CN111270102B - Near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa and preparation method thereof - Google Patents
Near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa and preparation method thereof Download PDFInfo
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Abstract
The invention provides a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa, wherein the volume fraction of a primary alpha phase in the near-beta ultrahigh-strength titanium alloy is 15-30%, and a secondary alpha phase is uniformly distributed on a beta matrix. The preparation method comprises the following steps: (1) determining a trunk component system of the novel ultrahigh-strength titanium alloy; (2) measuring the beta transformation temperature, performing cogging forging above the beta transformation temperature of the titanium alloy ingot, and then gradually reducing the forging temperature to below the beta transformation temperature to perform repeated upsetting-drawing forging; (3) setting the temperature of the finish forging process below the beta transition temperature to obtain an ultrahigh-strength titanium alloy forging stock; (4) after the ultrahigh-strength titanium alloy forging stock in the hot working state is subjected to solution treatment and double aging strengthening treatment, the near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa is obtained. The strength of the ultrahigh-strength titanium alloy reaches over 1450MPa, and simultaneously, the comprehensive performance matching of good plasticity, toughness and the like can be met.
Description
Technical Field
The invention belongs to the technical field of metal materials, and relates to a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa and a preparation method thereof.
Background
Titanium alloy is used as a novel light metal material developed in recent decades, and has excellent comprehensive performance matching of strength, modulus, toughness, high damage tolerance, corrosion resistance, weldability and the like, so that the titanium alloy becomes one of main structural materials of advanced airplanes. The application of titanium and titanium alloy in the airplane body structure can obtain good weight-reducing benefit, meet the design requirements of high maneuverability, high reliability and long service life of the airplane, and the use amount of the titanium and titanium alloy becomes an important mark for measuring the advanced degree of airplane material selection.
Titanium alloys have undergone the development process from low strength, medium strength to high strength, and at present, ultrahigh strength titanium alloys (replacing ultrahigh strength structural steel) become an important trend in the development of titanium alloys in various countries. The high-strength titanium alloy generally refers to titanium alloy with tensile strength of more than 1100MPa, and the application of the high-strength titanium alloy on an airplane mainly comprises important structural components such as a torsion arm and a strut of an undercarriage, a bearing frame beam of an airplane body and the like.
At present, the high-strength titanium alloy mainly takes beta titanium alloy as a main part, and comprises partial alpha + beta two-phase alloy, and the alloying is mainly characterized in that more beta stable elements, such as Mo, V, Cr, Mn, Nb, Fe and the like, are added, the content of impurity gas elements such as N, O, H and the like is strictly controlled, and the stable beta-phase structure is obtained by carrying out solid solution and aging treatment at high temperature. Beta titanium alloy has been widely concerned at home and abroad due to its high strength, good cold formability and good strong plasticity matching, especially near beta and metastable beta alloys, which have the performance advantages of two-phase alloys and beta alloys. According to the difference of Mo equivalent, the beta type titanium alloy can be subdivided into four types, when the Mo equivalent is 0-5, the beta-rich stable element alpha + beta type titanium alloy is obtained; when the Mo equivalent is between 5 and 10, the alloy is called a near beta type titanium alloy; when the Mo equivalent is between 10 and 30, the alloy is called metastable beta-type titanium alloy; when the Mo equivalent is more than 30, the alloy is called stable beta type titanium alloy. High-strength titanium alloys having international advanced levels and being practically applied in the field of aviation mainly include beta type titanium alloys Ti-1023(Ti-10V-2Fe-3Al), Ti-15-3(Ti-15V-3Cr-3Sn-3Al), beta-21S (Ti-15Mo-2.7Nb-3Al-0.2Si), Ti-5553(Ti-5Al-5Mo-5V-3Cr-0.5Fe), and alpha + beta type two-phase titanium alloys BT22(Ti-5V-5Mo-1Cr-1Fe-5Al) and the like.
In order to realize design ideas of light weight, long service life, high reliability and the like, a new generation of airplane provides more urgent weight reduction requirements for a main load-bearing structure, the titanium alloy is required to have higher strength and excellent comprehensive performance, namely, the static strength, the fracture, the fatigue and other performances are improved and matched, and meanwhile, the fatigue performance and the reliability of the structure are effectively improved, so that the service life of the airplane is ensured. However, for titanium alloys, strength properties are often incompatible with plasticity and toughness. The existing high-strength titanium alloy generally sacrifices the plasticity and toughness while improving the strength, for example, the existing latest Ti-5553 high-strength titanium alloy has excellent strength-plasticity matching and fatigue performance at 1200MPa, and the plasticity is obviously reduced along with the further increase of the strength, so that the further application of the alloy under the condition of higher strength is severely restricted.
