CN101935776A - Beta titanium alloy material and preparation method thereof - Google Patents
Beta titanium alloy material and preparation method thereof Download PDFInfo
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Abstract
The invention provides a beta titanium alloy material, consisting of the following components in percentage by mass: 83.0 to 88.0 percent of Ti, 8.0 to 13.0 percent of Cr, 0.5 to 1.5 percent of Fe, 2.0 to 4.0 percent of Al, and other trace impurities. The preparation method comprises the following steps: preparing the raw materials according to the mass percentage required by the beta titanium alloy material; smelting the mixture in a vacuum induction furnace with the vacuum degree of between 0 and 5Pa and the smelting power of 200KW after uniform mixing; cutting and removing the sink hole part of an ingot after smelting; and forging the ingot at the temperature which is higher than beta-phase change temperature and lower than 1,000 DEG C. The titanium alloy has the advantages of lower cost, higher strength, higher elongation rate and higher impact toughness; after solid solution treatment, the whole the alloy is a metastable beta-phase tissue, the alloy has excellent cold and heat processing performance, and the cold working rate achieves 87.2 percent.
Description
Technical field
The present invention relates to a kind of titanium alloy material technology, particularly a kind of beta titanium alloy material and preparation method thereof.
Background technology
In the titanium alloy system, beta-titanium alloy has the highest specific tenacity and good cold-forming property.Beta-titanium alloy is applied as purpose with the aviation military project the earliest, and present industrial beta-titanium alloy more and more widely is applied to civil area, as chemical industry, medical treatment, sports equipment etc.In existing beta-titanium alloy, all need the beta stable element of heavy addition costliness such as V, Mo, Nb, Ta etc., for example, Ti-10V-2Fe-3Al, Ti-15V-3Al-3Cr-3Sn, Ti-3Al-8V-6Cr-4Mo-4Sn, Ti-13V-11Cr-3Al, Ti-15Mo-5Zr-3Al, Ti-29Nb-13Ta-4.6Zr etc.
For example: Ti1023 (Ti-10V-2Fe-3Al) alloy is that U.S. Timet company succeeded in developing in 1971, is a kind of high tough nearly beta-titanium alloy that is most widely used up to now, and domestic trade mark TB6 sees GB GB/T 3620.1-2007.Alloy after heat treatment its tensile strength is 965～1310MPa, K
ICBe 99～33MPam
1/2Though this material belongs to the high strength beta-titanium alloy, but this material V element costs an arm and a leg, and content is very high, make the cost of this alloy very high, limited the application of beta-titanium alloy greatly, now be mainly used in aerospace field, as being applied to Boeing 777 passenger plane landing gear girders, the passenger capacity that European Air Passenger company makes reaches the main unit of landing gear of the above passenger plane A380 the biggest in the world of 500 people.
The cost of beta-titanium alloy alloy is very high, has limited the application of beta-titanium alloy greatly.Timetal62S (Ti-6Al-2Fe-0.1Si) is the low-cost alloy that designs at Ti-6Al-4V, replaced V fully with Fe, performance but is better than Ti-6Al-4V, has added a spot of Si in the alloy and has improved anti-oxidant and creep-resistant property, and the yield strength under its as-annealed condition reaches 896～965MPa.This material belongs to the alpha+beta low-cost titanium alloy, but this material cold deformation rate variance is not suitable for cold-formed.
In order to utilize the performance of beta-titanium alloy excellence, beta-titanium alloy is used widely, need development to contain or do not contain the beta-titanium alloy of expensive alloy element less.It is that TFC alloy alloy and Ti-4.3Fe-7.1Cr-3.0Al are TFCA alloy alloy that the people such as B.Gunawarman of Japan have studied Ti-4.3Fe-7.1Cr, beta stable element in this alloy uses cheap Fe and Cr, alloy is the β phase all after the β phase region quenches, and has good cold-forming property.The cold rolling working modulus of Ti-4.3Fe-7.1Cr-3.0Al (TFCA alloy) can reach 90%, and alloy can have good obdurability coupling by mechanical thermal treatment simultaneously.But this material Fe has very big segregation tendency, and macrosegregation makes macrostructure that bigger variation be arranged, thereby has increased the dispersiveness of mechanical properties data greatly, and macrosegregation also can not be removed through Overheating Treatment or plastic working.And both at home and abroad such as beta titanium alloy materials such as Ti-4.3Fe-7.1Cr in preparation process, about adopting the three three rarely seen reports of forging process that crystal grain thinning such as pull out of upsetting.
