CN115627385A - Ti-Sn-based alloy with high damping and excellent mechanical property and preparation method and application thereof - Google Patents
Ti-Sn-based alloy with high damping and excellent mechanical property and preparation method and application thereof Download PDFInfo
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- CN115627385A CN115627385A CN202211300448.6A CN202211300448A CN115627385A CN 115627385 A CN115627385 A CN 115627385A CN 202211300448 A CN202211300448 A CN 202211300448A CN 115627385 A CN115627385 A CN 115627385A
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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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- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/04—Influencing the temperature of the metal, e.g. by heating or cooling the mould
- B22D27/045—Directionally solidified castings
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C13/00—Alloys based on tin
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Abstract
The invention belongs to the technical field of Ti-Sn-based alloy preparation, and particularly relates to a Ti-Sn-based alloy with high damping and excellent mechanical properties, a preparation method and an application thereof, wherein the preparation method comprises the following steps: a binary alloy consisting of metallic titanium and tin, wherein metallic tin is 10-30at.% of the total number of atoms of the alloy, the balance being titanium. The Ti-Sn-based high-damping alloy material with high damping property and excellent mechanical property overcomes the problem of larger brittleness of the material, has high damping property at the same time, has wider application field, and especially plays a role in micro-vibration inhibition in special fields such as aerospace and the like.
Description
Technical Field
The invention belongs to the technical field of Ti-Sn-based alloy preparation, and particularly relates to a Ti-Sn-based alloy with high damping and excellent mechanical properties, and a preparation method and application thereof.
Background
With the wide application of high-precision spacecrafts such as high-resolution remote sensing satellites in the fields of deep space exploration, communication and the like, the work tasks and the work loads are gradually complicated, the precision requirements are higher and higher, wherein the micro-vibration of the satellite structure becomes an important factor influencing the high-precision performance of the precision loads, and the research on the related micro-vibration suppression technology is also greatly concerned by people. Compared with the traditional method, the micro-vibration suppression technology based on the damping material directly starts from a vibration source, mechanical vibration energy of the material is irreversibly converted into energy in other forms such as heat energy and the like through an internal mechanism, the response speed is high, and meanwhile, the system structure is simplified, so that the micro-vibration suppression technology becomes an important technical means. Meanwhile, light weight is also an important aspect of spacecraft development, so that the realization of the light weight and function integration of the damping material also becomes a new idea for solving the micro-vibration of the spacecraft.
Light Ti 3 The Sn alloy is a newer damping material, the highest damping value can reach 0.2 within a broadband range (1-100 KHz) -150 ℃, and the maximum damping value is far greater than the maximum damping value of 0.045 of TiNi shape memory alloy and 0.052 of Mn-Cu alloy. And Ti 3 The specific gravity of the Sn alloy is low (5 g/cm) 3 ) The amplitude dependence is very small, meaning that it can maintain a relatively high damping value at very small strain amplitudes. Thus Ti 3 The Sn alloy has great potential application value in the aspect of micro-vibration suppression in the field of aerospace.
However, ti 3 The crystal structure of the Sn alloy at room temperature is hexagonal D0 19 Lack of sufficient sliding system, very high brittleness, and limitation of subsequent deformation treatment, processing application and the like of the material to a certain extent. If the brittleness of the material can be improved and the elongation of the material can be improved, the application range of the material can be expanded, and the material has larger operation space on subsequent treatment such as rolling, forging and the like, thereby fully exerting Ti 3 The Sn-based high-damping material has the application advantage of light-weight function integration design.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provide a Ti-Sn-based alloy material with high damping and excellent mechanical property. The material can play a role in high damping characteristic in micro-vibration suppression in the aerospace field and the like, more importantly, the plasticity of the alloy can be effectively improved through the design and regulation of the microstructure of the material, particularly the application of a laminated structure, and various problems in the aspects of material later deformation treatment, processing and the like are solved.
The above object is achieved by the following preparation process:
a Ti-Sn based alloy having both high damping and excellent mechanical properties, comprising:
a binary alloy consisting of metallic titanium and tin, wherein metallic tin is 10-30at.% of the total number of atoms of the alloy, the balance being titanium.
As a further improvement of the above technical scheme, the alloy is a ternary alloy formed by metallic titanium, tin and a proper amount of alloying elements;
wherein, the dosage of the metallic tin is 10 to 30at.% of the total number of alloy atoms;
the amount of the alloying element is 0-5at.% of the total atomic number of the alloy, 0-5at.% of titanium is replaced by the alloying element, and the balance is titanium.
As a further improvement of the technical scheme, the alloying element is any one of vanadium, nickel, chromium, molybdenum and niobium.
As a further improvement of the technical scheme, the Ti-Sn-based alloy has oriented large grains with the size of 100-1000um.
As a further improvement of the technical scheme, the Ti-Sn-based alloy has a compact twin crystal sheet layer structure inside, and the thickness of the single layer structure is 0.5-5um.
