CN116240412B - Method for improving strength of titanium alloy and reducing elastic modulus - Google Patents
Method for improving strength of titanium alloy and reducing elastic modulus Download PDFInfo
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- CN116240412B CN116240412B CN202310115428.XA CN202310115428A CN116240412B CN 116240412 B CN116240412 B CN 116240412B CN 202310115428 A CN202310115428 A CN 202310115428A CN 116240412 B CN116240412 B CN 116240412B
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- 238000000034 method Methods 0.000 title claims abstract description 31
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 26
- 239000000956 alloy Substances 0.000 claims abstract description 96
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 94
- 239000010949 copper Substances 0.000 claims abstract description 53
- 238000010438 heat treatment Methods 0.000 claims abstract description 29
- 229910052751 metal Inorganic materials 0.000 claims abstract description 12
- 239000002184 metal Substances 0.000 claims abstract description 12
- 239000010955 niobium Substances 0.000 claims abstract description 9
- 239000002245 particle Substances 0.000 claims abstract description 8
- 229910004353 Ti-Cu Inorganic materials 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims abstract description 4
- 238000002156 mixing Methods 0.000 claims abstract description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 32
- 230000008569 process Effects 0.000 claims description 17
- 230000003647 oxidation Effects 0.000 claims description 12
- 238000007254 oxidation reaction Methods 0.000 claims description 12
- 238000004321 preservation Methods 0.000 claims description 10
- 230000001276 controlling effect Effects 0.000 claims description 2
- 230000001105 regulatory effect Effects 0.000 claims description 2
- 229910001040 Beta-titanium Inorganic materials 0.000 abstract description 8
- 210000000988 bone and bone Anatomy 0.000 abstract description 7
- 239000000463 material Substances 0.000 abstract description 7
- 238000012545 processing Methods 0.000 abstract description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 29
- 229910052802 copper Inorganic materials 0.000 description 29
- 239000010936 titanium Substances 0.000 description 14
- 239000007943 implant Substances 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 239000006104 solid solution Substances 0.000 description 7
- 230000000844 anti-bacterial effect Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 230000035882 stress Effects 0.000 description 5
- 238000003723 Smelting Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000002513 implantation Methods 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910017985 Cu—Zr Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000000172 allergic effect Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 208000010668 atopic eczema Diseases 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 239000003519 biomedical and dental material Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000003139 buffering effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000012669 compression test Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 208000015181 infectious disease Diseases 0.000 description 1
- 230000002757 inflammatory effect Effects 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 239000012567 medical material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 231100000252 nontoxic Toxicity 0.000 description 1
- 230000003000 nontoxic effect Effects 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000004445 quantitative analysis Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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 discloses a method for improving the strength of a titanium alloy and reducing the elastic modulus, and belongs to the field of heat treatment processing of titanium alloy materials. The method of the invention comprises the following steps: preparing intermediate alloy Ti-Cu alloy in advance; then mixing niobium particles, zirconium particles with a master alloy, wherein the metal Nb is added in 35 wt.%; metal Zr is added in 7 wt.%; metal Cu is added in 10 wt.%; ti is the balance; the addition error of the alloy is less than 1wt.%, the alloy is smelted in a vacuum non-consumable arc furnace and turned over for 4 to 5 times; the obtained finished titanium alloy ingot; putting the obtained finished titanium alloy ingot into a vacuum tube furnace, and heating at the temperature of T β Heating at 10-20deg.C/min for 90-120min; the beta titanium alloy obtained by the invention has good compressive strength and yield strength, is close to the elastic modulus of human bones, and has wide application prospect as a medical replacement material.
Description
Technical Field
The invention relates to a method for improving the strength of a titanium alloy and reducing the elastic modulus, belonging to the field of heat treatment processing of titanium alloy materials.