Summary of the invention
Technical problem to be solved by this invention provides a kind of beta titanium alloy material and preparation method thereof, adopt cheap eutectoid type beta stable element Fe, Cr etc. to replace expensive isomorphism beta stable element such as Mo, V, Nb etc., the raw materials cost that reduces beta-titanium alloy makes it suitable with pure titanium, and simultaneously alloy keeps high strength and heat, excellent cold-workability exhibiting.
The beta titanium alloy material that the technical problem that the present invention further solves provides is to be that matrix adds cheap Cr, Fe, Al alloying element with the titanium, make the raw materials cost of beta-titanium alloy be reduced to the scope of titanium sponge, alloy has excellent processing characteristics again simultaneously, can produce low cost, high-intensity titanium-alloy thin-plate, with the range of application of further expansion titanium alloy.
For the purpose that realizes solving the problems of the technologies described above, the present invention has adopted following technical scheme:
A kind of beta titanium alloy material of the present invention, its mass percent consist of Ti:83.0～88.0%, Cr:8.0～13.0%, Fe:0.5～1.5%, Al:2.0～4.0%, and the impurity of other traces.
Beta titanium alloy material of the present invention, its preferred mass percent consists of Ti:86.0～87.5%, Cr:8.0～10.0%, Fe:1.0～1.5%, Al:3.0%.
Titanium alloy material of the present invention can be that matrix adds pure Cr, pure Fe, pure Al with the sponge Ti, constitutes thereby reach above-mentioned mass percent.Certainly, also can access other distributions of the mass ratio of requirement, for example, use and contain the alloy of some or all of composition among the Ti-Cr-Fe-Al as raw material according to other.
Beta titanium alloy material preparation method of the present invention is: raw material is prepared through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing by the mass percent of beta titanium alloy material requirement, the shrinkage cavity part is removed in the ingot casting warp cutting of refining back, is forging below 1000 ℃ more than the β transformation temperature then.
Described preparation method, its concrete forging method is:
(1), first fire forges: more than the β transformation temperature below 1000 ℃, ingot blank forged to L/D ratio be about 1.5～2, upset through commutation three then and three pull out, the forging ratio of each jumping-up and pulling is 1.5～2;
(2), second fire forges: more than the β transformation temperature below 1000 ℃, forging stock three is upset and three pulled out through commutating, the forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size;
(3), forge finish the back more than the β transformation temperature 50 ℃ carry out solution treatment, the time of solution treatment is definite according to following formula:
t＝(2～3)D+(5～8)min
D represents net thickness in the formula, and unit is a millimeter; The unit of t is minute; Described net thickness is meant the conventional net thickness notion of thermal treatment process, and sheet material can directly be thought the thickness of plate, and irregular sample is approximate thinks mean thickness;
(4) shrend under the rapid room temperature after the solid solution obtains material requested.
Owing to adopted technical scheme as mentioned above, the present invention has following superiority:
1, Ti-10Cr-1Fe-3Al titanium alloy of the present invention has very low cost, higher intensity, unit elongation, impelling strength.
2, Ti-10Cr-1Fe-3Al titanium alloy of the present invention all is metastable β phase constitution after carrying out solution treatment, and alloy has excellent cold and hot working performance, and cold working rate can reach 87.2%.The mechanical performance index of this beta-titanium alloy is:
1) alloy property: yield strength 〉=883MPa behind 900 ℃ of solid solution 40min, tensile strength 〉=916MPa, unit elongation 〉=9.0%, relative reduction in area 〉=25.2%, impelling strength 〉=16.9J/cm
2
2) have excellent heat, cold-forming property, can make the high-strength titanium alloy thin plate.
Description of drawings
Fig. 1 and Fig. 2 are the cold rolling back of a kind of Ti-10Cr-1Fe-3Al alloy photos.