The invention also provides a preparation method of the Ti-Sn-based alloy with high damping and excellent mechanical property, which comprises the following steps:
s1: mixing the raw materials according to the atomic dosage proportion, putting the mixture into a vacuum arc melting furnace for melting, vacuumizing, then filling argon, controlling the pressure in the furnace, and starting arc striking;
s2: slowly adding current to 100A, melting the titanium particles and the tin particles on the surface layer firstly, avoiding the deviation of alloy components caused by the loss of tin, and then increasing the current to 200A to avoid the influence on the accuracy of the alloy components caused by too low loss of tin due to too low melting point; after the metal is in a flowing state, increasing the current to 300A and keeping the current for 3-5 minutes to ensure that the melt keeps a certain superheat degree so as to ensure that the raw materials are fully reacted;
s3: starting electromagnetic stirring to ensure that alloy components are uniformly mixed, repeatedly smelting the sample obtained in the step S2 forward and backward for at least 5 times, and preparing a slender round bar sample by adopting a suction casting mold sample for directional solidification growth in the next step;
s4: and (3) putting the round bar sample into a cold crucible directional solidification furnace, heating the round bar sample after vacuumizing, starting directional downward drawing after the melt is overheated to the maximum, and ensuring that the feeding volume and the drawing volume are equal to each other to obtain the Ti-Sn-based alloy.
As a further improvement of the above technical solution, S1 specifically is: putting the mixed raw materials into a vacuum arc melting furnace for melting, putting the mixed raw materials into a crucible, putting the crucible into the vacuum arc melting furnace for melting, and putting another crucible in the middle of the furnace for containing a titanium block for removing residual oxygen in the furnace; vacuumizing to 6E-3Pa, filling argon, controlling the pressure in the furnace to-0.05 MPa, and starting arc striking.
As a further improvement of the above technical means, the pulling rate in S6 is as low as possible, and is about 0.1 to 200um/S.
The invention also provides application of the Ti-Sn-based alloy with high damping and excellent mechanical property in the field of preparing a micro-vibration inhibiting material.
The invention has the beneficial effects that:
compared with the prior art, the Ti-Sn-based high-damping alloy material with high damping property and excellent mechanical property overcomes the problem of larger brittleness of the material, still has high damping property, has wider application field, and especially plays a role in micro-vibration inhibition in special fields such as aerospace and the like.
The preparation method disclosed by the invention belongs to the combination of a vacuum arc melting technology and a directional solidification growth technology, can regulate and control the microstructure of the Ti-Sn-based alloy, mainly regulates and controls directional large crystal grains and a microscopic twin crystal lamella structure in the alloy, and further improves the plasticity of the material.
The preparation method disclosed by the invention has the advantages of simple and easy operation in the preparation process, time saving and energy saving, does not need expensive die cost, and is suitable for large-scale industrial production.
Drawings
FIG. 1 is an internal wear performance test of example 1 of the present invention;
FIG. 2 is a tensile property test of example 1 of the present invention;
FIG. 3 is a microstructure of example 1 of the present invention;
FIG. 4 is an internal wear performance test of example 2 of the present invention;
FIG. 5 is a tensile property test of example 2 of the present invention;
FIG. 6 shows the microstructure of example 2 of the present invention;
FIG. 7 is the internal wear performance test of example 3 of the present invention;
FIG. 8 is a tensile property test of example 3 of the present invention;
FIG. 9 is a microstructure of example 3 of the present invention;
FIG. 10 is the internal wear performance test of example 4 of the present invention;
FIG. 11 shows tensile properties of example 4 of the present invention;
FIG. 12 shows the microstructure of example 4 of the present invention;
Detailed Description
The present application will now be described in further detail with reference to the drawings, and it should be noted that the following detailed description is given for purposes of illustration only and should not be construed as limiting the scope of the present application, as these numerous non-limiting modifications and variations will suggest themselves to those skilled in the art in light of the foregoing disclosure.
1. Material
The methods and apparatuses used in the present invention are, unless otherwise specified, conventional methods and apparatuses known to those skilled in the art, and the reagents and other materials used therein are, unless otherwise specified, commercially available products.
2. Method for producing a composite material
2.1 binary alloy
2.1.1 example 1
The Ti-Sn based alloy of this example was prepared as follows:
the method comprises the following steps: pure Ti and pure Sn are used as raw materials, and nominal components of Ti are arranged according to atomic ratio 75 Sn 25 Wherein pure Ti:40.000g; pure Sn:33.058g, putting the mixed raw materials into a crucible, putting the crucible into a vacuum arc melting furnace for melting, and putting another crucible in the middle of the furnace for containing a titanium block for later melting and deoxidizing. When vacuumizing, firstly opening a mechanical pump to 5Pa, then opening a front-stage valve, vacuumizing to 5Pa, and finally vacuumizing to 6E-3Pa by using a molecular pump. Then argon is filled in and the pressure in the furnace is controlled to be-0.05 MPa, so that arc striking is facilitated.
