CN112063887A - Multifunctional titanium alloy, preparation method and application thereof - Google Patents
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Abstract
The application relates to the technical field of titanium alloy, in particular to a multifunctional titanium alloy, a preparation method and application thereof. The application discloses a preparation method of a titanium alloy, which comprises the following steps: step a, smelting and preparing the titanium alloy according to alloy components in the multifunctional titanium alloy, wherein the alloy components comprise: 2-20 wt% of Nb, 3-8 wt% of Zr, 2-6 wt% of Sn, 0.5-3 wt% of Fe, 0.1-0.7 wt% of O and the balance of Ti; b, thermally deforming the titanium alloy in an alpha + beta two-phase region; c, annealing heat treatment is carried out on the titanium alloy after thermal deformation; and d, pre-deforming the titanium alloy subjected to annealing heat treatment to obtain the multifunctional titanium alloy, and solving the technical problems that the existing alloy cannot have both functionality and structure due to mutual repulsion of elastic functionality and high strength, and high elasticity and high strength are difficult to realize in the same alloy.
Description
Technical Field
The application relates to the technical field of new materials, in particular to a titanium alloy and a preparation method thereof, and specifically relates to a multifunctional titanium alloy with wide strain range superelasticity, ultrahigh temperature shape memory effect, ultralow elastic modulus and high strength, a preparation method and an application thereof.
Background
With the development of science and technology and the increase of use requirements, metal parts in various fields have higher requirements. For example: in the fields of aerospace, automobiles, biomedical treatment, intelligent robots and the like, many application occasions require that metal parts have characteristics of superelasticity, shape memory effect, high elasticity, high strength and the like.
The superelasticity and shape memory effect of metallic Materials results from a reversible thermoelastic martensitic phase transformation, the stress-induced martensite will reverse back to the parent austenite upon stress unloading or heating at a certain temperature, thereby achieving the elastic functionality of superelasticity and shape memory effect (Jani J., Leary M., Subic A., Gibson M., A review of shape memory alloy research, applications and opportunities,2014, Materials and Design,56: 1078-. However, the strength, particularly the yield strength, of such metallic materials is generally low. The elasticity of a metal material is determined by its elastic modulus and yield strength, the lower the elastic modulus, the higher the yield strength, and the better the elastic deformability. Metal materials having elastic functionality such as low elastic modulus, superelasticity, and shape memory effect have low strength because of low interatomic bonding force. The mutual repulsion of elastic functionality and high strength makes it impossible to combine elastic functionality such as low elastic modulus, superelasticity and shape memory effect with high strength structural properties, making it difficult to achieve high elasticity and high strength in the same metal material, thus limiting its further applications.
In the prior art, the metastable beta Titanium alloy usually relies on stress-induced beta → alpha 'martensitic transformation and reverse transformation thereof to obtain super elasticity and shape memory effect, but performance tests show that the super elasticity is generally in a low strain range (lower than 8%), and the shape recovery temperature of the shape memory effect is generally lower than 200 ℃ (ramezanejad, A., Xu W., Xiao W.L., Fox K., Liang D., Ma Q., New instructions in organic-front subelementary Titanium alloy for biological Applications, Current optics in Solid State and Materials Science,2019,23: 100783; ramenzejad, A., Xu W., Ma Q., Ni-free subelementic Titanium alloy for the use of the medium Q., Ni-free subelementary Titanium alloy for the use of the medium and the application of high strain, and high strain requirements are not met by high-temperature environments, such as stress-induced beta → alpha' martensitic transformation and application, Ti-free subelementary Titanium alloy, and application of high strain, and high strain ranges are not met. Meanwhile, the elastic modulus of the metastable beta titanium alloy is about 50-80 GPa and far higher than 5-30 GPa of human bones, the strength is lower due to the mutual repulsion of low elastic modulus and high strength, and the elastic strain is often lower than 1.5%. High strength can be obtained by α precipitation strengthening or severe plastic deformation, but α precipitation improves strength and increases elastic modulus to 80GPa or more, making it difficult to achieve both low elastic modulus and high strength.
Therefore, it is an urgent technical problem to be solved by those skilled in the art to provide a metal material having both elastic functionality and high strength.
Disclosure of Invention
In view of the above, the present application provides a multifunctional titanium alloy, a preparation method and an application thereof, which solve the technical problems that the existing alloy cannot have both functionality and structure due to mutual repulsion of elastic functionality and high strength, and it is difficult to realize high elasticity and high strength in the same alloy.
