CN103649350A - Beta titanium alloy with low elasticity and high strength - Google Patents
Beta titanium alloy with low elasticity and high strength Download PDFInfo
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- CN103649350A CN103649350A CN201280004071.8A CN201280004071A CN103649350A CN 103649350 A CN103649350 A CN 103649350A CN 201280004071 A CN201280004071 A CN 201280004071A CN 103649350 A CN103649350 A CN 103649350A
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- C22C14/00—Alloys based on titanium
Abstract
The present invention provides a beta titanium alloy with a low modulus of elasticity and high strength compared with known alloys. According to the present invention, the titanium alloy comprises 6-13% of Mo, 0.1-3.9% of Fe, and the balance of Ti and inevitable impurities by weight, and selectively comprises 0.1-3.9% of Al. According to the present invention, the titanium alloy implements high tensile strength of 1,300 MPa or higher and a low modulus of elasticity of 95 GPa or lower at low cost.
Description
Technical field
The present invention relates to a kind of have low elastic modulus and high-intensity beta titanium alloy, more specifically, relate to and a kind ofly there is low elastic modulus and high strength and there is the high performance beta titanium alloy under low-cost.
Background technology
Titanium has high specific strength (strength/weight) and good erosion resistance, and as base material, has high suitability at each industrial circle.Therefore, titanium is called as dreamlike advanced material, and is that expection is by one of advanced metallic substance for application in future.Due to the various good natures of titanium, therefore in biological medicine, boats and ships, aviation, motion and leisure field, conduct extensive research.
Based on form the crystalline texture of the phase of metal construction in room temperature, titanium alloy is divided into α type (Patterns for Close-Packed Hexagonal Crystal: hcp), β type (body-centered cubic: bcc) and type alpha+beta conventionally.By adding the alloy of a small amount of for example industrial aluminium or titanium acquisition, it is α type.Known as high-strength alloy and be type alpha+beta for the Ti-6Al-4V alloy of aircraft, and β type is to comprise more amount for stablizing the alloy of the alloying element of β phase.
When with steel relatively time, with respect to the steel having under the state of same intensity, titanium alloy has approximately 56% density and approximately 50% shearing modulus of elasticity.Therefore, with respect to steel, the spring with identical performance can have approximately 28% theoretical weight, maybe can realize approximately 72% loss of weight.
When using Ti-3Al-8V-6Cr-4Mo-4Zr (β-C) alloy to manufacture whisker, this spring can be used for the maximum shear stress of 839MPa.In addition, helical spring weight is only helical spring 47% for what have that the use steel of identical performance manufacture, can obtain in the nature of things the effect of lightweight.
In addition, because titanium alloy has high damping capacity and natural frequency, surge (sufging) phenomenon therefore throwing into question in high engine speeds rotary course can be avoided, and can realize life-time dilatation.The natural frequency that is commonly used for the Ti-3Al-8V-6Cr-4Mo-4Zf alloy of spring is 870Hz, the natural frequency of the 483Hz of the spring that is better than being manufactured by common iron.
In addition, because the shearing modulus of elasticity of titanium alloy spring material is very little, be approximately 50% of common spring steel, so the winding number of spring can reduce.In addition, by reducing the contact height of valve spring, can promote miniaturization and the lighting of engine.In addition,, due to the various character of titanium alloy as above, when titanium alloy spring is used for to the suspension of automobile, can obtains good cushioning effect, thereby improve driving comfort.
But, when considering vehicle weight, more than should being at least 1300MPa for the tensile strength of the titanium alloy of bearing spring.For fully obtaining the effect of titanium as above, the Young's modulus of titanium alloy is preferably less than or equal to 95GPa.
Meanwhile, for manufacturing beta titanium alloy, need to comprise quite a large amount of β stabilizing elements.Because β stabilizing element is conventionally very expensive, so its use is limited to the above-mentioned special component need to good physical properties.
