CN109055815B - Method for rapidly screening low-elasticity-modulus biological titanium alloy - Google Patents
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Abstract
The invention belongs to the field of material research methods, and particularly relates to a method for rapidly screening low-elasticity-modulus biological titanium alloy. The method comprises the steps of firstly determining two terminal component components in the BCC-phase titanium alloy according to a phase diagram calculation result, then taking pure metal as a raw material according to the components, sequentially carrying out smelting, linear cutting and annealing to obtain two terminal component components, then fixing the two terminal component components together for annealing treatment to obtain a diffusion couple, and finally carrying out component gradient analysis and elastic modulus test on the BCC-phase in the diffusion couple to obtain a corresponding relation between the titanium alloy components and the elastic modulus, thereby determining the composition of the low-elastic-modulus biological titanium alloy. The screening method is easy to realize, efficient and rapid, and can greatly save research and development, manpower and time cost compared with the traditional research method. A large amount of approximately continuous experimental data information of phase composition-alloy composition-elastic modulus is obtained in a short time, which is helpful for comprehensive and systematic understanding of the BCC phase titanium alloy system.
Description
Technical Field
The invention belongs to the field of material research methods, and particularly relates to a method for rapidly screening low-elasticity-modulus biological titanium alloy.
Background
The biological titanium alloy is a very important industrial material, and is widely applied to clinical medical treatment as a human hard tissue implant material due to the low elastic modulus and good biocompatibility. In consideration of non-toxicity to human body, the main additive elements in the biological titanium alloy include Cr, Fe, Hf, Mn, Mo, Nb, Sn, Ta, W, Zr and the like, and the titanium alloy containing the above additive elements forms BCC phase titanium alloy after solution treatment. At present, Ti-Nb base, Ti-Zr base, Ti-Nb-Ta-Zr base and Ti-Nb-Zr-Sn base alloys are main alloy systems for developing low-elastic modulus biological titanium alloys, and Ti-Cr base, Ti-Fe base and Ti-Mn base alloys are related alloy systems of low-cost biological titanium alloys. Compared with the traditional pure Ti and Ti-Al-V alloys, the BCC-phase titanium alloys have better biocompatibility and lower elastic modulus and have the potential of replacing the traditional clinical biological metal materials greatly.
In different BCC-phase titanium alloy systems, the determination of the alloy component corresponding to the lowest elastic modulus is very important research work. The traditional alloy development mainly comprises the steps of carrying out material performance test on single-component samples one by one, and then carrying out comparative analysis, thereby selecting the alloy with the optimal performance in the tested samples. On one hand, the method needs to consume a large amount of manpower and material resources to carry out large-batch experiments, and is difficult to ensure the rigor of experimental conclusions, and on the other hand, due to the limitation of experimental points, researchers lack comprehensive and systematic understanding of a BCC-phase titanium alloy system, so that related basic theory research and product research and development are trapped in bottlenecks. Therefore, experimental data such as alloy components, elastic modulus and the like of the BCC-phase titanium alloy are efficiently and quickly acquired, so that the biological titanium alloy with low elastic modulus is quickly screened out, and the method has important and profound significance for research and development of novel high-performance biological titanium alloy and understanding of related mechanisms.
Disclosure of Invention
In order to overcome the defects and shortcomings of the prior art, the invention aims to provide a method for rapidly screening low-elasticity-modulus biological titanium alloy. The method is a method capable of efficiently researching the phase composition, the alloy composition and the elastic modulus of a multi-component titanium alloy system, and gradient change combination areas of alloy interfaces with different components can be obtained on a single sample, so that elastic modulus data of a plurality of multi-component titanium alloy systems can be obtained, and the titanium alloy composition with the lowest elastic modulus can be finally obtained.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
a method for rapidly screening low-elasticity-modulus biological titanium alloy comprises the following steps:
(1) determining two terminal component components of a diffusion couple to be researched by adopting a phase diagram calculation method;
(2) according to the two terminal component components determined in the step (1), smelting by taking pure metal as a raw material to obtain two terminal component metal ingots, then carrying out linear cutting on the obtained metal ingots to obtain uniform blocks of a metal ingot core part, cleaning the surfaces of the blocks, sealing the blocks into a vacuum container with sponge titanium or sponge yttrium, carrying out annealing treatment, taking out the blocks for quenching after annealing, and carrying out grinding and polishing on the blocks to obtain two terminal components of a diffusion couple;
(3) fixing the two terminal elements obtained in the step (2) together, sealing the two terminal elements into a vacuum container in which titanium sponge or yttrium sponge is stored, annealing, and taking out the blocks fixed together after annealing for quenching to obtain a diffusion couple;
(4) and (4) analyzing the microstructure of the diffusion couple obtained in the step (3) to determine a region where the BCC phase is located, performing component gradient analysis and elastic modulus test on the region to obtain batch experimental data of the BCC phase alloy component-elastic modulus of the titanium alloy, and finally determining the corresponding titanium alloy component according to the lowest value of the elastic modulus.