The application provides a preparation method of a multifunctional titanium alloy in a first aspect, which comprises the following steps:
step a, determining alloy components according to the beta stability range of the multifunctional titanium alloy, enabling the alloy to generate stress-induced beta → alpha' martensite phase transformation, and smelting according to the alloy components to prepare the titanium alloy. The stability of the titanium alloy is determined by electronic parameters and molybdenum equivalent, wherein the valence electron concentration e/a range is 4.08-4.15,
The value range is 2.80 to 2.83,
The value ranges from 2.41 to 2.46, and the molybdenum equivalent is less than 6.5. The alloy comprises the following components: 2-20 wt% of Nb, 3-8 wt%Zr, 2-6 wt% of Sn, 0.5-3 wt% of Fe, 0.1-0.7 wt% of O and the balance of Ti;
b, thermally deforming the titanium alloy in an alpha + beta two-phase region to refine grains; annealing heat treatment is carried out on the titanium alloy after thermal deformation;
and c, pre-deforming the titanium alloy subjected to annealing heat treatment to obtain the multifunctional titanium alloy.
Alternatively,
the pre-deformation mode of the step c is cold deformation.
Alternatively,
the cold deformation mode comprises the following steps: pre-stretching deformation, cold rolling deformation or other cold deformation modes.
Alternatively,
and c, the deformation amount of the pre-deformation in the step c is 5-15%.
Alternatively,
and the thermal deformation temperature of the step b is 600-800 ℃.
Alternatively,
the annealing temperature in the step b is 700-800 ℃, and the annealing time is 10-120 min.
In a second aspect, the present application provides a multifunctional titanium alloy obtained by the method for preparing the multifunctional titanium alloy of the first aspect.
Alternatively,
the valence electron concentration e/a range of the multifunctional titanium alloy is 4.08-4.15,
The value range is 2.80 to 2.83,
The value range is 2.41 to 2.46.
Alternatively,
the multifunctional titanium alloy has a molybdenum equivalent of less than 6.5.
Alternatively,
the multifunctional titanium alloy comprises the following components: 2-20 wt% of Nb, 3-8 wt% of Zr, 2-6 wt% of Sn, 0.5-3 wt% of Fe, 0.1-0.7 wt% of O and the balance of Ti.
In a third aspect, the application provides an application of the multifunctional titanium alloy in aerospace high-strength high-elasticity parts and biomedical high-strength high-elasticity parts.
Compared with the prior art, the method has the following advantages:
according to the method, alloy components are determined according to beta stability of the multifunctional titanium alloy, after the titanium alloy is prepared by smelting, the titanium alloy is subjected to thermal deformation in an alpha + beta two-phase region to refine grains, then the thermal deformed titanium alloy is subjected to annealing heat treatment, and finally the annealing heat treated titanium alloy is subjected to pre-deformation to obtain the multifunctional titanium alloy. According to specific alloy components, firstly smelting to prepare a titanium alloy, then carrying out thermal deformation and annealing heat treatment on the titanium alloy, wherein the titanium alloy has wide strain range superelasticity (the superelasticity is about 3% after the deformation amount is 12%) and ultrahigh temperature shape memory effect (the shape recovery is about 2.7% at 800 ℃), then carrying out pre-deformation treatment on the titanium alloy, and the titanium alloy prepared after pre-deformation has ultralow elastic modulus and high strength, and can realize the elastic modulus as low as 29GPa, the high strength as high as 1081MPa and the high elasticity with the elastic strain limit of 3.1%. The method controls the beta stability through the specific component design, so that the titanium alloy induces the beta → alpha 'martensite phase transformation under the stress loading, realizes the wide strain range hyperelasticity and the ultrahigh temperature shape memory effect which are not possessed by the traditional hyperelasticity and shape memory titanium alloy, and simultaneously realizes the ultralow elastic modulus and the high elasticity after the titanium alloy is subjected to the low strain amount pre-deformation induction of the beta → alpha' martensite phase transformation, thereby solving the technical problems that the existing alloy cannot realize the functionality and the structure due to the mutual repulsion of the elastic functionality and the high strength, and the high elasticity and the high strength are difficult to realize in the same alloy.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present application, the drawings needed to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present application, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without inventive exercise.