Although above-mentioned titanium alloy has good character, owing to using component at a low price in automobile, thereby can not substitute the common iron for the manufacture of those component with described titanium alloy yet.
Summary of the invention
Technical problem
The object of the invention is to overcome above-mentioned defect, and provide a kind of titanium alloy with low cost, described titanium alloy has good physical properties, as is more than or equal to the high tensile and the low elastic modulus that is less than or equal to 95GPa of 1300MPa.
Technical scheme
For overcoming above-mentioned defect, a kind of beta titanium alloy is provided in the present invention, described titanium alloy has low elastic modulus and high strength, the titanium that comprises 6 % by weight～13 % by weight Mo, 0.1 % by weight～3.9 % by weight Fe, surplus and inevitably impurity.This titanium alloy has the tensile strength that is more than or equal to 1300MPa and the Young's modulus that is less than or equal to 95GPa.
In addition, according to an aspect of the present invention, this titanium alloy can also comprise the Al of 0.1 % by weight～3.9 % by weight.; a kind of beta titanium alloy is provided in the present invention; described titanium alloy has low elastic modulus and high strength; the titanium that comprises 6 weight～13 % by weight Mo, 0.1 % by weight～3.9 % by weight Fe, 0.1 % by weight～3.9 % by weight Al, surplus and inevitably impurity; wherein, described titanium alloy has the tensile strength that is more than or equal to 1300MPa and the Young's modulus that is less than or equal to 95GPa.The interpolation of Al can improve processibility, formability, castibility etc., and can provide and can apply various heat treatment technicss to obtain the advantage of strengthening effect.
In addition, according to an aspect of the present invention, in titanium alloy, can additionally comprise the B of 0.005 % by weight～0.5 % by weight.
In addition, according to an aspect of the present invention, the extension per-cent of titanium alloy can be more than or equal to 6%.
In addition, according to an aspect of the present invention, the tensile strength of titanium alloy can be more than or equal to 1400MPa.
In addition, according to an aspect of the present invention, the microstructure of titanium alloy can comprise the ω phase particle being dispersed in imperceptibly in β matrix.ω mutually can be by using heat treatment technics to remove or generate, to obtain desirable strength, ductility and Young's modulus.
Advantageous effects
Titanium alloy according to the present invention has the tensile strength that is more than or equal to 1300MPa and the Young's modulus that is less than or equal to 95GPa, and can be applied to various low elastic modulus and the high-intensity fields of needing.
In addition, due to according to the present invention, the use of noble alloy element in titanium alloy is minimized, so the manufacturing cost of alloy can significantly reduce.
In addition, when manufacturing titanium alloy by forging and rolling, can manufacture tensile strength and be more than or equal to 1300MPa, Young's modulus and be less than or equal to 95GPa and extend per-cent and be more than or equal to approximately 6% bar, rectangle square bar and sheet material, and without carrying out as solution thermal treatment or the thermal treatment such as aging.Therefore, can transport the component in automobile-use spring and various field with high strength and low elastic modulus with low cost fabrication.Particularly, when titanium alloy is used for to spring material, compares and can realize weight saving to 50%～60% with the spring that uses steel manufacture.
Accompanying drawing explanation
Fig. 1～5th, about the microstructural photo of the forge hot material manufactured in embodiments of the invention 1～5 respectively, it is taken by opticmicroscope.
Fig. 6 and 7 is microstructural photos of the rolled bar material about manufacturing in embodiments of the invention 2 and 3, and it is taken by opticmicroscope.
Fig. 8 and 9 is microstructural photos of the rolled bar material about manufacturing in embodiment 2 and 3 respectively, and it is taken by dark-field image (DFI) transmission electron microscope.
Embodiment
To describe the preferred embodiment of the present invention in detail below, but the present invention is not limited to following embodiment.
First, according to the compositing range of each element in beta titanium alloy of the present invention, limit as follows.
