CN109487121A - A kind of gear division titanium alloy and preparation method thereof - Google Patents
A kind of gear division titanium alloy and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C14/00—Alloys based on titanium
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- C22C1/02—Making non-ferrous alloys by melting
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- 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
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Abstract
The invention discloses a kind of gear division titanium alloys and preparation method thereof, belong to titanium alloy material design and preparation technical field, which has high-intensitive and good plasticity, and preparation process is simple.The present invention includes: following weight percent chemical component: Zr:0.5 wt% ~ 4.5 wt%, O:0.05 wt% ~ 0.4 wt%, surplus Ti, nano-twin crystal structure occurs in alloy；Alloy cast ingot is obtained using vacuum melting method, pyroplastic deformation is carried out in different phase regions after homogenizing annealing, obtains final shape.Titanium alloy of the invention intensity with higher, tensile strength reaches as high as 955 MPa, and has good plasticity, and elongation after fracture reaches as high as 30%；The system alloy has α homogeneous structure, compatible with SLA process of surface treatment with dental implant, excellent without bio-toxicities element, biocompatibilities such as Al, V；Added alloy element is less, and preparation process is simple, and economic cost is lower, has broad application prospects in oral cavity restoration field.
Description
Technical field
The invention belongs to titanium alloy material design and preparation technical field more particularly to a kind of gear division titanium alloy and its systems
Preparation Method.
Background technique
Titanium or titanium alloy has excellent biocompatibility, splendid corrosion resistance and suitable mechanical property, it has also become state
Inside and outside widely used bio-medical material.In gear division field, at present the medical pure titanium and the titanium alloy trade mark of mainstream be TA2 and
TC4, and the tensile strength of TA2 only has 400MPa or so, it is unbearable compared with big load；Although then intensity is higher for TC4 alloy, modeling
Property it is poor and also poor containing bio-toxicities element, the biocompatibility such as Al, V.Zirconium be the neutral element of the same clan with titanium, have compared with
High biological safety, and can be infinitely dissolved in α and the β phase of titanium；Since titanium is different from the atomic radius of zirconium, in Titanium base
Middle addition zirconium can play solution strengthening, significantly improve the strength of materials, and improve matrix corrosion resistance.In addition, having single-phase group of α
The Ti-Zr alloy and dental implant SLA process for treating surface compatibility knitted are splendid, at the same have both excellent biocompatibility and
Mechanical property.Therefore, in oral cavity restoration field, Ti-Zr alloy is a kind of medical material having a extensive future.
Recently, the research about Ti-Zr bianry alloy mechanical property is increasing.Bernhard etc. develops a kind of entitledTi-Zr alloy (Zr:13wt%~17wt%), tensile strength is up to 953MPa (Bernhard N, Berner
S,De Wild M,et al.The binary TiZr alloy-A newly developed Ti alloy for use in
Dental implants, Forum Implantologicum, 2009,5:30-39), but its described titanium alloy zirconium content is higher,
Processing method is complicated, and preparation cost is higher.Steinemann is on May 1st, 2012, Publication No. in publication date
Proposed in the United States Patent (USP) of US8168012B2 a kind of Ti-Zr alloy (Zr:5wt%~25wt%, O:0.1wt%~
0.3wt%) and its preparation process, when adding micro oxygen element and carrying out subsequent cold working, the tensile strength of alloy can for discovery
Close to 1000MPa, due to solution strengthening and processing hardening, although system Ti-Zr alloy intensity has a distinct increment, plasticity is anxious
It falls sharply low.The oxygen that Vicente etc. passes through addition 0.02wt%~0.04wt% in Ti-Zr alloy (Zr:5wt%~15wt%)
Element, discovery in the composition range crystal structure of alloy, microscopic structure and biocompatibility without significant change, described in
Ti-Zr alloy does not embody the intensity and plasticity level (Vicente F B, Correa D R N, Donato T suitable for gear division