Background
In the medical field, it is necessary to replace a damaged portion of a joint damaged or broken by an external force. Among the medical materials, titanium alloy is an indispensable first-choice biomedical material because of low density, light weight, no magnetism, excellent mechanical property, biocompatibility, good corrosion resistance, low elastic modulus and other advantages. At present, the beta titanium alloy Ti-35Nb-7Zr which is successfully developed internationally and is nontoxic and free of allergic alloy elements has lower elastic modulus (48-55 Gpa), and is beneficial to stress buffering and uniform transmission between the implant and the bone. The occurrence of stress shielding is reduced, and the method has very important significance for improving the success rate of the implant. However, the alloy itself has a small amount of alpha phase, and the elastic modulus is still higher than that of human bones (0 to 30 Gpa). Meanwhile, the Ti-35Nb-7Zr alloy itself does not have antibacterial property, and a series of inflammatory infections are induced after implantation into a human body.
For the alloy, the cooling speed of the alloy is too high in vacuum non-consumable smelting, so that unbalanced solidification is aggravated, and the microstructure is uneven; the alloy is remelted repeatedly, so that the residual stress in the alloy is high, and the comprehensive performance of the alloy is influenced. Aging treatment can lead to the generation of a secondary alpha phase, so that the elastic modulus of the alloy is improved; therefore, the research and development of the heat treatment method for regulating and controlling the precipitation phase of the medical titanium alloy solves the problem that the titanium alloy cannot be matched with human bones due to no antibacterial property and high elastic modulus of the alloy, and has great significance for further explaining the performance mechanism of the titanium alloy.
The Chinese patent application with the application number of CN202210390223.8 discloses a high-entropy antibacterial medical titanium alloy which has high strength and elongation, however, the method is complex in process and high in energy consumption, the elastic modulus of the prepared titanium alloy is kept above 54GPa, the requirement of low modulus cannot be well met, and the action mechanism of the complex alloy is not clear.
Disclosure of Invention
The invention aims to provide a method for improving the strength of a titanium alloy and reducing the elastic modulus, so that the alloy can be replaced by the elastic modulus close to that of human bones, the precipitation of copper-containing phases can be clearly controlled, and the antibacterial property is improved; the method specifically comprises the following steps:
(1) Preparing intermediate alloy Ti-Cu alloy in advance; then mixing niobium particles, zirconium particles with a master alloy, wherein the metal Nb is added in 35 wt.%; metal Zr is added in 7 wt.%; metal Cu is added in 10 wt.%; ti is the balance; the addition error of the alloy is less than 1wt.%, the alloy is smelted in a vacuum non-consumable arc furnace and turned over for 4 to 5 times; the obtained finished titanium alloy ingot has uniform components and no obvious segregation.
(2) Putting the obtained finished titanium alloy ingot into a vacuum tube furnace, and heating at the temperature of T β Heating at 10-20deg.C/min for 90-120min; then cooling to room temperature, wherein the cooling process needs to isolate air and preventOxidation stopping; according to DSC test, the phase transition point T of the alloy β ≈789.4℃。
The cooling process in the step (2) of the invention can be air cooling and furnace cooling, preferably water quenching cooling, and is cooled to room temperature at the speed of 90-100 ℃/s, and the faster the speed, the more obvious the regulation effect of the precipitated phase is, and the cooling process needs to isolate air to prevent oxidation.
Preferably, the heat-insulating temperature in step (2) of the present invention is 1000 ℃, and the obtained alloy contains copper phase in Cu x Zr y The phase is mainly, and spherical crystals containing copper phase are uniformly distributed in the alloy.
Preferably, the heat-insulating temperature in the step (2) is 900-1000 ℃, and the obtained alloy contains copper phase in Cu x Zr y The phases are dominant, but spherical crystals with uniformly distributed copper-containing phases have not been formed in the alloy.
Preferably, the heat-insulating temperature in the step (2) is 800-900 ℃, and the obtained alloy contains copper phase and Ti x Cu y The phase is dominant.