Fig. 1 is the middle part of cold rolling back plate, and Fig. 2 is the end.
As depicted in figs. 1 and 2, the 5mm slab after 900 ℃ of solution treatment of Ti-10Cr-1Fe-3Al alloy carries out cold rolling, does not carry out process annealing between passage, does not occur crackle when being rolled to 0.64mm through 37 passages yet, and this moment, working modulus reached 87.2%.Generally about 20%, the cold working rate of Ti-10Cr-1Fe-3Al alloy is considerably beyond the TC4 alloy without the cold rolling working modulus of process annealing for the TC4 alloy.
Fig. 3 is Ti-10Cr-1Fe-3Al alloy true stress and true strain curve.
As seen from Figure 3 the Ti-10Cr-1Fe-3Al alloy when compression stress approximately is stabilized in 1000MPa, be stead deformation, and do not rupture during 0.5 the strain that reaches that machine sets.
Embodiment
Embodiment 1
With sponge Ti, pure Cr, pure Fe, pure Al, Ti:87.5%, Cr:8%, Fe:1.5%, Al:3.0% preparation by weight percentage, through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing.Chemical ingredients measured result after the melting is as shown in table 1:
Table 1 ingot casting chemical ingredients
The shrinkage cavity part is removed in the cutting of ingot casting warp after the melting, forges according to following technology then.
(1) first fire forges: Φ 110mm * 50mm radially breaks into Φ 70mm * L, pulls out through three rammers three that commutate then and is swaged into Φ 70mm * 120mm.The forging ratio of each jumping-up and pulling is 1.5～2.
Initial forging temperature: 1000 ℃, charging temperature: 1000 ℃, heat-up time: 50min final forging temperature: 850 ℃
(2) second fire forge: pull out through three rammers three that commutate and be swaged into Φ 32mm * 550mm.The forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size.
Initial forging temperature: 950 ℃, charging temperature: 950 ℃, heat-up time: 40min final forging temperature: 850 ℃
Thermal treatment process:
Forge the back in 900 ℃ of solid solution 40min rapid shrend of coming out of the stove.
Mechanical property after the solution treatment: yield strength 883MPa, tensile strength 916MPa, unit elongation 9.0%, relative reduction in area 25.2%, impelling strength 16.9J/cm
2
Embodiment 2
With sponge Ti, pure Cr, pure Fe, pure Al, Ti:85.5% by weight percentage; Cr:10%; Fe:0.5%; The Al:4% preparation is through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing.Chemical ingredients after the melting is as shown in table 2:
Table 2 ingot casting chemical ingredients
The shrinkage cavity part is removed in the cutting of ingot casting warp after the melting, forges according to following technology then.
(1) first fire forges: Φ 110mm * 50mm radially breaks into Φ 70mm * L, pulls out through three rammers three that commutate then and is swaged into Φ 70mm * 120mm.The forging ratio of each jumping-up and pulling is 1.5～2.
Initial forging temperature: 1000 ℃, charging temperature: 1000 ℃, heat-up time: 50min final forging temperature: 850 ℃
(2) second fire forge: pull out through three rammers three that commutate and be swaged into Φ 32mm * 550mm.The forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size.
Initial forging temperature: 950 ℃, charging temperature: 950 ℃, heat-up time: 40min final forging temperature: 850 ℃
Thermal treatment process:
Forge the back in 900 ℃ of solid solution 40min rapid shrend of coming out of the stove.
Mechanical property after the solution treatment: yield strength 969MPa, tensile strength 981MPa, unit elongation 13.8%, relative reduction in area 38.7%, impelling strength 29.7J/cm
2
Embodiment 3
With sponge Ti, pure Cr, pure Fe, pure Al, Ti:84% by weight percentage; Cr:13%; Fe:1%; The Al:2% preparation is through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing.Chemical ingredients after the melting is as shown in table 3:
Table 3 ingot casting chemical ingredients
The shrinkage cavity part is removed in the cutting of ingot casting warp after the melting, forges according to following technology then.
(1) first fire forges: Φ 110mm * 50mm radially breaks into Φ 70mm * L, pulls out through three rammers three that commutate then and is swaged into Φ 70mm * 120mm.The forging ratio of each jumping-up and pulling is 1.5～2.