A G,et al,The influence of small quantities of oxygen in the structure,
microstructure,hardness,elasticity modulus and cytocompatibility of Ti-Zr
alloys for dental applications,Materials,2014,7(1):542–553).Zhou Yunkai etc. has studied not
The as cast condition Ti-Zr alloy of same zirconium content (Zr:17wt%~94wt%) finds Ti-70wt%Zr strength of alloy highest, is
1216.68MPa, but elongation is only 7.12% (Zhou Y K, Jing R, Ma M Z, et al, Tensile strength
of Zr-Ti binary alloy,Chinese Physics Letters,2013,30(11):116201).In addition, they are also
It was found that hot rolling technology has significant strengthening effect for Ti-65wt%Zr alloy, tensile strength reaches as high as 1135MPa,
But elongation after fracture is only 3% (Zhou Y K, Liang S X, Jing R, et al, Microstructure and
tensile properties of hot-rolled Zr50-Ti50binary alloy,Materials Science&
Engineering A,2014,621:259-264).Above two alloy zirconium content is excessively high, not only increases cost of material, together
Shi Yanchong reduces plasticity.Matayshi etc. have studied different zirconium contents rolling state Ti-Zr alloy (Zr:2wt%,
10wt%), discovery Ti-10wt%Zr alloy has maximum pulling strength, is 877MPa, but elongation is only 6.2%, resultant force
Learn not ideal enough (Matayshi Y, Homma T, the Effect of Zr addition on recrystallization of performance
behavior in rolled Ti-Zr alloys,TMS(The Minerals,Metals&Materials Society)
Supplemental Proceedings,2015,979-988)。
In conclusion the zirconium content of Ti-Zr alloy is generally greater than 5wt% in research at present, cost of material is higher；And it can not
The contradiction between high-intensitive and inductile is solved by simple and easy preparation method.
Summary of the invention
The present invention provides a kind of gear division titanium alloy and preparation method thereof, the titanium alloy has the same of high intensity
When, good plasticity is had both, and added alloy element is less, preparation process is simple, and economic cost is lower.
In order to achieve the above object, the invention adopts the following technical scheme:
A kind of gear division titanium alloy, including following weight percent chemical component:
Zr:0.5wt%~4.5wt%；
O:0.05wt%~0.4wt%；
Surplus is Ti.
There is the twin structure of nanoscale in titanium alloy described above.
A kind of preparation method of gear division titanium alloy, comprising the following steps:
Step 1: according to composition proportion, raw material is subjected to multiple vacuum melting, obtains the uniform alloy cast ingot of ingredient；
Step 2: alloy cast ingot described in step 1 is placed in vacuum drying oven, carries out homogenizing annealing under protection of argon gas,
Subsequent slow cooling is to room temperature；
Step 3: the alloy cast ingot after homogenizing annealing described in step 2 is subjected to thermoplastic forming simultaneously in different phase regions
It is cooled to room temperature, obtains final plate.
In step described above, homogenizing annealing heating temperature described in step 2 is 1000 DEG C~1100 DEG C, when heat preservation
Between be 6~8h, the type of cooling be furnace it is cold.
Thermoplastic forming heating temperature described in step 3 is 800 DEG C~1000 DEG C, and deflection is 85%~90%, cooling
Mode is air-cooled.
Beneficial effects of the present invention: the present invention provides a kind of gear division titanium alloy and preparation method thereof, the titanium alloys
Alloy element type and content are as follows: Zr (0.5wt%~4.5wt%), O (0.05wt%~0.4wt%), tensile strength highest
Up to 955MPa, reach alpha+beta type Ti-6Al-4V level of alloy；Elongation after fracture reaches as high as 30%, nanometer occurs in alloy
The twin of scale makes alloy have both good plasticity while having high-intensitive；And titanium alloy room temperature texture of the invention
It is all α homogeneous structure, it is mutually compatible with SLA process of surface treatment with existing dental implant；Without the bio-toxicities element such as Al, V,
Biocompatibility is excellent；Added alloy element is less, and preparation process is thermoplastic forming, and preparation process is simple, it is economical at
This lower, operability with higher；Its excellent comprehensive performance has fully met the requirement of clinical application, can be used as tooth kind
It plants body material and is used for oral cavity restoration field, have broad application prospects.