Mo:6 % by weight～13 % by weight
Mo is the stabilizing element of β phase, and has the Young's modulus of reduction and propose high-intensity effect.Because Mo is expensive, so the amount of Mo is optimised, to reduce costs when obtaining mechanical properties.The preferred amounts of Mo is 6 % by weight～13 % by weight.
Fe:0.1 % by weight～3.9 % by weight
Fe is the stabilizing element of β phase, but can improve deformation resistance.Therefore be, all to add as few as possible Fe in the prior art.In the present invention, compare with other β stabilizing elements, used relatively a large amount of cheap Fe.When the amount of Fe is less than 0.1 % by weight, β static stabilization is insufficient, and when the amount of Fe surpasses 3.9 % by weight, thereby deformation resistance can excessively make processibility deteriorated.Therefore, the preferred amounts of Fe is less than or equal to 3.9 % by weight.
Meanwhile, by stablizing β phase, there is the Mo equivalent explanation that the create index of the beta titanium alloy of low elastic modulus can be in [equation 1].While calculating with Fe, preferred Mo equivalent is approximately 7.0～20.0.
[equation 1]
Mo equivalent=[Mo]+1/5[Ta]+1/3.6[Nb]+1/2.5[W]+1/1.5[V]+1.25[Cr]+1.25[Ni]+1.7[Mn]+1.7[Co]+2.5[Fe]
Al:0.1 % by weight～3.9 % by weight
Al adds to improve according to the element of the intensity of beta titanium alloy of the present invention.Al has suppressed the deposition of ω phase, and this has improved the hardness of titanium alloy in heat treatment process by embrittlement, improved intensity and ductility, and has improved processibility and castibility.Al is alternative in the present invention adds.When the amount of Al surpasses 3.9 % by weight, hardness can excessively be improved, and unit elongation can reduce, thereby reduces processibility.Therefore, the amount of the Al of interpolation is preferably less than or equal to 3.9 % by weight.
B:0.005 % by weight～0.5 % by weight
B is the element that suppresses huge consolidated structure growth when carrying out solution-cast.When interpolation is less than the B of 0.005 % by weight, the enlarged meeting of consolidated structure can not get effective inhibition.When the amount of B surpasses 0.5 % by weight, the further miniaturization of cast structure will can not be realized.Therefore, the preferred amounts of B is 0.005 % by weight～0.5wt%.
Inevitable impurity
Inevitably impurity is for may not inadvertently making an addition in the raw material of titanium alloy or the composition not inadvertently adding in the course of processing.Particularly, oxygen can make the deformability of titanium alloy deteriorated, can become the reason cracking in cold working process, and can become the reason that improves deformation resistance.Therefore, inevitably the amount of impurity need to remain and be less than or equal to 0.3 % by weight, and preferably need to be less than or equal to 0.18 % by weight.In addition, due to hydrogen make the ductility of titanium alloy and toughness deteriorated, so the amount of hydrogen is preferably the least possible.The amount of oxygen is more preferably less than or equals 0.03 % by weight, and is most preferably less than or equal to 0.01 % by weight.Carbon can reduce the deformability of titanium alloy significantly, therefore need to be contained in wherein with the least possible amount.Preferably, the amount of carbon is less than or equal to 0.05 % by weight, and more preferably, the amount of carbon is less than or equals 0.01 % by weight.In addition, nitrogen also can reduce the deformability of titanium alloy significantly, therefore need to be contained in wherein with the least possible amount.Preferably, the amount of nitrogen is less than or equal to 0.02 % by weight, and more preferably, the amount of nitrogen is less than or equals 0.01 % by weight.
In addition, according in the microstructure of titanium alloy of the present invention, α can be sneaked in β phase matrix mutually, and the ω phase particle of fine dispersion can be included in β phase matrix.