Initial forging temperature: 1000 ℃, charging temperature: 1000 ℃, heat-up time: 50min final forging temperature: 850 ℃
(2) second fire forge: Φ 70mm * 120mm ingot blank pulls out through three rammers three that commutate and is swaged into Φ 31mm * 550mm.The forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size.
Initial forging temperature: 950 ℃, charging temperature: 950 ℃, heat-up time: 40min final forging temperature: 850 ℃
Thermal treatment process:
Forge the back in 900 ℃ of solid solution 40min rapid shrend of coming out of the stove.
Mechanical property after the solution treatment: yield strength 979MPa, tensile strength 988MPa, unit elongation 15.9%, relative reduction in area 43.1%, impelling strength 36.2J/cm
2
Embodiment 4:
With sponge Ti, pure Cr, pure Fe, pure Al, Ti:86% by weight percentage; Cr:10%; Fe:1%; The Al:3% preparation is through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing.Chemical ingredients after the melting is as shown in table 4:
Table 4 ingot casting chemical ingredients
The shrinkage cavity part is removed in the cutting of ingot casting warp after the melting, forges according to following technology then.
(1) first fire forges: Φ 110mm * 50mm radially breaks into Φ 70mm * L, pulls out through three rammers three that commutate then and is swaged into Φ 70mm * 120mm.The forging ratio of each jumping-up and pulling is 1.5～2.
Initial forging temperature: 1000 ℃, charging temperature: 1000 ℃, heat-up time: 50min final forging temperature: 850 ℃
(2) second fire forge: Φ 70mm * 120mm pulls out blank and is swaged into Φ 32mm * 550mm through three rammers three that commutate.The forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size.
Initial forging temperature: 950 ℃, charging temperature: 950 ℃, heat-up time: 40min final forging temperature: 850 ℃
Thermal treatment process:
Forge the back in 900 ℃ of solid solution 40min rapid shrend of coming out of the stove.
With molten processing back mechanical property: yield strength 957MPa, tensile strength 973MPa, unit elongation 11.8%, relative reduction in area 31.2%, impelling strength 18.3J/cm
2
Ti-10Cr-1Fe-3Al alloy slab after 900 ℃ of solution treatment carries out cold rolling, does not do process annealing between rolling pass.Slab is of a size of 5mm * 100mm * 100mm.
Table 5 has provided the cold rolling reduction system of Ti-10Cr-1Fe-3Al alloy.
As shown in Table, crackle does not appear in blank yet when being rolled to 0.64mm through 37 passages, and this moment, working modulus reached 87.2%.Crackle appears in the slab edge part after being rolled to 0.60mm from 0.64mm.Roll back 0.60mm plate as shown in Figure 1.
The cold rolling reduction system of table 5Ti-10Cr-1Fe-3Al alloy
Claims (4)
1. beta titanium alloy material, it is characterized in that: the mass percent of titanium alloy material consists of Ti:83.0～88.0%, Cr:8.0～13.0%, Fe:0.5～1.5%, Al:2.0～4.0%, and other micro-impurity.
2. according to the described beta titanium alloy material of claim 1, it is characterized in that: described titanium alloy material mass percent consists of: Ti:86.0～87.5%, Cr:8.0～10.0%, Fe:1.0～1.5%, Al:3.0%.
3. described beta titanium alloy material preparation method of claim 1, it is characterized in that: raw material is prepared through melting under vacuum induction furnace vacuum tightness 0-5Pa, melting power 200KW behind the uniform mixing by the mass percent of beta titanium alloy material requirement, the shrinkage cavity part is removed in the ingot casting warp cutting of refining back, is forging below 1000 ℃ more than the β transformation temperature then.