Detailed description of the invention
Fig. 1 is the X ray diffracting spectrum of titanium alloy of the present invention；
Fig. 2 is Ti-1Zr-0.05O alloy SLA of the present invention treated surface topography map；
Fig. 3 is Ti-1Zr-0.30O alloy SLA of the present invention treated surface topography map；
Fig. 4 is Ti-2Zr-0.10O alloy SLA of the present invention treated surface topography map；
Fig. 5 is the nano-twin crystal structure occurred in Ti-3Zr-0.25O alloy of the present invention；
Fig. 6 is Ti-3Zr-0.25O alloy SLA of the present invention treated surface topography map；
Fig. 7 is metallographic microscope after Ti-3Zr-0.30O alloy pyroplastic deformation of the present invention；
Fig. 8 is metallographic microscope after Ti-4Zr-0.25O alloy pyroplastic deformation of the present invention；
Fig. 9 is the nano-twin crystal structure occurred in Ti-4Zr-0.25O alloy of the present invention.
Specific embodiment
The present invention is specifically described in the following with reference to the drawings and specific embodiments:
Embodiment 1
Step 1: weight percentage of each component are as follows: Zr:1wt%, O:0.05wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1000 DEG C under protection of argon gas, keeps the temperature furnace after 8h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 950 DEG C of progress pyroplastic deformations, deflection 90%, with
After be air-cooled to room temperature, obtain final plate.
Material phase analysis: producing X-ray diffraction analysis sample with wire cutting from above-mentioned plate, is determined with X-ray diffractometer
Alloy object phase composition, scanning angle are 20 °~80 °, and scanning speed is 10 °/min.X ray diffracting spectrum is as shown in Figure 1, determine
Alloy is formed by α is single-phase.
Tensile test at room temperature: cutting out tensile sample from institute's alloyage with wire cutting, net specimen surface oxide skin of polishing, really
Determining sample marking distance is 20mm, with a thickness of 1.5mm, carries out tensile test at room temperature to sample on universal testing machine, stretches speed
Degree is 1mm/min, and one group of sample is measured in parallel 3 times.The specific data of tensile sample mechanical property are as shown in table 1, average tensile
Intensity is 510MPa, average yield strength 446MPa, and average elongation after fracture is 30%.
SLA (sandblasted and acid-etching) processing: SLA processing sample, sample table of polishing are cut from institute's alloyage with wire cutting
Face then carries out SLA processing to specimen surface to without obvious scratch and being cleaned by ultrasonic, and with scanning electron microscopic observation surface shape
Looks.Treated specimen surface pattern is as shown in Fig. 2, surface can form the typical multistage nested type three-dimensional hole knot of SLA processing
Structure.
Embodiment 2
Step 1: weight percentage of each component are as follows: Zr:1wt%, O:0.30wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1100 DEG C under protection of argon gas, keeps the temperature furnace after 6h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 1000 DEG C of progress pyroplastic deformations, deflection 88%, with
After be air-cooled to room temperature, obtain final shape.
Material phase analysis operating procedure is with embodiment 1, and X ray diffracting spectrum is as shown in Figure 1, determine that alloy is formed by α is single-phase.
For tensile test at room temperature operating procedure with embodiment 1, the specific data of tensile sample mechanical property are as shown in table 1, put down
Equal tensile strength is 885MPa, average yield strength 730MPa, and average elongation after fracture is 12.8%.
SLA processing operation step is with embodiment 1, and specimen surface pattern after processing is as shown in figure 3, surface can form SLA
The typical multistage nested type three-dimensional hole configurations of processing.
Embodiment 3
Step 1: weight percentage of each component are as follows: Zr:2wt%, O:0.10wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1000 DEG C under protection of argon gas, keeps the temperature furnace after 8h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 900 DEG C of progress pyroplastic deformations, deflection 88%, with
After be air-cooled to room temperature, obtain final shape.