By using according to the method for titanium alloy processing bar, rectangle square bar and sheet material of the present invention, comprise: the titanium alloy liquid metal that (a) preparation comprises mentioned component; (b) titanium alloy that casting is prepared is thus to manufacture ingot casting; (c) at 800 ℃～1200 ℃ forge hot ingot castings; (d) at 25 ℃～650 ℃ titanium alloys that rolling is forged.
The temperature of forge hot and rolling preferably remains in the scope of above restriction, to prevent from cracking and obtaining sufficient rate of compression in the course of processing.
[embodiment]
By use sense, answer skull melting (ISM) manufacture to there is the titanium alloy of composition as shown in Table 1 below.In all alloys as the amount of the impurity such as oxygen (O), nitrogen (N), carbon (C) and hydrogen (H) is less than 0.5 % by weight.
Table 1
The liquid metal of alloy with the melting of the composition shown in upper table 1 is cast as to ingot casting, and this ingot casting is of a size of 100mm diameter * 90mm height.
For selection in the alloy shown in table 1 has the alloy of the abundant mechanical properties of the suspension that can be used for conveyor motor-car, the present inventor is at 1100 ℃ of heating ingot castings.Then, ingot casting is inserted in warm forming machine, and forge hot is to manufacture the target material of long 120mm, wide 60mm and high 40mm.
Evaluate the tensile property of the target material of forge hot thus, result is presented in following table 2.
[table 2]
| Alloy | Yield strength (Mpa) | Tensile strength (Mpa) | Extend per-cent (%) |
| Embodiment 1 | 1198 | 1204 | 10 |
| Embodiment 2 | 769 | 887 | 8.5 |
| Embodiment 3 | 772 | 895 | 17 |
| Embodiment 4 | 809 | 934 | 8.0 |
| Embodiment 5 | 655 | 806 | 16 |
| Embodiment 1 | 896 | 898 | 18 |
| Comparative example 2 | 1088 | 1192 | 5.4 |
| Comparative example 3 | 780 | 916 | 10 |
* comparative example 1 is corresponding to the tensile property of common material.
* comparative example 2 and 3 is corresponding to by the tensile properties that use the sample make with bar shape silks to record.
Evaluation result as shown in Figure 2 can confirm, has over the tensile strength of 1200MPa and 10% extension per-cent at the most, and shown the character very approaching with target physical character of the present invention according to the alloy of embodiments of the invention 1.Therefore, the alloy in confirmation embodiment 1 can be realized object of the present invention by additional process.
In addition, although the alloy in embodiment 2～5 has the tensile strength that is less than 1000MPa, unit elongation per-cent, and Young's modulus is less than 95GPa.Therefore, by subsequent handling, can additionally improve intensity, and the alloy in embodiment 2～5 can be applied as the mechanical suspension spring of transmission.
For confirming, the alloy in the alloy in embodiment 2 and embodiment 3 is selected from respectively embodiment 2 and 5 and embodiment 3 and 4, and they have respectively similar Mo and Fe content.Then, carry out subsequent handling, and measure tensile property and elastic property.
On the other hand, after completing subsequent handling, comparative example 1,2 and 3 alloy can be bar states, or may have too low tensile property or too high Young's modulus.Therefore, these alloys extremely difficulty be used as spring.
Tensile property based on room temperature, forges according to the firm material standed for of the titanium alloy of embodiment 1,2 and 3, and take titanium alloy manufacture is rectangle square bar or bar.Then, titanium alloy is heated to 600 ℃, and by 3 rollings, take manufacture diameter as 16mm～20mm and length the bar more than 500mm.
From the central position sampling of the bar manufactured thus, and evaluate the character of this sample.
First, by using the microstructure of the bar of opticmicroscope and tem study rolling.By standard metal preparation technology for the preparation of the sample of analyzing by opticmicroscope.First, mirror polish sample, and use etching solution to its etching.