The phase diagram calculation described in step (1) is preferably performed using commercial calculation software THERMO-CALC or Pandat.
The method for determining the components of the two terminal elements of the diffusion couple to be researched in the step (1) comprises the following steps: for a binary system, preferably calculating a composition-temperature phase diagram; for the ternary system, isothermal cross-sectional diagrams of different temperatures are preferably calculated; for a multi-element system, preferably calculating a phase relation diagram of alloys with different components; and then determining a region where a BCC phase with titanium mass percent higher than 50% is located in a composition-temperature phase diagram or an isothermal cross-section diagram or a phase relation diagram of alloys with different compositions, and taking component values corresponding to two titanium alloys with the largest composition difference in the region, namely two endpoint values when the composition gradient of the titanium alloy is the largest, namely two endpoint components of the diffusion couple to be researched.
The terminal component in the step (1) can be a pure metal component or an alloy component.
The smelting in the step (2) preferably adopts an electric arc smelting method, in the smelting process, volatile metals are placed below, high-melting-point metals are crushed and placed above, and the metal ingots are turned over for multiple times to ensure that the components of the metal ingots are uniform, and the smelting temperature is higher than the liquid phase temperature corresponding to the components obtained after phase diagram calculation.
The volatile metal is Mn or Cr, etc.; a high melting point metal such as Ta or W.
The step (2) of obtaining the uniform block of the metal ingot core part and annealing the block are to obtain a block sample with uniform components and larger grain size; the uniform block of the metal ingot core part is obtained by adopting a linear cutting mode, so that the flatness of the surface of the block is improved, and samples at two ends are tightly combined in the preparation process of the diffusion couple; the titanium sponge or yttrium sponge is placed in the quartz tube to prevent the bulk from being oxidized during annealing.
The size of the uniform block in the step (2) is preferably 0.5-10 mm in thickness, 1-50 mm in length and 1-50 mm in width.
The vacuum degree in the container in the step (2) is preferably less than 10Pa, and the annealing temperature is preferably 900-1200 ℃; the time is preferably 2 to 10 days.
The block is preferably subjected to sand paper grinding, mechanical polishing, deionized water or ethanol ultrasonic cleaning and low-temperature drying in sequence in the grinding and polishing mode in the step (2), and finally the surface of the sample is clean, bright, free of obvious scratches and free of an oxide film.
The method for fixing the two terminal components together in the step (3) preferably adopts a high-purity molybdenum clamp for fixing, so that the two terminal components can be tightly attached together and are not obviously deformed.
The vacuum degree in the container in the step (3) is preferably less than 10Pa, and the annealing temperature is preferably 900-1200 ℃; the time is preferably 6 to 48 hours.
The quenching method described in step (2) and step (3) is preferably carried out in an ice-water mixture.
The microstructure analysis in the step (4) is preferably performed by using an electron probe, a scanning electron microscope or a three-dimensional atom probe.
The method for analyzing the component gradient in the step (4) preferably adopts a spectrometer to perform fixed-point analysis or an energy spectrometer to perform surface scanning.
The method for elastic modulus test described in step (4) is preferably nanoindentation.
The microstructure analysis, the component gradient analysis and the elastic modulus test in the step (4) can be completed on a single-phase diffusion couple, and before each analysis or test, the diffusion couple is firstly subjected to surface treatment such as grinding and polishing, deionized water ultrasonic cleaning and the like, and then is subjected to analysis or test.
