cooling mode is air cooling.
(3) Three-stage heat treatment
And (3) placing the Ti-6Al-2Zr-1Mo-1V sample obtained in the step (2) into a heat treatment furnace for heat preservation treatment, and cooling to room temperature. The heat preservation treatment temperature is 600 ℃, the treatment time is 4 hours, and the cooling mode is air cooling. Microscopic structure observation is carried out on the sample after the three-stage heat treatment to find that the interior of the material is converted into a tri-state structure, and the tensile strength of the material is 1019MPa and the elongation is 16.33%.
The most essential difference between comparative example 1 and the present invention is that the generation of spherical grains in comparative example 1 is due to the cleavage of lamellar grains, and although the interior of the material is also transformed into a tri-state structure, the proportion of spherical grains is regulated depending on dislocation generated during printing of the material, and for the same composition and heat treatment process, different printing parameters may also cause variation of the proportion of spherical grains in the interior of the material. In the invention, the generation of equiaxed grains is from the growth of low-length-diameter ratio lamellar grains, and the spheroidization and growth degree can be controlled cooperatively by processes such as electric pulse and heat treatment and parameters, so the invention can realize the control of adjusting the proportion of spherical grains by controlling related processes and parameters. In addition, since the process of lamellar grain splitting requires high temperatures and long soak times to promote dislocation movement, the prior art requires high temperature long heat treatment, which results in more energy consumption. The invention realizes the short-process preparation of the tri-state structure alloy at a lower temperature in a shorter time, so the invention saves more time and energy consumption than the process of comparative example 1, and the alloy performance obtained by the invention is more excellent.
Comparative example 2
This comparative example was introduced from Tri-modal microstructure inhigh temperature toughening and low temperature strengthening treatments of near-. Beta.forged TA15 Ti-alloy, paper by the university of North-west industry, sun Zhichao, published in 2016 at Materials Characterization, and cited in the range of pages 213-221. The method comprises the following specific steps:
(1) Deformation treatment
High-temperature rolling is carried out on Ti-6Al-2Zr-1Mo-1V titanium alloy, and rolling parameters are as follows: the rolling temperature is 970 ℃, and the rolling speed is 0.1s -1 The rolling amount is 60% -65%, and the rolled sample is cooled to 835 ℃ by air and then cooled to room temperature by water.
(2) First-stage heat treatment
And (3) placing the Ti-6Al-2Zr-1Mo-1V titanium alloy obtained in the step (1) into a heat treatment furnace for heat preservation treatment, and cooling to room temperature. The heat preservation treatment temperature is 930-950 ℃, the treatment time is 0.5-1.5h, and the cooling mode is air cooling, furnace cooling and water cooling.
(3) Two-stage heat treatment
And (3) placing the Ti-6Al-2Zr-1Mo-1V titanium alloy obtained in the step (2) into a heat treatment furnace for heat preservation treatment, and cooling to room temperature. The heat preservation treatment temperature is 750-850 ℃, the treatment time is 3-8h, and the cooling mode is air cooling. And (3) observing the microstructure of the sample obtained in the step (3) to find that the interior of the material is converted into a tri-state structure, and the tensile strength of the material is 975-1010MPa.
The most essential difference between comparative example 2 and the present invention is that the spherical grains in comparative example 2 originate from the primary growth of alpha grains and the division of lamellar alpha grains remained in the interior of the material during deformation, and although the interior of the material is also transformed into a tri-state structure, the proportion of lamellar grains and spherical grains needs to be regulated by introducing deformation, and this process can destroy the shape of the material itself, and is obviously unsuitable for alloys with service shapes after processing. The process of the present invention hardly changes the net shape of the material (i.e., the deformation process of comparative example 2 is not employed), and is therefore more suitable for the modification process of alloys having a service shape. In addition, high temperature deformation and long post heat treatment result in more energy consumption, and a large deformation device will have special requirements on the working environment. The pulse current and the heat treatment process used by the invention have no special requirements on the working environment. In addition, the heat treatment time required by the invention is shorter, and the energy consumed by the working of the electric pulse equipment is also far smaller than that of the deformation equipment, so the invention saves more time and energy consumption than the process of comparative example 2, and the performance of the alloy is superior to that of the prior art.
Comparative example 3
(1) First-stage heat treatment
Carrying out heat preservation treatment on Ti-6Al-4V alloy by using a tube furnace, wherein the heat preservation treatment parameters are as follows: the temperature is 970 ℃, the heat preservation time is 1.5h, and the cooling mode is water cooling.
(2) Two-stage heat treatment
Carrying out heat preservation treatment on the Ti-6Al-4V alloy obtained in the step (1) by using a tube furnace, wherein the heat preservation treatment parameters are as follows: the temperature is 930 ℃, the heat preservation time is 3 hours, and the cooling mode is air cooling.
(3) Three-stage heat treatment is carried out,
carrying out heat preservation treatment on the Ti-6Al-4V alloy obtained in the step (2) by using a tube furnace, wherein the heat preservation treatment parameters are as follows: the temperature is 600 ℃, the heat preservation time is 4 hours, and the cooling mode is air cooling. The tensile strength of the obtained Ti-6Al-4V alloy is 1040MPa, and the elongation is 16%.