Disclosure of Invention
(1) Technical problem to be solved
With the continuous improvement of the strength, the comprehensive performances such as plasticity, toughness, fatigue property, damage tolerance property and the like of the ultrahigh-strength titanium alloy are reduced to different degrees, so that the ultrahigh-strength titanium alloy becomes a main reason that the performance potential of the ultrahigh-strength titanium alloy is difficult to fully exert, and is also an important factor for limiting the further application of the ultrahigh-strength titanium alloy on new-generation weapons. Aiming at the problems, the invention mainly provides a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa and a preparation method thereof, so that the strength of the near-beta ultrahigh-strength titanium alloy reaches above 1450MPa, and simultaneously, the high comprehensive performance matching of plasticity, toughness and the like can be met, and the engineering application of the ultrahigh-strength titanium alloy is further promoted.
(2) Technical scheme
The near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa has the volume fraction of a primary alpha phase of 15-30% and a secondary alpha phase uniformly distributed on a beta matrix.
A preparation method of a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa comprises the following operation steps:
(1) determining a main component system of the novel ultrahigh-strength titanium alloy, and realizing active optimization design of the components of the novel ultrahigh-strength titanium alloy: calculating the types and ranges of the main components of the novel ultrahigh-strength titanium alloy by using a first principle and combining a CALPHAD calculation tool on the basis of multi-component reinforcement under the condition of critical molybdenum equivalent, checking the preliminarily obtained main components of the novel ultrahigh-strength titanium alloy by using a component design method, and finally determining a main component system of the novel ultrahigh-strength titanium alloy, wherein the component design method comprises a molybdenum equivalent and a d-electron theoretical method;
(2) preparing a titanium alloy ingot with uniform chemical components and tissues by three times of vacuum consumable melting according to an obtained ultrahigh-strength titanium alloy main component system, measuring the beta transition temperature of the titanium alloy ingot, cogging and forging the titanium alloy ingot above the beta transition temperature, then gradually reducing the forging temperature to below the beta transition temperature for repeated upsetting and forging, cogging and forging the titanium alloy ingot above the beta transition temperature, crushing original coarse grains of the ingot, gradually reducing the forging temperature to below the beta transition temperature for repeated upsetting and forging, and realizing static and dynamic recrystallization of alloy tissues, fully refining the grains and realizing regulation and control of the titanium alloy blank tissue uniformity through multiple-fire-time forging modification;
(3) designing the temperature of a finish forging process to be set in a temperature range of 30-70 ℃ below a beta transition temperature, obtaining a target forging stock structure with primary alpha phases uniformly distributed at the three-fork junction of fine beta grains through finish forging to obtain an ultrahigh-strength titanium alloy forging stock, forming an ultrahigh-strength titanium alloy toughening leading process, establishing the relationship between process parameters and structure-performance, and obtaining an ultrahigh-strength titanium alloy toughening forging technology, thereby realizing the active regulation and control of the microstructure of the ultrahigh-strength titanium alloy forging stock;
(4) and carrying out solution treatment and double aging strengthening treatment on the ultrahigh-strength titanium alloy forging stock in a hot working state, wherein the temperature of the solution treatment is set in a temperature range of 10-50 ℃ below the beta transition temperature, and the temperature of the first aging strengthening is 150-240 ℃ lower than that of the second aging strengthening, so that the final microstructure of the ultrahigh-strength titanium alloy material is further actively controlled, and the near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa is obtained. Through solution treatment at the temperature of 10-50 ℃ below the beta transition temperature, a large amount of metastable beta phases can be formed in the structure, and the primary alpha phase obtained in the forging process can inhibit excessive growth of beta grains. An intermediate transition phase (isothermal omega phase) is firstly precipitated through low-temperature aging, and then the transition phase can induce a large amount of secondary alpha phase to be dispersed and precipitated in the high-temperature aging process. The secondary alpha phase precipitated by the mode of beta → omega → alpha is finer and more dispersed, the crystal grains can be further refined, and the performance is improved. By designing different aging process parameters, the size, the form, the distribution and the quantity of precipitated phases can be actively regulated and controlled, so that the precipitation strengthening is realized, and the strength of the beta titanium alloy is greatly improved.