FIG. 1 is a schematic flow chart of a method for preparing a multifunctional titanium alloy according to an embodiment of the present application;
FIG. 2 is a drawing of the microstructure of an annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy in an example of the present application;
FIG. 3 is a graph of cyclic tensile stress-strain for an as-annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy in an example of the present application;
FIG. 4 is an XRD pattern of a Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy after a pre-drawing deformation treatment in an example of the present application;
FIG. 5 is a diagram showing the structure of an optical lens made of a Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy after a pre-stretching deformation treatment in an example of the present application;
FIG. 6 is a tensile engineering stress-strain diagram of a Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy after a pre-stretching deformation treatment in the examples of the present application.
Detailed Description
The embodiment provides a multifunctional titanium alloy, a preparation method and application thereof, and solves the technical problems that the existing alloy has incompatible functionality and structure due to mutual repulsion of elastic functionality and high strength, and high elasticity and high strength are difficult to realize in the same alloy.
In order to make the technical solutions of the present invention better understood, the technical solutions of the present embodiment will be clearly and completely described below with reference to the drawings of the present embodiment, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application.
Referring to fig. 1, a flow chart of an embodiment of a method for preparing a multifunctional titanium alloy in the present embodiment is schematically illustrated.
It should be noted that the obtaining of the super-elastic, ultra-high temperature shape memory effect, ultra-low elastic modulus and high strength titanium alloy in this embodiment depends on having specific functional components and within the strictly limited content range, and after the fusion casting, thermal deformation and heat treatment processes in the prior art, performing the specific treatment process defined in this embodiment, so as to make the obtained alloy have all the structural changes different from any prior art, thereby obtaining the excellent specific performance desired by this embodiment. The whole process system of the embodiment of the invention is the result of the synergistic effect of all links, all parameters are mutually restricted and influenced and are in synergistic effect, and the structure and the performance of the finally obtained alloy are determined by the synergy.
The preparation method of the multifunctional titanium alloy in the embodiment includes:
Note that the alloy composition in this example includes: 2-20 wt% of Nb, 3-8 wt% of Zr, 2-6 wt% of Sn, 0.5-3 wt% of Fe, 0.1-0.7 wt% of O and the balance of Ti. In order to achieve the technical effects of the present invention, the preferred combination of the alloying elements is such that the valence electron concentration e/a of the alloy is in the range of 4.08 to 4.15,
The value range is 2.80 to 2.83,
The value is in the range of 2.41-2.46, and the molybdenum equivalent is less than 6.5, so as to ensure the stability of the alloy to enable the beta → alpha' martensitic transformation under the induction of stress.
And 102, thermally deforming the titanium alloy in an alpha + beta two-phase region.
After the titanium alloy is prepared by smelting, the titanium alloy is thermally deformed in an alpha + beta two-phase region to refine grains.
In order to ensure the beta stability and the structural state of the alloy, the heat distortion temperature of the step b is set to be 600-800 ℃ in the embodiment. It should be understood that the setting of the temperature is only an illustrative example, and those skilled in the art may also set different temperatures according to different requirements, which is not described in detail herein.
And 103, annealing the titanium alloy subjected to thermal deformation.
After the titanium alloy is subjected to thermal deformation, the thermally deformed titanium alloy is subjected to annealing heat treatment.
In order to ensure the stability and the recrystallization degree of the alloy, the annealing temperature in the step c is set to be 700 to 800 ℃ and the annealing time is set to be 10 to 120min in the embodiment. It should be understood that the above-mentioned setting of temperature and time is also only an illustrative example, and those skilled in the art may also set different temperatures according to different requirements, and thus detailed description is omitted here.
After annealing heat treatment, the titanium alloy has wide strain range super elasticity (the super elasticity is about 3% after the deformation amount is 12%), ultrahigh temperature shape memory effect (the shape recovery at 800 ℃ is about 2.7%) and total recoverable strain of about 5.7%. For conventional superelastic and shape memory titanium alloys, the superelasticity achieved by the stress-induced β → α "martensitic transformation is generally in the low strain range (less than 5%) and the shape memory effect temperature is generally below 200 ℃ (as disclosed in chinese patent CN 1648268A).
The titanium alloy provided by the invention utilizes stress induction beta → alpha' martensite transformation to obtain super-elasticity and shape memory effect, and can still obtain 3% of super-elasticity and 2.7% of 800 ℃ super-high temperature shape memory effect after the strain amount is up to 12%, and the strain amount and the use temperature are superior to those of the traditional super-elasticity and shape memory titanium alloy, so that the titanium alloy can be used for manufacturing super-elasticity and shape memory effect elastic functional components under the special environment of large deformation and high temperature.