Material phase analysis operating procedure is with embodiment 1, and X ray diffracting spectrum is as shown in Figure 1, determine that alloy is formed by α is single-phase.
For tensile test at room temperature operating procedure with embodiment 1, the specific data of tensile sample mechanical property are as shown in table 1, put down
Equal tensile strength is 601MPa, average yield strength 508MPa, and average elongation after fracture is 22.8%.
SLA processing operation step is with embodiment 1, and specimen surface pattern after processing is as shown in figure 4, surface can form SLA
The typical multistage nested type three-dimensional hole configurations of processing.
Embodiment 4
Step 1: weight percentage of each component are as follows: Zr:3wt%, O:0.25wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1000 DEG C under protection of argon gas, keeps the temperature furnace after 8h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 800 DEG C of progress pyroplastic deformations, deflection 86%, with
After be air-cooled to room temperature, obtain final shape.
Material phase analysis operating procedure is with embodiment 1, and X ray diffracting spectrum is as shown in Figure 1, determine that alloy is formed by α is single-phase.
For tensile test at room temperature operating procedure with embodiment 1, the specific data of tensile sample mechanical property are as shown in table 1, put down
Equal tensile strength is 854MPa, average yield strength 799MPa, and average elongation after fracture is 23.1%.
Tem observation: the sequin of one piece of 1.5mm thickness is cut with Wire EDM from the plate after rolling, is used
502 glue are sticked to sample seating face, then carried out on waterproof abrasive paper it is thinned, it is with acetone that glue is molten after being thinned to 100 μm or so
Sheet metal specimens are removed after change.Then the disk of diameter 30mm, is subtracted using double spray ions under being cut on sheet metal specimens using mold
Thin method obtains final test sample, and electrolytic solution is+60% methyl alcohol mixed liquor of+35% n-butanol of 5% perchloric acid.Preparation of samples
After, it is observed using the transmission electron microscope (TEM) of model JEM-1200EX, acceleration voltage is controlled in 120kV.Alloy
TEM pattern is as shown in figure 5, there is apparent nano-twin crystal structure.
SLA processing operation step is with embodiment 1, and specimen surface pattern after processing is as shown in fig. 6, surface can form SLA
The typical multistage nested type three-dimensional hole configurations of processing.
Embodiment 5
Step 1: weight percentage of each component are as follows: Zr:3wt%, O:0.30wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1100 DEG C under protection of argon gas, keeps the temperature furnace after 6h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 950 DEG C of progress pyroplastic deformations, deflection 90%, with
After be air-cooled to room temperature, obtain final shape.
Material phase analysis operating procedure is with embodiment 1, and X ray diffracting spectrum is as shown in Figure 1, determine that alloy is formed by α is single-phase.
For tensile test at room temperature operating procedure with embodiment 1, the specific data of tensile sample mechanical property are as shown in table 1, put down
Equal tensile strength is 955MPa, average yield strength 893MPa, and average elongation after fracture is 10.8%.
Metallographic observation: it is cut from the plate after hot rolling having a size of 10mm × 10mm × 1.5mm with electric spark wire cutting machine
Then small sample uses XQ-2B type pointing machine, it is embedding to add phenolic resin inlay progress hot insert inside.Successively using water-fast
Sand paper, 0# to 7# fine sandpaper carry out corase grinding and fine grinding to the sample inlayed respectively, and it is unified to be milled to scratch.Then in metallurgical polishing
It is polished on machine, chrome green aaerosol solution is added dropwise in whole process, is polished to until specimen surface do not have obvious scratch, polishing knot
It is successively cleaned and is dried up using clear water and alcohol after beam.It is molten that 50ml corrosion is prepared using nitric acid, hydrofluoric acid and distilled water
Liquid, specific volume ratio are 25:5:70, and 3-4 drop etchant solution is dripped on sample, stand 5 seconds or so and dry up.Use XJP-300
Type metallographic microscope (OM) carries out that domain is selected to shoot.Metallographic microstructure after pyroplastic deformation is as shown in fig. 7, mainly by sheet α
Mutually and etc. shaft-like α phase composition.