According to the technical scheme, the beneficial effects of the invention are as follows:
(1) the invention guides the design and optimization of the components of the ultrahigh-strength titanium alloy by a comprehensive titanium alloy component design method, combines a small amount of tests, quickly screens and determines the target components of the novel ultrahigh-strength titanium alloy, can obviously shorten the development period and reduce the development cost;
(2) according to the invention, the cast ingot is subjected to multi-pass cogging forging, a finish forging process within a temperature range of 30-70 ℃ below the beta transition temperature is selected, and a strengthening and toughening heat treatment process of solid solution and double aging is combined to realize active control on the microstructure of the ultrahigh-strength titanium alloy material, so that a comprehensive strengthening and toughening technology of a novel ultrahigh-strength titanium alloy system is established.
(3) The novel ultrahigh-strength titanium alloy obtained by the method has the static strength of more than or equal to 1450MPa, the elongation of more than or equal to 6 percent and the fracture toughness of more than or equal to 45 MPa.m1/2The method realizes good matching of comprehensive properties of the titanium alloy, and provides theoretical and material technical basis for promoting engineering application of the ultrahigh-strength titanium alloy, further forming an aviation titanium alloy material system in China and meeting the future requirements on the ultrahigh-strength titanium alloy material.
Drawings
FIG. 1 is a microstructure of an ultra-high strength titanium alloy after solution treatment and double aging strengthening treatment in example I;
FIG. 2 is an SEM picture of a tensile fracture of the ultrahigh-strength titanium alloy in the first embodiment;
FIG. 3 is a microstructure of the ultra-high strength titanium alloy after solution treatment and double aging strengthening treatment in example II;
FIG. 4 is an SEM picture of the tensile fracture of the ultrahigh-strength titanium alloy in example II;
FIG. 5 is a microstructure of the ultra-high strength titanium alloy after solution treatment and double aging strengthening treatment in example III;
figure 6 SEM picture of tensile fracture of ultra-high strength titanium alloy in example three.
Detailed Description
The present invention will be described in further detail with reference to specific examples, but the scope of the present invention is not limited to these examples, and all changes or equivalent substitutions that do not depart from the spirit of the present invention are intended to be included within the scope of the present invention.
Example 1
A preparation method of Ti-Al-V-Mo-Cr series near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa comprises the following operation steps:
(1) determining a main component system of the novel ultrahigh-strength titanium alloy, and realizing active optimization design of the components of the novel ultrahigh-strength titanium alloy: the method comprises the following steps of calculating the types and ranges of novel ultrahigh-strength titanium alloy main components by using a first principle and combining a CALPHAD calculation tool on the basis of multi-component reinforcement under the condition of critical molybdenum equivalent, checking the preliminarily obtained novel ultrahigh-strength titanium alloy main components by a component design method, and finally determining a main component system of the novel ultrahigh-strength titanium alloy, wherein the component design method comprises a molybdenum equivalent and d electronic theory method, the measured Ti-Al-V-Mo-Cr system alloy main components are Ti-Al-V-Mo-Cr-Fe, and the weight percentages of the elements are as follows: 2.5 to 4 percent of aluminum, 6.5 to 8 percent of vanadium, 2.5 to 4 percent of molybdenum, 1 to 2 percent of chromium, 1 to 2.5 percent of iron, less than or equal to 0.05 percent of carbon, less than or equal to 0.05 percent of nitrogen, less than or equal to 0.015 percent of hydrogen, less than or equal to 0.15 percent of oxygen, and the balance of titanium and inevitable impurity elements;
(2) preparing a titanium alloy ingot with uniform chemical components and tissues by three times of vacuum self-consumption smelting according to an obtained ultrahigh-strength titanium alloy main component system, measuring the beta transition temperature of the titanium alloy ingot to be 800-810 ℃, performing cogging forging at the temperature range of 1050-1100 ℃, crushing original coarse grains of the ingot, then gradually reducing the forging temperature to be below a phase transformation point for repeated upsetting forging, and realizing static and dynamic recrystallization of a microstructure of the ingot through multiple-fire forging modification, and cooperatively regulating the structure and the performance of the ingot;