And 104, pre-deforming the titanium alloy subjected to annealing heat treatment to obtain the multifunctional titanium alloy.
In this embodiment, the titanium alloy after the annealing heat treatment in step 103 is subjected to simple low-strain pre-deformation, so as to obtain a titanium alloy with an ultra-low elastic modulus and high strength.
The multifunctional titanium alloy obtained by pre-deforming the titanium alloy provided by the invention utilizes stress-induced alpha' martensite transformation to obtain ultralow elastic modulus and high strength, solves the problem that the traditional titanium alloy cannot have both elastic functionality and high strength, and realizes excellent high elasticity and high strength in the same alloy. The traditional method for realizing high strength and low elastic modulus of the titanium alloy is to carry out severe plastic deformation to refine crystal grains, wherein the deformation is about 90 percent (as disclosed in Chinese patent CN102581550B and CN 104220612A), the severe plastic deformation is used for refining the crystal grains and separating out a certain amount of alpha phase reinforced beta matrix (as disclosed in Chinese patent CN103060609A, CN109355531A, CN109628796A and CN 110423933A), and the structure state is mainly ultrafine crystal or nanocrystalline beta. In the embodiment, the transformation of the alpha 'martensite is induced by low strain amount pre-deformation, the ultralow elastic modulus and the high strength can be realized by only 5-15% of deformation amount, and the structure state is that the alpha' martensite is added with less than 10% of beta.
In this embodiment, the pre-deformation mode of step d is cold deformation. It is understood that the pre-deformation manner in the present embodiment includes, but is not limited to: pre-stretching deformation, cold rolling deformation, cold heading deformation, cold drawing deformation, cold forging deformation or other cold deformation modes. Other modifications can be made by those skilled in the art as long as the above technical effects are achieved.
In this embodiment, after determining alloy components according to a β stability range of the multifunctional titanium alloy, a titanium alloy is prepared by melting according to the alloy components, then the titanium alloy is thermally deformed in an α + β two-phase region, then the thermally deformed titanium alloy is subjected to annealing heat treatment, and finally the titanium alloy after the annealing heat treatment is subjected to pre-deformation, so as to obtain the multifunctional titanium alloy. According to the method, firstly, titanium alloy is smelted according to specific alloy components, then the titanium alloy is subjected to thermal deformation and annealing heat treatment, the titanium alloy has wide strain range superelasticity and ultrahigh temperature shape memory effect, then the titanium alloy is subjected to pre-deformation treatment, and the multifunctional titanium alloy prepared by the pre-deformation treatment has ultralow elastic modulus and high strength, can realize elastic modulus as low as 29GPa and high strength as high as 1081MPa and high elasticity with elastic strain limit of 3.1%, so that the technical problems that the existing alloy cannot have both functionality and structural property due to mutual repulsion of elastic functionality and high strength, and high elasticity and high strength are difficult to realize in the same alloy are solved.
The above is an embodiment of a method for preparing a multifunctional titanium alloy provided in the embodiments of the present application, and the following is an embodiment of a multifunctional titanium alloy provided in the embodiments of the present application.
The multifunctional titanium alloy in the present embodiment is prepared by the preparation method of the multifunctional titanium alloy in the above embodiment.
Specifically, in order to ensure the stability of the alloy, the valence electron concentration of the multifunctional titanium alloy in the embodiment is
The degree e/a is in the range of 4.08 to 4.15,
The value range is 2.80 to 2.83,
The value range is 2.41 to 2.46.
Specifically, the molybdenum equivalent of the multifunctional titanium alloy is lower than 6.5 to ensure the stability of the alloy.
The multifunctional titanium alloy in the embodiment can realize the elastic functionality of wide strain range superelasticity and ultrahigh temperature shape memory effect, and can realize ultralow elastic modulus as low as 29GPa, high strength as high as 1081MPa and high elasticity with elastic strain limit of 3.1% after pre-deformation treatment, thereby solving the technical problems that the existing alloy cannot realize both functionality and structure due to mutual repulsion of elastic functionality and high strength, and is difficult to realize high elasticity and high strength in the same alloy.
For the convenience of understanding, the preparation method of the multifunctional titanium alloy is described in detail in the examples of the present application by combining the specific components and the implementation method.
First, the multifunctional titanium alloy herein has the following alloy components: Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O (wt%), the electronic parameters of which are: the ratio of e/a is 4.133,
the molybdenum equivalent was 2.41.
The preparation method of the corresponding multifunctional titanium alloy comprises the following steps:
step 1: preparing the annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O titanium alloy.