Embodiment 6
Step 1: weight percentage of each component are as follows: Zr:4wt%, O:0.25wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1050 DEG C under protection of argon gas, keeps the temperature furnace after 7h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 1000 DEG C of progress pyroplastic deformations, deflection 88%, with
After be air-cooled to room temperature, obtain final shape.
Material phase analysis operating procedure is with embodiment 1, and X ray diffracting spectrum is as shown in Figure 1, determine that alloy is formed by α is single-phase.
For tensile test at room temperature operating procedure with embodiment 1, the specific data of tensile sample mechanical property are as shown in table 1, put down
Equal tensile strength is 862MPa, average yield strength 723MPa, and average elongation after fracture is 19.7%.
Metallographic observation step is with embodiment 5, and the metallographic microstructure after pyroplastic deformation is as shown in figure 8, mainly by sheet α
Mutually and etc. shaft-like α phase composition.
Tem observation step is with embodiment 4, and the TEM pattern of the composition alloy is as shown in Figure 9, it can be seen that apparent nanometer
Twin structure.
Titanium alloy mechanical property described in titanium alloy described in 1 Examples 1 to 6 of table and other documents compares
The mechanical property comparison of titanium alloy described in 6 embodiments and titanium alloy described in other documents only selects to have no progeny in table 1
Elongation meets the alloy of GB/T 13810-2007 floor level (10%).
Titanium alloy described in embodiment 1 and the minimum mechanical performance index phase of TA2 described in Chinese Industrial Standards (CIS) GB/T 13810-2007
Than tensile strength improves 27.5%, and yield strength improves 62.2%, and elongation after fracture improves 20%；Titanium alloy described in embodiment 2
Compared with the Ti-14.9Zr alloy described in the United States Patent (USP) US8168012B2, tensile strength improves 35%, and yield strength improves
30.5%, elongation after fracture is suitable；Titanium alloy described in embodiment 3 and Ti-5.1Zr alloy described in United States Patent (USP) US8168012B2
It compares, tensile strength improves 21.2%, and yield strength improves 18.4%, and elongation after fracture is suitable；Titanium alloy described in embodiment 4 with
Ti-14.9Zr alloy described in United States Patent (USP) US8168012B2 is compared, and tensile strength improves 30.4%, and yield strength improves
42.9%, elongation after fracture improves 59.3%；Titanium alloy described in embodiment 5 and TC4 described in Chinese Industrial Standards (CIS) GB/T 13810-2007
The minimum mechanical performance index of alloy is compared, and tensile strength improves 3.2%, and yield strength improves 2.6%, and elongation after fracture improves
8%；Compared with the Ti-14.9Zr alloy described in the United States Patent (USP) US8168012B2 of titanium alloy described in embodiment 6, tensile strength is improved
31.6%, yield strength improves 29.3%, and elongation after fracture improves 35.9%.The intensity and plasticity of titanium alloy of the present invention have
It significantly improves, from occurring apparent nano-twin crystal structure in terms of the test result of TEM in alloy structure, makes the mechanical property of alloy
Can have and be obviously improved.
Embodiment 7
Step 1: weight percentage of each component are as follows: Zr:0.5wt%, O:0.05wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1000 DEG C under protection of argon gas, keeps the temperature furnace after 6h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 1000 DEG C of progress pyroplastic deformations, deflection 85%, with
After be air-cooled to room temperature, obtain final shape.
Embodiment 8
Step 1: weight percentage of each component are as follows: Zr:4.5wt%, O:0.4wt%, surplus Ti；
Step 2: according to composition proportion, carrying out multiple vacuum melting for raw material titanium sponge, sponge zirconium and titanium dioxide,
Obtain the uniform alloy cast ingot of ingredient；
Step 3: above-mentioned alloy cast ingot is placed in vacuum drying oven, is heated to 1100 DEG C under protection of argon gas, keeps the temperature furnace after 8h
It is cooled to room temperature, completes homogenizing annealing；
Step 4: by the alloy after above-mentioned homogenizing annealing in 1000 DEG C of progress pyroplastic deformations, deflection 90%, with
After be air-cooled to room temperature, obtain final shape.