Compared with the prior art, the invention has the following advantages and beneficial effects:
1. the screening method of the low-elasticity-modulus biological titanium alloy is easy to implement, efficient and rapid, and can greatly save research and development, labor and time cost compared with the traditional research method.
2. The screening method of the low-elasticity-modulus biological titanium alloy can obtain a large amount of approximately continuous experimental data information of phase composition-alloy composition-elasticity modulus in a short time, and is favorable for comprehensively and systematically recognizing a BCC-phase titanium alloy system.
Drawings
FIG. 1 is an isothermal cross-sectional view at 900 ℃ of the Ti-Nb-Zr system obtained in example 1.
FIG. 2 is a schematic diagram of a high purity molybdenum clip used in examples 1 to 3 of the present invention.
FIG. 3 is a schematic flow chart of the process for preparing a diffusion couple in step (3) of the present invention.
FIG. 4 is a graph showing the variation of the elastic modulus with the composition of the Ti-Nb-Zr diffusion couple obtained in example 1.
FIG. 5 is an isothermal cross-sectional view at 1000 ℃ of the Ti-Nb-Cr system obtained in example 2.
FIG. 6 is a secondary electron image of the microstructure of the Ti-Nb-Cr diffusion couple obtained in example 2.
FIG. 7 is a graph showing the variation of the elastic modulus with the composition of the Ti-Nb-Cr diffusion couple obtained in example 2.
FIG. 8 is a graph showing the variation of the elastic modulus with the composition of the Ti-Nb-Zr-Cr diffusion couple obtained in example 3.
Detailed Description
The present invention will be described in further detail with reference to examples and drawings, but the present invention is not limited thereto. For process parameters not specifically noted, reference may be made to conventional techniques.
Example 1
This example provides a method for rapidly screening low modulus of elasticity Ti-Nb-Zr alloys.
(1) Phase diagram calculations were performed on the Ti-Nb-Zr system alloy, and the resulting isothermal cross-sectional diagram at 900 ℃ was shown in fig. 1, and it was determined that the two terminal constituent components were pure Ti and Ti-17.70 at.% Nb-29.50 at.% Zr alloy, respectively.
(2) Pure Ti metal ingots and Ti-17.70 at.% Nb-29.50 at.% Zr alloy metal ingots are smelted in an electric arc smelting furnace by using high-purity Ti, high-purity Nb and high-purity Zr as raw materials. And during smelting, the arc temperature exceeds 3400 ℃, and the metal ingot is turned for five times, wherein the turning interval time is 1 minute. After melting, the ingot obtained was wire-cut to a core size of 8X 1mm3The block of (1). The surface of the block is subjected to coarse grinding, fine grinding, deionized water ultrasonic cleaning and low-temperature drying in sequence, then the block is placed into a vacuum seal quartz tube with titanium sponge (the vacuum degree is lower than 10Pa), homogenization annealing is carried out in an annealing furnace at 900 ℃, the block is taken out from the furnace after 10 days and is rapidly placed into ice water, and the quartz tube is broken to rapidly cool the block. And then the surfaces of the annealed pure Ti block and the annealed Ti-Nb-Zr alloy block are subjected to coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and low-temperature drying in sequence to obtain two terminal components of the diffusion couple.
(3) Fixing the two terminal components obtained in the step (2) by using a special high-purity molybdenum clamp shown in figure 2 according to the mode shown in figure 3, putting the two terminal components into a vacuum sealed quartz tube filled with titanium sponge, carrying out high-temperature annealing at 900 ℃ in an annealing furnace, taking out the quartz tube from the annealing furnace after 48 hours, putting the quartz tube into ice water, and quickly breaking the quartz tube to reduce the temperature of the obtained diffusion couple within 1 minute. The molybdenum clamps were disassembled to obtain a composition gradient diffusion couple of pure Ti/Ti-17.70 at.% Nb-29.50 at.% Zr alloy.