Step 1.1, preparing titanium sponge, high-purity Nb particles, Zr particles, Fe particles and Ti-80Sn intermediate alloy, performing ultrasonic cleaning, acid washing and other steps on raw materials for 30min to remove surface impurities and pollutants, and performing raw material proportioning according to target alloy components.
Step 1.2, putting the raw materials into a vacuum non-consumable arc furnace for smelting under vacuum and high-purity argon, and repeatedly smelting for 5 times to obtain Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy cast ingots with uniform components;
step 1.3, homogenizing the cast ingot at 1000 ℃ for 2 hours by using a tubular furnace, introducing argon for protection, and cooling by water after heat treatment;
step 1.4, cutting the ingot after the homogenization heat treatment into a plate with the thickness of 10mm by linear cutting, and then carrying out hot rolling treatment in a two-phase region of 750 ℃ and 650 ℃, wherein the reduction of the rolling thickness is 85%;
step 1.5, annealing the rolled plate at 770 ℃ for 30min, and performing water cooling treatment after annealing to obtain an annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy, wherein the titanium alloy structure is shown in figure 2 and consists of a recrystallized equiaxial beta matrix and a small amount of fine equiaxial primary alpha phase, and the diagram of the wide strain range superelasticity SE and the superhigh temperature shape memory effect SME of the titanium alloy is shown in figure 3.
Step 2: and (3) carrying out pre-deformation treatment on the annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O titanium alloy in the step (1) to obtain the high-strength high-elasticity multifunctional titanium alloy.
Mode 1: deformation by pre-stretching
Step 2.1, processing the annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy plate into a standard tensile sample by wire cutting;
and 2.2, performing pre-stretching deformation treatment on the Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy tensile sample, accurately controlling the strain by using an extensometer in the stretching process, wherein the pre-stretching deformation is 5-15%, and immediately unloading after the tensile deformation is achieved.
The Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O multifunctional titanium alloy prepared by pre-stretching deformation mainly comprises alpha' martensite and a small amount of residual beta phase, as shown in figure 4, the volume fraction of the residual beta phase is less than 10%, and the structure is shown in figure 5. By the tensile test, as shown in fig. 6, the alloy subjected to 12.5% pre-stretching deformation treatment has the elastic modulus as low as 29GPa, the tensile strength of 1081MPa, the elastic strain limit of 3.1% and the elongation after fracture of 8%.
Mode 2: cold rolling deformation
And 2.1, carrying out cold rolling deformation on the annealed Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O alloy plate, wherein the reduction amount of the rolling thickness is 10%.
The Ti-17Nb-6Sn-4Zr-0.8Fe-0.2O multifunctional titanium alloy prepared by rolling deformation mainly comprises alpha' martensite and a small amount of residual beta phase, and has the elastic modulus of 49GPa, the tensile strength of 1003MPa and the elastic strain limit of 2 percent through a tensile test.
The embodiment of the application also provides application of the multifunctional titanium alloy in aerospace high-strength high-elasticity parts and biomedical high-strength high-elasticity parts.
The multifunctional titanium alloy in the embodiment can obtain the elastic modulus as low as 29GPa (55 GPa lower than that of rubber metal), the high strength (1081MPa equivalent to that of the rubber metal) and the high elasticity with the elastic strain limit of 3.1 percent (2.5 percent higher than that of the rubber metal), and is particularly suitable for manufacturing elastic connecting pieces such as fasteners, springs and the like and high-temperature shape memory components such as airplane landing gear up-and-down locking springs, flight control springs, nuts, bolts, shock absorbers, high-temperature pipe joints and the like in the fields of aerospace, automobile industry and the like. In addition, the elastic modulus of the titanium alloy is as low as 29GPa, and the titanium alloy is matched with human bones (5-30 GPa), so that the titanium alloy can be used for an implant for the human body to solve the stress shielding effect caused by the high elastic modulus of the existing biomedical titanium alloy, such as orthopedics, dentistry, cavity bone, marrow bone, screws, medical instruments for operation and the like.
The above-mentioned embodiments are only used for illustrating the technical solutions of the present invention, and not for limiting the same; although the present invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some technical features may be equivalently replaced; and such modifications or substitutions do not depart from the spirit and scope of the corresponding technical solutions of the embodiments of the present invention.