The most essential difference between comparative example 3 and the present invention is that for the conventional rolled annealed Ti-6Al-4V alloy, the three-stage heat treatment can only convert the material into a dual-state structure with primary alpha grains and lamellar alpha grains, and the structure is not substantially different from the structure generated by the solid solution-aging (STA) treatment commonly used in the current titanium alloy, so that the mechanical property of the titanium alloy is also represented as the mechanical property of the dual-state structure (the tensile strength is 1040MPa, the elongation is 16%), and the tri-state structure cannot be formed. The strength and the elongation of the Ti-6Al-4V alloy with the tri-state structure obtained by the invention are obviously higher than those of the Ti-6Al-4V alloy with the tri-state heat treatment. This is because the tri-state structure is more uniformly dispersed and forms smaller sized equiaxed alpha phases and martensite grains, which will contribute to the strength and plasticity of the material. In addition, spherical grains in the Ti-6Al-4V alloy subjected to tertiary heat treatment are primary alpha grains which are not phase-changed in heat preservation treatment, and the grains grow up during heat preservation, so that the strength of the alloy is reduced; the spherical grains are spheroidized by the lamellar grains with lower length-diameter ratio, so that the spherical grains are smaller in size and more dispersed, and the alloy has more excellent performance.
Comparative example 4
(1) Solution treatment of
Carrying out heat preservation treatment on Ti-6Al-4V alloy by using a tube furnace, wherein the heat preservation treatment parameters are as follows: the temperature is 950 ℃, the heat preservation time is 2 hours, and the cooling mode is water cooling.
(2) Aging treatment
Carrying out heat preservation treatment on the Ti-6Al-4V alloy obtained in the step (1) by using a tube furnace, wherein the heat preservation treatment parameters are as follows: the temperature is 530 ℃, the heat preservation time is 2 hours, and the cooling mode is air cooling. The tensile strength of the obtained Ti-6Al-4V alloy is 1020MPa, and the elongation is 18.1%.
Comparative example 4 is a solution-aging (STA) treatment currently commonly used in dual phase titanium alloys. But the tristate structure strength and plasticity prepared by the combination process are better than those of Ti-6Al-4V alloy treated by STA. This is because the tri-state structure produced by the invention contains martensite, and the hardness difference between the martensite and the spherical alpha/lamellar alpha grains can cause the phenomenon of strain distribution of the material in the deformation process, so that the elongation of the alloy is increased; in addition, cracks are hindered by martensite having different orientations as the martensitic regions are propagated, which increases the crack propagation resistance of the alloy and thus increases the elongation at break. The strength is improved due to the reduction of the grain size, and the lamellar grains in the tri-state structure have an inhibition effect on dislocation movement, so that the tensile strength is improved.
To sum up: compared with the prior art, the preparation method reduces the reaction energy consumption and shortens the reaction time by the synergistic effect of the process and the parameters, and realizes the preparation of the tri-state tissue titanium alloy in a short process; in addition, under the condition that the net shape of the workpiece is not damaged, the barrier that the tri-state structure obtained in the prior art needs high-density dislocation is broken, the tri-state structure is generated by means of spheroidization of lamellar alpha grains, the volume fraction and the size of the equiaxed alpha grains are regulated and controlled, and the equiaxed grains are obtained through cylindricization of the lamellar grains, so that the equiaxed grains are dispersed and have finer sizes, in addition, different microstructures (martensite/secondary alpha grains) can be generated, and the phenomenon that the strain distribution occurs in the deformation process of the material due to the hardness difference between the martensite and the spherical alpha/lamellar alpha grains is finally and synchronously and obviously improved; the mechanical property and the plasticity of the titanium alloy obtained by the invention are better than those of the alloy obtained by the prior art.
Finally, it is to be understood that the above embodiments are only for illustrating the technical solution of the present invention and not for limiting the same, and it should be understood by those skilled in the art that modifications and equivalents may be made thereto without departing from the spirit and scope of the technical solution of the present invention, which is intended to be covered by the claims of the present invention.
Claims (9)
1. A titanium alloy having a tri-state structure, characterized in that: the preparation method comprises the following steps:
cooling after carrying out pulse current treatment on the titanium alloy, wherein the pulse current treatment is as follows: the frequency is 50-2000Hz, and the voltage is 3-18V, current density of 1×10 7 ～1×10 8 A/m 2 The processing time is 300ms-2s; then carrying out heat preservation treatment and cooling to obtain the titanium alloy with the tri-state structure, wherein the heat preservation treatment temperature is as follows: 600-980 ℃, and the heat preservation treatment time is as follows: 0.5-3h.
2. A titanium alloy having a tri-state structure according to claim 1, wherein: the titanium alloy is alpha titanium alloy or alpha+beta titanium alloy.
3. A titanium alloy having a tri-state structure according to claim 1, wherein: the voltage is 4-15V.
4. A titanium alloy having a tri-state structure according to claim 1, wherein: the current density is 3×10 7 ～7×10 7 A/m 2 。
5. A titanium alloy having a tri-state structure according to claim 1, wherein: the processing time is 360ms-480ms.
6. A titanium alloy having a tri-state structure according to claim 1, wherein: the pulse current is alternating current or direct current.
7. A titanium alloy having a tri-state structure according to claim 1, wherein: the heat preservation treatment temperature is 850-960 ℃.
8. A titanium alloy having a tri-state structure according to claim 1, wherein: the heat preservation treatment time is 1h-2h.
9. A titanium alloy having a tri-state structure according to claim 1, wherein: the cooling is water cooling or air cooling.
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