The invention can make titanium alloy have higher beta-Ti content and regulate and control the precipitation type of copper-containing phase, and the difference of precipitation phases makes the obtained alloy have distinct mechanical properties.
The beneficial effects of the invention are as follows:
(1) The preparation process is carried out under vacuum or high-purity argon protective atmosphere, thereby preventing the oxidation of raw materials and ensuring that the components of the added raw materials are not changed.
(2) The heat treatment method ensures that the alloy is pure beta titanium alloy, has uniform alloy structure, and avoids the serious segregation in the traditional vacuum arc melting.
(3) The heat treatment process of the beta titanium alloy can effectively control the precipitation of the copper-containing phase of the alloy, the heat preservation temperature is 900-1000 ℃, and the copper-containing phase of the alloy mainly uses Cu x Zr y The phase is mainly, the heat preservation temperature is 800-900 ℃, the copper-containing phase of the alloy is Ti x Cu y The phases are dominant and the alloy exhibits superelasticity.
(4) The beta titanium alloy has higher strength, compressive strength (1300-1800 MPa) and lower elastic modulus (21-45 GPa) which is close to that of human bone, and can effectively reduce the stress shielding effect.
(5) The addition of copper to the titanium alloy can improve the antibacterial property, but at the same time the elastic modulus can be increased.
The invention solves the problem of high elastic modulus of the prior medical titanium and alloy thereof in the clinical application process, and has wide application panorama.
Drawings
FIG. 1 is a phase analysis XRD pattern for a novel beta titanium alloy of the present invention at different processing temperatures;
FIG. 2 is an SEM image of the novel beta titanium alloy of the present invention at various processing temperatures;
FIG. 3 is a graph showing the true stress strain of compression tests of the novel beta titanium alloy of the present invention at different processing temperatures.
Detailed Description
The invention will be described in further detail with reference to the drawings and the specific embodiments, but the scope of the invention is not limited to the description.
Example 1
A method for improving the strength of titanium alloy and simultaneously reducing the elastic modulus specifically comprises the following steps:
(1) Alloy smelting: preparing intermediate alloy Ti-Cu in advance; then mixing niobium particles, zirconium particles with a master alloy, wherein the metal Nb is added in 35 wt.%; metal Zr is added in 7 wt.%; metal Cu is added in 10 wt.%; ti is the balance; the addition error of the alloy is less than 1wt.% so as to meet the component requirement of the alloy; smelting the electrode in a vacuum non-consumable arc furnace, and turning over for 4-5 times; the obtained finished titanium alloy ingot has uniform components and no obvious segregation.
(2) Determination of the transformation Point T of the alloy β : according to DSC test, the phase transition point T of the alloy β The temperature is about 789.4 ℃, the design temperature of heat treatment is ensured to be above the transition point, the temperature interval of eutectoid reaction of components is selected according to the Ti-Cu and Cu-Zr phase diagram, and the heat treatment temperature route of the alloy is designed as follows: raising the temperature to the heat preservation temperature at a heating rate of 20 ℃/min, carrying out single solid solution treatment, and preserving heatThe temperature is 1000 ℃, the heat preservation time is 120min, the cooling speed is 100 ℃/s, the cooling is carried out to the room temperature, and the cooling process needs to isolate air to prevent oxidation.
(3) And (3) placing the obtained finished titanium alloy ingot into a vacuum tube furnace, selecting according to the heat treatment temperature route in the step (1), heating to the target temperature, preserving heat, quenching and cooling to room temperature, wherein the cooling process needs to isolate air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the alloy is mainly composed of beta-Ti (97.4 wt.%) and copper-containing phase, wherein the copper-containing phase is mainly composed of Cu x Zr y (2.6 wt.%) the copper-containing phase is spherical crystals, uniformly dispersed in the alloy matrix, and the mechanical properties of the alloy are tested to obtain: the elastic modulus is 28GPa, the yield strength is 1098MPa, the strength of the material is higher, the elastic modulus is lower, and the requirement of mechanical compatibility of the implant is met.