Claims (10)
1. A preparation method of a multifunctional titanium alloy at least comprises the following steps:
step a, determining alloy components according to the beta phase stability range of the titanium alloy, so that the obtained alloy can generate stress-induced beta → alpha' martensite phase transformation in subsequent treatment, specifically, the alloy components are as follows: 2-20 wt% of Nb, 3-8 wt% of Zr, 2-6 wt% of Sn, 0.5-3 wt% of Fe, 0.1-0.7 wt% of O and the balance of Ti;
b, thermally deforming and thermally treating the obtained titanium alloy in an alpha + beta two-phase region; characterized in that the preparation method further comprises the following steps:
and c, adopting stress induction to enable the titanium alloy to generate beta → alpha' martensite transformation.
2. The method of claim 1, wherein in step a, the beta phase stability of the titanium alloy is determined by its electronic parameters and molybdenum equivalent, wherein the valence electron concentration e/a is in the range of 4.08-4.15,
The value range is 2.80 to 2.83,
The value ranges from 2.41 to 2.46, and the molybdenum equivalent is less than 6.5.
3. The method for preparing the multifunctional titanium alloy according to claim 1, wherein the treatment in the step b is: the titanium alloy is subjected to thermal deformation in an alpha + beta two-phase region, and then the titanium alloy after thermal deformation is subjected to annealing heat treatment. Preferably, the thermal deformation temperature is 600-800 ℃, the annealing temperature in the step c is 700-800 ℃, and the annealing time is 10-120 min.
4. The method for preparing the multifunctional titanium alloy according to claim 1, wherein in the step c, the titanium alloy is subjected to β → α' martensitic transformation by using stress induction, and specifically: and pre-deforming the titanium alloy subjected to annealing heat treatment, wherein preferably, the deformation amount is 5-15%.
5. The method for preparing the multifunctional titanium alloy according to claim 4, wherein the pre-deformation mode is cold deformation, and preferably, the cold deformation mode comprises the following steps: pre-stretching deformation, cold rolling deformation or other cold deformation modes.
6. The multifunctional titanium alloy produced according to any one of claims 1 to 5, wherein the multifunctional titanium alloy has a stress-induced β → α 'martensitic structure transformation, and the elastic functionality and strength structural properties thereof result from the stress-induced β → α' martensitic transformation.
7. The multifunctional titanium alloy of claim 6, wherein the multifunctional titanium alloy structure is α' martensite and β phase, and the volume fraction of β phase is less than 10%.
8. The multifunctional titanium alloy according to claim 6 or 7, wherein the multifunctional titanium alloy has an elastic modulus of not higher than 49GPa, a tensile strength of not lower than 1003MPa and an elastic strain limit of not lower than 2%.
9. The multifunctional titanium alloy according to claim 8, wherein preferably the multifunctional titanium alloy has an elastic modulus of not higher than 29 GPa; preferably, the tensile strength is not lower than 1081 MPa; elastic strain limit is not less than 3.1%, and the alloy has wide strain range super elasticity (super elasticity is about 3% after deformation amount is 12%), and ultra-high temperature shape memory effect (shape recovery is about 2.7% after 800 ℃).
10. Use of the multifunctional titanium alloy of any one of claims 6 to 9 in aerospace high strength high elasticity parts, high temperature shape memory parts and biomedical high strength high elasticity parts.
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| CN109628796A (en) * | 2019-01-21 | 2019-04-16 | 北京航空航天大学 | A kind of high elastic and strength titanium alloy and its preparation method and application |
| US20190338397A1 (en) * | 2018-05-07 | 2019-11-07 | Ati Properties Llc | High Strength Titanium Alloys |
| US20200071806A1 (en) * | 2018-08-28 | 2020-03-05 | Ati Properties Llc | Creep Resistant Titanium Alloys |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2017210658A (en) * | 2016-05-26 | 2017-11-30 | 国立大学法人東北大学 | HEAT-RESISTANT Ti ALLOY AND HEAT-RESISTANT Ti ALLOY MATERIAL |
| US20190338397A1 (en) * | 2018-05-07 | 2019-11-07 | Ati Properties Llc | High Strength Titanium Alloys |
| US20200071806A1 (en) * | 2018-08-28 | 2020-03-05 | Ati Properties Llc | Creep Resistant Titanium Alloys |
| CN109628796A (en) * | 2019-01-21 | 2019-04-16 | 北京航空航天大学 | A kind of high elastic and strength titanium alloy and its preparation method and application |
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| YU FU: ""Ultrahigh strain hardening in a transformation-induced plasticity and twinning-induced plasticity titanium alloy"", 《SCRIPTA MATERIALIA》 * |
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