(3) performing finish forging at the temperature of 740-770 ℃ to obtain a certain amount of target forging stock tissues with primary alpha phases uniformly distributed at the trifurcate junctions of fine beta grains to obtain ultrahigh-strength titanium alloy forging stocks;
(4) carrying out solid solution and double aging treatment on the titanium alloy forging stock in the hot working state obtained in the step, carrying out solid solution treatment in a temperature range of 750-780 ℃ to form a metastable beta phase, wherein a primary alpha phase can inhibit excessive growth of beta grains, then carrying out low-temperature aging in a temperature range of 300-350 ℃ to separate out an intermediate transition omega phase, then carrying out high-temperature aging in a temperature range of 500-540 ℃ to induce dispersion separation of a secondary alpha phase, and the alpha phase separated out in the way is fine and dispersed and can further refine the grains, so that precipitation strengthening is realized, and the finally obtained microstructure of the near-beta ultrahigh-strength titanium alloy is shown in figure 1. The performance test result shows that the finally prepared near-beta ultrahigh-strength titanium alloy has the tensile strength of 1486MPa, the yield strength reaches more than 1350MPa, the elongation reaches more than 6 percent, the reduction of area reaches more than 20 percent, and the fracture toughness is 45-70 MPa.m1/2And the excellent matching of the comprehensive properties of the titanium alloy is achieved, and the SEM picture of the near-beta ultrahigh-strength titanium alloy tensile fracture prepared by the embodiment is shown in FIG. 2.
Example 2
A preparation method of a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa comprises the following operation steps:
(1) in this embodiment, the main component system of the ultrahigh-strength titanium alloy is: according to the weight percentage, 3 to 4 percent of aluminum, 6 to 7 percent of vanadium, 5 to 6 percent of molybdenum, 1.5 to 3 percent of chromium and 0.5 to 2 percent of iron;
(2) preparing a titanium alloy ingot with uniform chemical components and tissues by three times of vacuum consumable melting, measuring the beta transition temperature of the titanium alloy ingot to be 830-840 ℃, performing cogging forging at the temperature range of 1050-1100 ℃, crushing original coarse grains of the ingot, then gradually reducing the forging temperature to be below a phase transformation point, performing repeated upsetting forging, and performing multiple-fire re-forging to realize static and dynamic recrystallization of a microstructure of the titanium alloy ingot and cooperatively regulate the structure and performance of the titanium alloy ingot;
(3) performing finish forging at the temperature range of 770-800 ℃ to obtain a certain amount of target forging stock tissues with primary alpha phases uniformly distributed at the trifurcate junctions of fine beta grains to obtain ultrahigh-strength titanium alloy forging stocks;
(4) carrying out solid solution and double aging treatment on the titanium alloy forging stock in the hot working state obtained in the step, carrying out solid solution treatment in a temperature range of 780-810 ℃ to form a metastable beta phase, wherein a primary alpha phase can inhibit excessive growth of beta grains, then carrying out low-temperature aging in a temperature range of 300-350 ℃ to separate out an intermediate transition omega phase, then carrying out high-temperature aging in a temperature range of 500-540 ℃ to induce dispersion separation of a secondary alpha phase, and the alpha phase separated out in the way is fine and dispersed and can further refine the grains, so that precipitation strengthening is realized, and the finally obtained microstructure of the near-beta ultrahigh-strength titanium alloy is shown in figure 3. The performance test result shows that the finally prepared near-beta ultrahigh-strength titanium alloy has the tensile strength of 1477MPa, the yield strength of more than 1350MPa and the elongation ofMore than 6 percent, the reduction of area is more than 20 percent, and the fracture toughness is 45-65 MPa.m1/2And excellent matching of comprehensive properties of the titanium alloy is achieved, and an SEM picture of the near-beta ultrahigh-strength titanium alloy tensile fracture prepared by the embodiment is shown in FIG. 4.