Example 2
Example 2 differs from example 1 in that the heat treatment route in example 2 is: raising the temperature to the heat preservation temperature at the heating rate of 20 ℃/min, only performing single solid solution treatment, wherein the heat preservation temperature is 950 ℃, the heat preservation time is 120min, the cooling rate is 100 ℃/s, cooling is performed to the room temperature, and the cooling process needs to isolate air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the copper-containing phase of the alloy is mainly Cu x Zr y (1.5 wt.%) copper-containing phases are distributed at the alloy grain boundaries, and the mechanical properties of the alloy were tested: the elastic modulus is 45GPa, the yield strength is 1555MPa, the strength of the material is higher, the elastic modulus is lower, and the requirement of mechanical compatibility of the implant is met.
Example 3
Example 3 differs from example 1 in that the heat treatment route in example 3 is: raising the temperature to the heat preservation temperature at the heating rate of 20 ℃/min, only carrying out single solid solution treatment, keeping the temperature at 900 ℃, keeping the temperature for 120min, cooling to the room temperature at the cooling rate of 100 ℃/s, and isolating air to prevent oxidation in the cooling process.
Ti-35Nb-7Zr-1 prepared in the example0Cu alloy, according to XRD result quantitative analysis, copper phase of alloy is mainly Ti x Cu y (5.6 wt.%) copper-containing phases are distributed at the alloy grain boundaries, and the mechanical properties of the alloy were tested: the elastic modulus is 21GPa, the yield strength is 687MPa, the strength of the material is higher, the elastic modulus is lower, and the requirement of mechanical compatibility of the implant is met.
Example 4
Example 4 differs from example 1 in that the heat treatment route in example 4 is: raising the temperature to the heat preservation temperature at the heating rate of 20 ℃/min, only carrying out single solid solution treatment, keeping the temperature at 850 ℃ for 90min, cooling to the room temperature at the cooling rate of 100 ℃/s, and isolating air to prevent oxidation in the cooling process.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the copper-containing phase of the alloy is mainly Ti x Cu y (3.8 wt.%) copper-containing phases were distributed at the alloy grain boundaries and the mechanical properties of the alloy were tested: the elastic modulus is 37GPa, the yield strength is 815MPa, and the alloy has super elasticity.
Example 5
Example 5 differs from example 1 in that the heat treatment route in example 5 is to raise the temperature to the holding temperature at a heating rate of 20 ℃/min, only a single solid solution treatment is performed, the holding temperature is 800 ℃, the holding time is 90min, the cooling rate is 100 ℃/s, and the cooling process needs to isolate air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the copper-containing phase of the alloy is mainly Ti x Cu y (3.6 wt.%) copper-containing phases are distributed at the alloy grain boundaries, and the mechanical properties of the alloy were tested: the elastic modulus is 31GPa, the yield strength is 765MPa, and the alloy has super elasticity.
Example 6
Example 6 differs from example 1 in that the heat treatment route in example 6 is to raise the temperature to the holding temperature at a heating rate of 10 ℃/min, only a single solid solution treatment is performed, the holding temperature is 1000 ℃, the holding time is 90min, the cooling rate is 0.5 ℃/s, and the cooling process needs to isolate air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the copper-containing phase of the alloy is mainly Ti x Cu y (6.4 wt.%) and a small portion of Cu x Zr y (2.7 wt%) phase, the copper-containing phase is spherical crystal, uniformly dispersed in alloy matrix, and the mechanical property of alloy is tested to obtain: the elastic modulus is 35GPa, the yield strength is 1354MPa, the strength of the material is higher, the elastic modulus is lower, and the requirement of mechanical compatibility of the implant is met.