4. according to the described preparation method of claim 3, it is characterized in that: the concrete technical scheme of described forging method is:
(1), first fire forges: more than the β transformation temperature below 1000 ℃, ingot blank forged to L/D ratio be about 1.5～2, upset through commutation three then and three pull out, the forging ratio of each jumping-up and pulling is 1.5～2;
(2), second fire forges: more than the β transformation temperature below 1000 ℃, forging stock three is upset and three pulled out through commutating, the forging ratio of each jumping-up and pulling is 1.5～2, continues then ingot blank is forged to target size;
(3), forge finish the back more than the β transformation temperature 50 ℃ carry out solution treatment, the time of solution treatment is definite according to following formula:
t＝(2～3)D+(5～8)min
D represents net thickness in the formula, and unit is a millimeter; The unit of t is minute;
(4) shrend under the rapid room temperature after the solid solution obtains material requested.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103495834A (en) * | 2013-09-12 | 2014-01-08 | 宝鸡鑫诺新金属材料有限公司 | Method for manufacturing medical TC20 titanium alloy plates for surgical implants |
| CN104726746A (en) * | 2015-04-17 | 2015-06-24 | 西北有色金属研究院 | High-strength metastable beta-type titanium alloy bar and production method thereof |
| CN104762526A (en) * | 2015-03-26 | 2015-07-08 | 河北工程大学 | Low-cost and high-strength Ti-Zr-Al-F2 alloy |
| CN104959506A (en) * | 2015-05-21 | 2015-10-07 | 西部超导材料科技股份有限公司 | Preparation method of hard-deformation non-burning titanium alloy boards |
| CN105328112A (en) * | 2015-11-14 | 2016-02-17 | 沈阳黎明航空发动机(集团)有限责任公司 | Forming method of large-concentration-ratio upset forging components made of titanium alloy |
| CN108486410A (en) * | 2018-05-24 | 2018-09-04 | 北京航空航天大学 | A kind of superelevation strength and ductility product low-cost titanium alloy and the preparation method and application thereof |
| CN109930100A (en) * | 2019-03-29 | 2019-06-25 | 中国科学院金属研究所 | A kind of damage tolerance titanium alloy plate rolling and mating heat treatment process |
| RU2701779C2 (en) * | 2014-10-31 | 2019-10-01 | Сафран Эркрафт Энджинз | Gas turbine engine part containing titanium-based alloy |
| CN111375715A (en) * | 2018-12-29 | 2020-07-07 | 宝武特种冶金有限公司 | Method for improving yield of TC17 titanium alloy bar |
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| CN103495834A (en) * | 2013-09-12 | 2014-01-08 | 宝鸡鑫诺新金属材料有限公司 | Method for manufacturing medical TC20 titanium alloy plates for surgical implants |
| CN103495834B (en) * | 2013-09-12 | 2016-08-17 | 宝鸡鑫诺新金属材料有限公司 | The preparation method of surgical implant medical TC20 titanium alloy plate |
| RU2701779C2 (en) * | 2014-10-31 | 2019-10-01 | Сафран Эркрафт Энджинз | Gas turbine engine part containing titanium-based alloy |
| CN104762526A (en) * | 2015-03-26 | 2015-07-08 | 河北工程大学 | Low-cost and high-strength Ti-Zr-Al-F2 alloy |
| CN104726746A (en) * | 2015-04-17 | 2015-06-24 | 西北有色金属研究院 | High-strength metastable beta-type titanium alloy bar and production method thereof |
| CN104726746B (en) * | 2015-04-17 | 2017-01-18 | 西北有色金属研究院 | High-strength metastable beta-type titanium alloy bar and production method thereof |
| CN104959506A (en) * | 2015-05-21 | 2015-10-07 | 西部超导材料科技股份有限公司 | Preparation method of hard-deformation non-burning titanium alloy boards |
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| CN105328112B (en) * | 2015-11-14 | 2018-07-13 | 沈阳黎明航空发动机(集团)有限责任公司 | A kind of big manufacturing process assembled than titanium alloy upset part |
| CN108486410A (en) * | 2018-05-24 | 2018-09-04 | 北京航空航天大学 | A kind of superelevation strength and ductility product low-cost titanium alloy and the preparation method and application thereof |
| CN111375715A (en) * | 2018-12-29 | 2020-07-07 | 宝武特种冶金有限公司 | Method for improving yield of TC17 titanium alloy bar |
| CN109930100A (en) * | 2019-03-29 | 2019-06-25 | 中国科学院金属研究所 | A kind of damage tolerance titanium alloy plate rolling and mating heat treatment process |
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