(4) And (3) performing coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and drying treatment on the diffusion couple obtained in the step (3), performing microstructure analysis by using an electronic probe, determining the region where the BCC phase is located, performing component gradient distribution quantitative analysis by using a spectrum, determining the elastic modulus distribution by using a nano indenter, and further establishing an experimental database corresponding to the components and the elastic modulus, wherein the curve of the elastic modulus changing along with the components of the diffusion couple is shown in FIG. 4. By comparing the changes of the elastic modulus at different components, BCC phase Ti with the lowest elastic modulus, namely 10.98 at.% Nb and 11.00 at.% Zr alloy (the elastic modulus is 43.60GPa) is quickly screened out.
Example 2
This example provides a method for rapidly screening low modulus of elasticity Ti-Nb-Cr alloys.
(1) Phase diagram calculation is performed on the Ti-Nb-Cr system alloy, an isothermal cross-sectional diagram at 1000 ℃ is shown in FIG. 5, and two terminal component compositions are determined to be Ti-17.35 at.% Nb alloy and Ti-9.20 at.% Cr alloy respectively.
(2) High-purity Ti, high-purity Nb and high-purity Cr are used as raw materials, and a Ti-17.35 at.% Nb alloy metal ingot and a Ti-9.20 at.% Cr alloy metal ingot are smelted in an electric arc smelting furnace. And during smelting, the arc temperature exceeds 3400 ℃, and the metal ingot is turned over five times, wherein the time interval between each turning is 1 minute. After melting, the ingot obtained was wire cut to a core size of 8X 2mm3The block of (1). The surface of the block is subjected to coarse grinding, fine grinding, deionized water ultrasonic cleaning and low-temperature drying in sequence, then the block is placed into a vacuum seal quartz tube (the vacuum degree is lower than 10Pa) with titanium sponge, homogenization annealing is carried out in an annealing furnace at 1000 ℃, the block is taken out from the furnace after 7 days and is rapidly placed into ice water, and the quartz tube is broken to rapidly cool the block. And then the surfaces of the annealed Ti-Nb and Ti-Cr alloy blocks are subjected to coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and low-temperature drying in sequence to obtain two terminal components of the diffusion couple.
(3) Fixing the two terminal components obtained in step (2) by using a special high-purity molybdenum clamp shown in figure 2 according to the mode shown in figure 3, putting the two terminal components into a vacuum sealed quartz tube filled with titanium sponge, carrying out high-temperature annealing at 1000 ℃, taking out the quartz tube from an annealing furnace after 25 hours, putting the quartz tube into ice water, and quickly breaking the quartz tube to reduce the temperature of the obtained diffusion couple within 1 minute. The molybdenum clamps were disassembled to obtain a compositional gradient of Ti-17.35 at.% Nb/Ti-9.20 at.% Cr diffusion couple.
(4) And (3) carrying out coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and drying treatment on the diffusion couple obtained in the step (3), carrying out microstructure analysis by using an electronic probe, determining the region where the BCC phase is located, and obtaining a secondary electronic image of the microstructure as shown in FIG. 6. Quantitative analysis of component gradient distribution is carried out by using a spectrum, elastic modulus distribution is measured by using a nanoindenter, and an experimental database corresponding to the components and the elastic modulus is further established, wherein a curve of the change of the elastic modulus along with the diffusion couple components is shown in FIG. 7. By comparing the changes of the elastic modulus at different components, BCC phase Ti with the lowest elastic modulus, 4.7 at.% Nb and 6.5 at.% Cr alloy (the elastic modulus is 41.02GPa) is quickly screened out.
Example 3
This example provides a method for rapidly screening low modulus of elasticity Ti-Nb-Zr-Cr alloys.
(1) Phase diagram calculations were performed on the Ti-Nb-Zr-Cr system alloy to determine the two terminal component compositions as pure Ti and Ti-26.70 at.% Nb-10.50 at.% Zr-2.7 at.% Cr alloy, respectively.