In addition, by sample is ground to, 60 μ m are thick to be come for the preparation of by the sample of tem study, and under the condition of 60V, in the solution that comprises 35% butanols-6% perchloric acid-methyl alcohol, carries out dual-jet polishing.
Fig. 1～5th, the ingot casting of manufacturing for the alloy by forge hot with the composition shown in embodiment 1～5, the microstructural photo of the forge hot material of taking by opticmicroscope.As shown in Fig. 1～5, the microstructure of all alloys all has β phase matrix, described β phase matrix by mean sizes be approximately hundreds of microns etc. axle construction form.In addition, a part of α deposits mutually and exists in microstructure.
For by opticmicroscope, the microstructure of rolled bar material being observed the photo in the Fig. 6 and 7 obtaining, the crystal grain obviously differentiating in the microstructure of forge hot material is carrying out disappearing after follow-up rolling process.In addition, observe microstructure and carrying out thering is waveform shape after serious viscous deformation.Meanwhile, the microstructure of using transmission electron microscope to observe by DFI has the fine ω phase being present in some regions according to observations, and described ω has several nanometers mutually to the size of tens nanometer.
Then, measure according to the tensile property and the Young's modulus that occupy the bar of inventive embodiment and comparative example manufacture, and be presented in following table 3.
[table 3]
As confirmed in table 3, alloy bar material has higher than the tensile strength of 1300MPa with lower than the Young's modulus of 95GPa according to an embodiment of the invention.Therefore, these bars meet and are comprising the required physical properties of component in the various fields such as spring material with low elastic modulus and high repulsion for suspension of conveyor motor-car.
Particularly, according to the alloy bar material of embodiment 2, there is the high tensile of 1501MPa, approximately 10% the good workability of extension per-cent and the low elastic modulus of 85GPa.Therefore, this alloy bar can suitably be used as spring material, as the spring material of automobile-use suspension.
According to the alloy bar material of embodiment 3, also there is the high tensile of 1498MPa, approximately 7% extension per-cent and the Young's modulus of 76GPa, and go for the component that need high strength and low elasticity character in each field.
In addition, alloy bar material according to the present invention is used cheap titanium (Fe) as β stabilizing element, and has confirmed to obtain and to compare good mechanical properties with common material Ti-15Mo with low cost.Therefore, compare with common alloy of titanium, the manufacturing cost of described titanium alloy can be reduced, and compares with common alloy of titanium, can obtain good tensile property and good elasticity character.
Claims (10)
1. a beta titanium alloy, described titanium alloy has low elastic modulus and high strength, and the Mo that comprises 6 % by weight～13 % by weight, 0.1 Fe of % by weight～3.9 % by weight be, the Ti of surplus and inevitably impurity,
Described titanium alloy has the tensile strength that is more than or equal to 1300MPa and the Young's modulus that is less than or equal to 95GPa.
2. titanium alloy as claimed in claim 1, described titanium alloy also comprises the Al of 0.1 % by weight～3.9 % by weight.
3. titanium alloy as claimed in claim 1, wherein, the microstructure of described beta titanium alloy has the shape that median size is the dispersion of the ω phase below 100nm.
4. titanium alloy as claimed in claim 1, wherein, is 7.0～20.0 by the Mo equivalent that [equation 1] defines below,
[equation 1]
Mo equivalent=[Mo]+1/5[Ta]+1/3.6[Nb]+1/2.5[W]+1/1.5[V]+1.25[Cr]+1.25[Ni]+1.7[Mn]+1.7[Co]+2.5[Fe].
5. the titanium alloy as described in any one in claim 1～4, wherein, the extension per-cent of described titanium alloy is more than or equal to 6%.
6. the titanium alloy as described in any one in claim 1～4, wherein, the tensile strength of described titanium alloy is more than or equal to 1400MPa.
7. a bar, described bar is by being used the titanium alloy as described in any one in claim 1～4 to manufacture.
8. a sheet material, described sheet material is by being used the titanium alloy as described in any one in claim 1～4 to manufacture.