Example 7
Example 7 differs from example 1 in that the heat treatment route in example 7 is to raise the temperature to the holding temperature at a heating rate of 10 ℃/min, only a single solid solution treatment is performed, the holding temperature is 1000 ℃, the holding time is 90min, the cooling rate is 0.05 ℃/s, and the cooling process needs to isolate air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the copper-containing phase of the alloy is mainly Ti x Cu y (7 wt.%); also a small part of Cu x Zr y (4.8 wt.%) phase, the copper-containing phase is spherical crystal, uniformly dispersed in alloy matrix, and the mechanical property of alloy is tested to obtain: the elastic modulus is 31GPa, the yield strength is 682MPa, the strength of the material is higher, the elastic modulus is lower, and the requirement of mechanical compatibility of the implant is met.
Comparative examples
The comparative example differs from example 1 in that in example 8, only smelting is performed and no subsequent heat treatment process is performed, the temperature is up to 1000 ℃, direct cooling to room temperature is not performed, and the cooling process needs to be isolated from air to prevent oxidation.
The Ti-35Nb-7Zr-10Cu alloy prepared in the embodiment is quantitatively analyzed according to XRD results, and the alloy Ti x Cu y 、Cu x Zr y alpha-Ti with more phases existing and distributed basically, copper-containing phases are dispersed at grain boundaries, and the mechanical properties of the alloy are tested to obtain: the elastic modulus is 74GPa, the yield strength is 1469MPa, the strength of the material is higher, but the elastic modulus is also higher, and the mechanical compatibility requirement of the implant cannot be met.
In summary, the examples all have significant performance improvement and can be used clinically, while the comparative example has too high an elastic modulus compared to human bone, which leads to an elastic modulus mismatch after implantation, while the results of example 1 cool most rapidly, retain more beta phase, while spherical Cu x Zr y The phase formation has a dispersion strengthening effect and has the best performance effect in the examples.
Regarding the change of the alloy precipitated phase, it can be seen from fig. 2 that the copper-containing phase is mainly distributed at the grain boundary because Cu is only limitedly solid-dissolved in β -Ti, while Nb, zr is infinitely solid-dissolved in β -Ti, the difference in solubility causes Cu to be repelled at the edge of the crystal, and the obtained energy of crystallization nucleation of the Cu phase with the rise of temperature causes the copper phase to be continuously aggregated at the grain boundary, while the alloy eventually forms spherical crystals uniformly distributed in the alloy matrix under the action of surface tension or the like, forming a strengthening effect.
Claims (1)
1. A method for improving the strength of a titanium alloy while reducing the elastic modulus, comprising the steps of: the method is realized by regulating and controlling the titanium alloy precipitated phase, and specifically comprises the following steps:
(1) Preparing intermediate alloy Ti-Cu alloy in advance; then mixing niobium particles, zirconium particles with a master alloy, wherein the metal Nb is added in an amount of 35 wt%; metal Zr is added in 7 wt%; metal Cu is added at 10 wt%; ti is the balance; the addition error of the alloy is less than 1wt percent, and the alloy is smelted in a vacuum non-consumable arc furnace and turned over for 4 to 5 times; the obtained finished titanium alloy ingot;
(2) Putting the obtained finished titanium alloy ingot into a vacuum tube furnace, and performing heat treatment at the temperature ofHeating at 10-20deg.C/min for 90-120min, and cooling to room temperature;
after heat preservation, the alloy is cooled to room temperature at the speed of 90-100 ℃/s, and the cooling process needs to isolate air to prevent oxidation.
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| CN105420549A (en) * | 2015-12-10 | 2016-03-23 | 东南大学 | Low-elasticity-modulus high-fatigue-strength biologic implantable titanium alloy and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7722805B2 (en) * | 2003-12-25 | 2010-05-25 | Institute Of Metal Research Chinese Academy Of Sciences | Titanium alloy with extra-low modulus and superelasticity and its producing method and processing thereof |
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| CN105420549A (en) * | 2015-12-10 | 2016-03-23 | 东南大学 | Low-elasticity-modulus high-fatigue-strength biologic implantable titanium alloy and preparation method thereof |
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| Title |
|---|
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