(2) Pure Ti metal ingots and Ti-26.70 at.% Nb-10.50 at.% Zr-2.7 at.% Cr alloy metal ingots are smelted in an electric arc smelting furnace by using high-purity Ti, high-purity Nb, high-purity Zr and high-purity Cr as raw materials. During smelting, the arc temperature exceeds 3400 ℃, and the metal ingot is overturned five times, wherein the smelting time is 1 minute each time. After melting, the ingot obtained was wire cut to a core size of 8X 2mm3The block of (1). The surface of the block is subjected to coarse grinding, fine grinding, deionized water ultrasonic cleaning and low-temperature drying in sequence, then the block is placed into a vacuum seal quartz tube with titanium sponge (the vacuum degree is lower than 10Pa), homogenization annealing is carried out in an annealing furnace at 1200 ℃, the block is taken out from the furnace after 2 days and is rapidly placed into ice water, and the quartz tube is broken to rapidly cool the block. And then the surfaces of the annealed pure Ti block and the annealed Ti-Nb-Zr-Cr alloy block are subjected to coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and low-temperature drying in sequence to obtain two terminal components of the diffusion couple.
(3) Fixing the two terminal components obtained in step (2) by using a special high-purity molybdenum clamp shown in fig. 2 according to the mode shown in fig. 3, putting the two terminal components into a vacuum sealed quartz tube filled with titanium sponge, carrying out high-temperature annealing at 1200 ℃, taking out the quartz tube from an annealing furnace after 6 hours, putting the quartz tube into ice water, and quickly breaking the quartz tube to reduce the temperature of the obtained diffusion couple within 1 minute. The molybdenum clamps were disassembled to obtain a composition gradient diffusion couple of pure Ti/Ti-26.70 at.% Nb-10.50 at.% Zr-2.7 at.% Cr alloy.
(4) And (3) performing coarse grinding, fine grinding, polishing, deionized water ultrasonic cleaning and drying treatment on the diffusion couple obtained in the step (3), performing microstructure analysis by using an electronic probe, determining the region where the BCC phase is located, performing component gradient distribution quantitative analysis by using a spectrum, determining the elastic modulus distribution by using a nano indenter, and further establishing an experimental database corresponding to the components and the elastic modulus, wherein the curve of the elastic modulus changing along with the components of the diffusion couple is shown in figure 8. By comparing the changes of the elastic modulus at different compositions, BCC phase Ti with the lowest elastic modulus, 8.22 at.% Nb, 2.68 at.% Zr and 0.83 at.% Cr alloy (the elastic modulus is 46.35GPa) is quickly screened out.
The above embodiments are preferred embodiments of the present invention, but the present invention is not limited to the above embodiments, and any other changes, modifications, substitutions, combinations, and simplifications which do not depart from the spirit and principle of the present invention should be construed as equivalents thereof, and all such changes, modifications, substitutions, combinations, and simplifications are intended to be included in the scope of the present invention.
Claims (8)
1. A method for rapidly screening low-elasticity-modulus biological titanium alloy is characterized by comprising the following steps:
(1) determining the components of two terminal components of a diffusion couple to be researched by adopting a phase diagram calculation method, namely calculating a component-temperature phase diagram for a binary system; calculating isothermal cross-sectional diagrams of different temperatures for the ternary system; calculating a phase relation diagram of alloys with different components for a multi-element system; then, determining a region where a BCC phase with titanium mass percent higher than 50% is located in a composition-temperature phase diagram or an isothermal cross-section diagram or a phase relation diagram of alloys with different compositions, and taking component values corresponding to two titanium alloys with the largest composition difference in the region, namely two endpoint values when the gradient of the titanium alloy composition is the largest, namely two endpoint component compositions of the diffusion couple to be researched;
(2) according to the two terminal component components determined in the step (1), smelting by taking pure metal as a raw material to obtain two terminal component metal ingots, then carrying out linear cutting on the obtained metal ingots to obtain uniform blocks of a metal ingot core part, cleaning the surfaces of the blocks, sealing the blocks into a vacuum container with sponge titanium or sponge yttrium, carrying out annealing treatment, taking out the blocks for quenching after annealing, and carrying out grinding and polishing on the blocks to obtain two terminal components of a diffusion couple;
(3) fixing the two terminal elements obtained in the step (2) together, sealing the two terminal elements into a vacuum container in which titanium sponge or yttrium sponge is stored, annealing, and taking out the blocks fixed together after annealing for quenching to obtain a diffusion couple;
(4) analyzing the microstructure of the diffusion couple obtained in the step (3) so as to determine a region where the BCC phase is located, performing component gradient analysis and elastic modulus test on the region to obtain batch experimental data of the BCC phase alloy component-elastic modulus of the titanium alloy, and finally determining the corresponding titanium alloy component according to the lowest value of the elastic modulus;
the microstructure analysis is carried out by adopting an electronic probe, a scanning electron microscope or a three-dimensional atom probe;
the component gradient analysis method adopts a spectrometer to carry out fixed-point analysis or an energy spectrometer to carry out surface scanning;
the method for testing the elastic modulus is nano indentation.
2. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: the components of the terminal elements in the step (1) are pure metal components or alloy components.
3. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: and (3) the vacuum degree in the container in the step (2) is less than 10Pa, the annealing temperature is 900-1200 ℃, and the annealing time is 2-10 days.
4. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: and (3) adopting an arc melting method for melting, wherein in the melting process, volatile metal is placed below, high-melting metal is crushed and placed above, and the metal ingot is turned over for multiple times to ensure that the components of the metal ingot are uniform, and the melting temperature is higher than the liquid phase temperature corresponding to the components obtained after phase diagram calculation.
5. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: and (3) the block is ground and polished in a mode of sequentially carrying out sand paper grinding, mechanical polishing, deionized water or ethanol ultrasonic cleaning and low-temperature drying on the block, and finally the surface of the sample is clean, bright, free of obvious scratches and free of an oxide film.
6. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: the method for fixing the two terminal components together in the step (3) adopts a high-purity molybdenum clamp to fix the two terminal components, so that the two terminal components can be tightly attached together and do not generate obvious deformation.
7. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: and (4) the vacuum degree in the container in the step (3) is less than 10Pa, the annealing temperature is 900-1200 ℃, and the annealing time is 6-48 hours.
8. The method for rapidly screening the low elastic modulus biological titanium alloy according to claim 1, which is characterized in that: the quenching method in the step (2) and the step (3) is to place the mixture in an ice-water mixture.
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| CN110340331B (en) * | 2019-07-31 | 2020-12-11 | 贵研铂业股份有限公司 | Method for efficiently preparing ternary diffusion couple |
| CN110715949A (en) * | 2019-11-19 | 2020-01-21 | 桂林电子科技大学 | Method for drawing isothermal cross-section phase diagram of La-Fe-B system by diffusion multi-element junction |
| CN111044544B (en) * | 2019-12-18 | 2022-11-18 | 山东省科学院新材料研究所 | In-situ quantitative detection method for diffusion growth of multi-element intermetallic compound and application |
| CN111136268B (en) * | 2020-01-13 | 2022-04-19 | 桂林电子科技大学 | High-throughput alloy preparation and Ho-Fe-B phase diagram test method |
| CN113528990A (en) * | 2021-06-17 | 2021-10-22 | 暨南大学 | Low-modulus high-strength high-wear-resistance biological titanium alloy and preparation method and application thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005064026A1 (en) * | 2003-12-25 | 2005-07-14 | Institute Of Metal Research Chinese Academy Of Sciences | Super elasticity and low modulus ti alloy and its manufacture process |
| CN105256172A (en) * | 2015-11-26 | 2016-01-20 | 上海理工大学 | Improved medical low-modulus titanium alloy and preparation method thereof |
-
2018
- 2018-08-03 CN CN201810874848.5A patent/CN109055815B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005064026A1 (en) * | 2003-12-25 | 2005-07-14 | Institute Of Metal Research Chinese Academy Of Sciences | Super elasticity and low modulus ti alloy and its manufacture process |
| CN105256172A (en) * | 2015-11-26 | 2016-01-20 | 上海理工大学 | Improved medical low-modulus titanium alloy and preparation method thereof |
Non-Patent Citations (3)
| Title |
|---|
| A novel combinatorial approach to the development of beta titanium alloys for orthopaedic implants;Banerjee等;《Materials Science and Engineering C》;20050505;第25卷(第3期);第282页左栏第1段、第283页右栏第2段至第284页左栏第2段、第285页右栏第1段 * |
| Design and mechanical properties of new β type titanium alloys;Kuroda等;《Materials Science and Engineering A》;19980315;第243卷(第1-2期);全文 * |
| β钛合金成分设计：理论、方法、实践;王光荣等;《材料导报Ａ：综述篇》;20170228;第31卷(第2期);全文 * |
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