The above is only a preferred embodiment of the present invention, it should be pointed out that: for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications are also answered
It is considered as protection scope of the present invention.
Claims (8)
1. a kind of gear division titanium alloy, which is characterized in that including following weight percent chemical component:
The wt% of Zr:0.5 wt% ~ 4.5；
The wt% of O:0.05 wt% ~ 0.4；
Surplus is Ti.
2. gear division titanium alloy according to claim 1, which is characterized in that have nanoscale in the titanium alloy structure
Twin structure.
3. a kind of preparation method of gear division titanium alloy, which comprises the following steps:
Step 1: according to composition proportion, raw material is subjected to multiple vacuum melting, obtains the uniform alloy cast ingot of ingredient；
Step 2: alloy cast ingot described in step 1 is placed in vacuum drying oven, carries out homogenizing annealing under protection of argon gas, then
Slow cooling is to room temperature；
Step 3: the alloy cast ingot after homogenizing annealing described in step 2 is subjected to thermoplastic forming and cooling in different phase regions
To room temperature, final plate is obtained.
4. the preparation method of gear division titanium alloy according to claim 3, which is characterized in that the raw material be titanium sponge,
Sponge zirconium and titanium dioxide.
5. the preparation method of gear division titanium alloy according to claim 3, which is characterized in that homogenization described in step 2
Annealing heating temperature is 1000 DEG C ~ 1100 DEG C, and soaking time is 6 ~ 8 h.
6. the preparation method of gear division titanium alloy according to claim 3 or 5, which is characterized in that cooling described in step 2
Mode is that furnace is cold.
7. the preparation method of gear division titanium alloy according to claim 3, which is characterized in that thermoplasticity described in step 3
Shaping heating temperature is 800 DEG C ~ 1000 DEG C, and deflection is 85% ~ 90%.
8. the preparation method of gear division titanium alloy according to claim 3 or 7, which is characterized in that cooling described in step 3
Mode is air-cooled.
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| CN110773686A (en) * | 2019-11-05 | 2020-02-11 | 西安西工大超晶科技发展有限责任公司 | Preparation method of TB3 titanium alloy wire for fastener |
| WO2020119074A1 (en) * | 2018-12-11 | 2020-06-18 | 南京航空航天大学 | Dental titanium alloy and preparation method therefor |
| CN112063891A (en) * | 2020-09-29 | 2020-12-11 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Zr-Cr alloy and preparation method thereof |
| CN112063893A (en) * | 2020-09-29 | 2020-12-11 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti6Al4V-Fe alloy and preparation method thereof |
| CN115948676A (en) * | 2022-12-13 | 2023-04-11 | 西安九洲生物材料有限公司 | Self-adaptive implant for bone insufficiency, titanium-zirconium-iron alloy and preparation method thereof |
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| WO2020119074A1 (en) * | 2018-12-11 | 2020-06-18 | 南京航空航天大学 | Dental titanium alloy and preparation method therefor |
| CN110773686A (en) * | 2019-11-05 | 2020-02-11 | 西安西工大超晶科技发展有限责任公司 | Preparation method of TB3 titanium alloy wire for fastener |
| CN110773686B (en) * | 2019-11-05 | 2021-12-28 | 西安西工大超晶科技发展有限责任公司 | Preparation method of TB3 titanium alloy wire for fastener |
| CN112063891A (en) * | 2020-09-29 | 2020-12-11 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Zr-Cr alloy and preparation method thereof |
| CN112063893A (en) * | 2020-09-29 | 2020-12-11 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti6Al4V-Fe alloy and preparation method thereof |
| CN115948676A (en) * | 2022-12-13 | 2023-04-11 | 西安九洲生物材料有限公司 | Self-adaptive implant for bone insufficiency, titanium-zirconium-iron alloy and preparation method thereof |
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