Example 3
A preparation method of a near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa comprises the following operation steps:
(1) in this embodiment, the main component system of the ultrahigh-strength titanium alloy is: according to the weight percentage, 5.5 to 7 percent of aluminum, 2 to 4 percent of vanadium, 3 to 5 percent of molybdenum, 4 to 5.5 percent of chromium and 2 to 3 percent of zirconium;
(2) preparing a titanium alloy ingot with uniform chemical components and tissues by three times of vacuum consumable melting, measuring the beta transition temperature of the titanium alloy ingot to be 840-850 ℃, performing cogging forging at the temperature range of 1050-1100 ℃, crushing original coarse grains of the ingot, then gradually reducing the forging temperature to be below a phase transformation point, performing repeated upsetting forging, and performing multiple-fire re-forging to realize static and dynamic recrystallization of a microstructure of the titanium alloy ingot and cooperatively regulate the structure and performance of the titanium alloy ingot;
(3) performing finish forging at the temperature of 780-810 ℃ to obtain a certain amount of target forging stock tissues with primary alpha phases uniformly distributed at the trifurcate junctions of fine beta grains to obtain ultrahigh-strength titanium alloy forging stocks;
(4) carrying out solid solution and double aging treatment on the titanium alloy forging stock in the hot working state obtained in the step, carrying out solid solution treatment in a temperature range of 790-820 ℃ to form a metastable beta phase, wherein a primary alpha phase can inhibit excessive growth of beta grains, then carrying out low-temperature aging in a temperature range of 300-350 ℃ to separate out an intermediate transition omega phase, then carrying out high-temperature aging in a temperature range of 500-540 ℃ to induce dispersion separation of a secondary alpha phase, and the alpha phase separated out in the way is fine and dispersed and can further refine the grains, so that precipitation strengthening is realized, and the finally obtained microstructure of the near-beta ultrahigh-strength titanium alloy is shown in figure 5. The performance test result shows that the finally prepared near-beta ultrahigh-strength titanium alloy has the tensile strength of 1534MPa, the yield strength of more than 1400MPa, the elongation of more than 6 percent, the reduction of area of more than 18 percent and the fractureThe toughness is 40 to 65 MPa.m1/2And excellent matching of comprehensive properties of the titanium alloy is achieved, and an SEM picture of the near-beta ultrahigh-strength titanium alloy tensile fracture prepared by the embodiment is shown in FIG. 6.
The above description is only an example of the present application and is not limited to the present application. Various modifications and alterations to this application will become apparent to those skilled in the art without departing from the scope of this invention. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present application should be included in the scope of the claims of the present application.
Claims (6)
1. The near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa is characterized by comprising the following elements in percentage by weight: 2.5 to 4 percent of aluminum, 6.5 to 8 percent of vanadium, 2.5 to 4 percent of molybdenum, 1 to 2 percent of chromium, 1 to 2.5 percent of iron, less than or equal to 0.05 percent of carbon, less than or equal to 0.05 percent of nitrogen, less than or equal to 0.015 percent of hydrogen, less than or equal to 0.15 percent of oxygen, and the balance of titanium and inevitable impurity elements;
the volume fraction of a primary alpha phase in the near-beta ultrahigh-strength titanium alloy is 15-30%, and a secondary alpha phase is uniformly distributed on a beta matrix.
2. A method for preparing the near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa according to claim 1, which comprises the following operation steps:
(1) determining a trunk component system of the novel ultrahigh-strength titanium alloy;
(2) according to the obtained ultrahigh-strength titanium alloy main component system, preparing a titanium alloy ingot with uniform chemical components and tissues by vacuum consumable melting, measuring the beta transition temperature of the titanium alloy ingot, cogging and forging the titanium alloy ingot above the beta transition temperature, and then gradually reducing the forging temperature to below the beta transition temperature for repeated upsetting-drawing forging;
(3) setting the temperature of the finish forging process below a beta transition temperature, and obtaining a target forging stock structure with primary alpha phases uniformly distributed at a fine beta grain trifurcate junction through finish forging to obtain an ultrahigh-strength titanium alloy forging stock;
(4) carrying out solid solution treatment and double aging strengthening treatment on the ultrahigh-strength titanium alloy forging stock in a hot working state to obtain a near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450 MPa;
in the step (1), the operation of determining the trunk component system of the novel ultrahigh-strength titanium alloy is as follows: calculating the types and ranges of the main components of the novel ultrahigh-strength titanium alloy by using a first principle and combining a CALPHAD calculation tool according to a principle of multi-component reinforcement under a critical molybdenum equivalent condition, checking the preliminarily obtained main components of the novel ultrahigh-strength titanium alloy by a component design method, and finally determining a main component system of the novel ultrahigh-strength titanium alloy;
and in the double aging strengthening treatment, the temperature of the first aging strengthening is 150-240 ℃ lower than that of the second aging strengthening.