9. a rectangle square bar, described rectangle square bar is by being used the titanium alloy as described in any one in claim 1～4 to manufacture.
10. a spring material, described spring material is by being used the titanium alloy as described in any one in claim 1～4 to manufacture.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020120057217A KR101418775B1 (en) | 2012-05-30 | 2012-05-30 | Beta type titanium alloy with low elastic modulus and high strength |
| KR10-2012-0057217 | 2012-05-30 | ||
| PCT/KR2012/006941 WO2013180338A1 (en) | 2012-05-30 | 2012-08-30 | Beta titanium alloy with low elasticity and high strength |
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| CN103649350A true CN103649350A (en) | 2014-03-19 |
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| CN201280004071.8A Pending CN103649350A (en) | 2012-05-30 | 2012-08-30 | Beta titanium alloy with low elasticity and high strength |
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|---|---|
| US (1) | US20150147225A1 (en) |
| KR (1) | KR101418775B1 (en) |
| CN (1) | CN103649350A (en) |
| WO (1) | WO2013180338A1 (en) |
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| CN104611611A (en) * | 2015-01-22 | 2015-05-13 | 北京科技大学 | Preparation method for ultralow-elastic-modulus high-strength titanium alloy material |
| CN105400990A (en) * | 2015-07-30 | 2016-03-16 | 贵州大学 | Low-modulus and high-strength biomedical titanium alloy and preparation method thereof |
| CN106435265A (en) * | 2016-09-14 | 2017-02-22 | 沈阳泰恒通用技术有限公司 | High-strength Ti alloy for springs for rail transit |
| 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 |
| CN110157949A (en) * | 2019-07-10 | 2019-08-23 | 山东建筑大学 | A kind of method of the channel pressings such as universal circle preparation nanometer beta-titanium alloy |
| CN114836650A (en) * | 2022-04-27 | 2022-08-02 | 北京航空航天大学 | Titanium alloy with complete equiaxed crystal structure and ultrahigh yield strength |
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| KR20240056276A (en) * | 2022-10-21 | 2024-04-30 | 국립순천대학교산학협력단 | Titanium alloy and manufacturing method for same |
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| CN104611611B (en) * | 2015-01-22 | 2016-12-07 | 北京科技大学 | A kind of preparation method of ultralow elasticity modulus high strength titanium alloy material |
| CN105400990A (en) * | 2015-07-30 | 2016-03-16 | 贵州大学 | Low-modulus and high-strength biomedical titanium alloy and preparation method thereof |
| CN105400990B (en) * | 2015-07-30 | 2017-10-31 | 贵州大学 | A kind of low modulus high strength biological medical titanium alloy and preparation method thereof |
| CN106435265A (en) * | 2016-09-14 | 2017-02-22 | 沈阳泰恒通用技术有限公司 | High-strength Ti alloy for springs for rail transit |
| 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 |
| CN110157949A (en) * | 2019-07-10 | 2019-08-23 | 山东建筑大学 | A kind of method of the channel pressings such as universal circle preparation nanometer beta-titanium alloy |
| CN114836650A (en) * | 2022-04-27 | 2022-08-02 | 北京航空航天大学 | Titanium alloy with complete equiaxed crystal structure and ultrahigh yield strength |
| CN114990382A (en) * | 2022-05-26 | 2022-09-02 | 西北工业大学 | Metastable beta titanium alloy with ultralow-gap phase-change induced plasticity and preparation method thereof |
| CN114990382B (en) * | 2022-05-26 | 2024-01-30 | 西北工业大学 | Ultra-low-gap phase transition induced plasticity metastable beta titanium alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20130134014A (en) | 2013-12-10 |
| WO2013180338A1 (en) | 2013-12-05 |
| US20150147225A1 (en) | 2015-05-28 |
| KR101418775B1 (en) | 2014-07-21 |
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