3. The method of claim 2, wherein the composition design method comprises molybdenum equivalent and d-electron theory.
4. The method for preparing the near-beta ultrahigh-strength titanium alloy with the tensile strength of more than 1450MPa according to claim 2, wherein in the step (2), the number of times of vacuum consumable melting is three.
5. The method for preparing near-beta ultrahigh-strength titanium alloy with tensile strength of more than 1450MPa according to claim 2, wherein in the step (3), the temperature of the finish forging process is set within a temperature range of 30-70 ℃ below the beta transus temperature.
6. The method according to claim 2, wherein the solution treatment temperature in the step (3) is set within a temperature range of 10 to 50 ℃ below the β transformation temperature.
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| CN113046591B (en) * | 2021-03-12 | 2022-04-29 | 中国航空制造技术研究院 | In-situ self-generated TiB reinforced beta titanium alloy composite material and preparation method thereof |
| CN113355559B (en) * | 2021-08-10 | 2021-10-29 | 北京煜鼎增材制造研究院有限公司 | High-strength high-toughness high-damage-tolerance titanium alloy and preparation method thereof |
| CN114959362B (en) * | 2022-06-20 | 2023-03-14 | 长安大学 | High-strength high-plasticity laser additive manufacturing titanium alloy based on equiaxial fine grain strengthening |
| CN116240478A (en) * | 2023-03-27 | 2023-06-09 | 西北工业大学 | Heat treatment method for improving strength of metastable beta titanium alloy to more than 1400MPa |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5698050A (en) * | 1994-11-15 | 1997-12-16 | Rockwell International Corporation | Method for processing-microstructure-property optimization of α-β beta titanium alloys to obtain simultaneous improvements in mechanical properties and fracture resistance |
| CN103243235A (en) * | 2013-05-22 | 2013-08-14 | 哈尔滨工业大学 | High strength titanium alloy |
| CN103924180A (en) * | 2014-04-08 | 2014-07-16 | 中南大学 | Thermal treatment method for TC18 titanium alloy |
| CN104451491A (en) * | 2014-12-15 | 2015-03-25 | 西北有色金属研究院 | Preparation method of Ti12LC titanium alloy forge piece |
| CN107217173A (en) * | 2017-05-27 | 2017-09-29 | 中国科学院金属研究所 | Titanium alloy and its preparation technology with high-strength high-plastic and good fracture toughness |
| CN108456805A (en) * | 2018-04-20 | 2018-08-28 | 温州市赢创新材料技术有限公司 | A kind of beta titanium alloy and its manufacturing method for being implanted into bone |
| CN108486408A (en) * | 2018-04-18 | 2018-09-04 | 王甲林 | A kind of low elastic modulus dental filling beta titanium alloy and its manufacturing method |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10053759B2 (en) * | 2014-08-29 | 2018-08-21 | Northwestern University | Computationally-designed transformation-toughened near-alpha titanium alloy |
-
2020
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Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5698050A (en) * | 1994-11-15 | 1997-12-16 | Rockwell International Corporation | Method for processing-microstructure-property optimization of α-β beta titanium alloys to obtain simultaneous improvements in mechanical properties and fracture resistance |
| CN103243235A (en) * | 2013-05-22 | 2013-08-14 | 哈尔滨工业大学 | High strength titanium alloy |
| CN103924180A (en) * | 2014-04-08 | 2014-07-16 | 中南大学 | Thermal treatment method for TC18 titanium alloy |
| CN104451491A (en) * | 2014-12-15 | 2015-03-25 | 西北有色金属研究院 | Preparation method of Ti12LC titanium alloy forge piece |
| CN107217173A (en) * | 2017-05-27 | 2017-09-29 | 中国科学院金属研究所 | Titanium alloy and its preparation technology with high-strength high-plastic and good fracture toughness |
| CN108486408A (en) * | 2018-04-18 | 2018-09-04 | 王甲林 | A kind of low elastic modulus dental filling beta titanium alloy and its manufacturing method |
| CN108456805A (en) * | 2018-04-20 | 2018-08-28 | 温州市赢创新材料技术有限公司 | A kind of beta titanium alloy and its manufacturing method for being implanted into bone |
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