Step two: the current is slowly added to 100A, the titanium particles and the tin particles on the surface layer are firstly melted, and then the current is increased to 200A, so that the condition that the tin is excessively consumed due to too low melting point and the accuracy of the alloy components is influenced is avoided. And after the metal is in a flowing state, increasing the current to 300A and keeping the current for 3-5 minutes to ensure that the melt keeps a certain superheat degree so as to ensure that the raw materials are fully reacted.
Step three: starting electromagnetic stirring to ensure that alloy components are uniformly mixed, repeatedly smelting the front and the back of the sample five times, and preparing a slender round bar sample by using a suction casting die for the next directional solidification growth.
Step four: and (2) putting the Ti-Sn base master alloy round bar material into a cold crucible directional solidification furnace, heating the round bar material after vacuumizing to ensure that the melt is overheated to the maximum, then starting directional drawing down, ensuring that the feeding volume is equal to the drawing volume, and the drawing speed is 0.1-200 um/s.
2.1.2 example 2
The Ti-Sn based alloy of this example was prepared as follows:
the method comprises the following steps: pure Ti and pure Sn are used as raw materials, and nominal components of Ti are arranged according to atomic ratio 83.2 Sn 16.8 Wherein pure Ti:48.000g; pure Sn:24.030g. And the step two-step four is 2.1.1.
2.1.3 binary alloy Performance analysis
2.1.3.1 microstructures
As seen from FIGS. 3 and 6, ti in example 1 75 Sn 25 And Ti in example 2 83.2 Sn 16.8 The alloy has oriented large crystal grains with the size of 100-1000um, a compact twin crystal lamellar structure is arranged inside the alloy, and the thickness of the single-layer structure is 0.5-5um.
2.1.3.2 internal loss Performance
The alloys prepared in examples 1 and 2 were subjected to internal wear performance test and tensile property test respectively using a multifunctional inverted torsional pendulum internal wear tester, and the test results are shown in fig. 1, 2, fig. 4, and 5.
According to the attached drawings, can knowTi prepared herein 75 Sn 25 Elongation of more than 60%, good plasticity, ti 83.2 Sn 16.8 The elongation of the material also reaches 8 percent, and the material has certain plasticity; the damping coefficients of the damping alloy and the damping alloy are both larger than 0.010, the damping alloy belongs to high-damping alloy, and the damping value is higher particularly at lower temperature.
2.2 ternary alloy
2.2.1 example 3
The Ti-Sn based alloy of this example was prepared as follows: the method comprises the following steps: pure Ti, pure Sn and pure Mo are taken as raw materials, and nominal components of Ti are arranged according to atomic ratio 74.25 Sn 24.75 Mo 1 Wherein pure Ti:37.165g; pure Sn:30.714g; pure Mo:1.003g, step two-four is 2.1.1.
2.2.2 example 4
The Ti-Sn based alloy of this example was prepared as follows:
the method comprises the following steps: pure Ti, pure Sn and pure V (any one of vanadium, nickel, chromium, molybdenum and niobium) are taken as raw materials, and the nominal component is Ti according to the atomic ratio configuration 74.25 Sn 24.75 V 1 The alloy of (1), wherein pure Ti:37.420g; pure Sn:30.925g; pure V:0.536g. Step two-four is the same as 2.1.1.
2.2.3 ternary alloy Performance analysis
2.2.3.1 microstructures
As seen from FIGS. 9 and 12, ti in example 3 74.25 Sn 24.75 Mo 1 And Ti in example 4 74.25 Sn 24.75 V 1 The alloy has oriented large crystal grains with the size of 100-1000um, a compact twin crystal lamellar structure is arranged inside the alloy, and the thickness of the single-layer structure is 0.5-5um.
2.2.3.2 internal loss Performance
The alloys prepared in examples 3 and 4 were subjected to internal wear performance test and tensile property test respectively using a multifunctional inverted torsional pendulum internal wear tester, and the test results are shown in fig. 7, 8, fig. 10, and 11.
According to the attached drawings, the Ti prepared by the method is shown in the specification 74.25 Sn 24.75 Mo 1 The elongation of (2) is more than 35%, the shaping is good, and Ti 74.25 Sn 24.75 V 1 The elongation rate of the alloy also reaches 20 percent, the plasticity is good, and other deformation treatments are facilitated; the damping of the two is more than 0.010 in a low-temperature range, and the alloy belongs to high-damping alloy and meets the application requirement.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that a person skilled in the art could make several modifications without departing from the inventive concept, which fall within the scope of protection of the invention.
Claims (9)
1. A Ti-Sn based alloy having both high damping and excellent mechanical properties, comprising:
a binary alloy consisting of metallic titanium and tin, wherein metallic tin is 10-30at.% of the total number of atoms of the alloy, the balance being titanium.
2. The Ti-Sn based alloy of claim 1, wherein 0 to 5at.% of Ti is replaced by an alloying element, and the Ti-Sn based alloy is a ternary alloy of metallic Ti, sn and a proper amount of alloying elements.
3. The Ti-Sn based alloy of claim 2 having both high damping and excellent mechanical properties, wherein the alloying element is any one of vanadium, nickel, chromium, molybdenum and niobium.
4. A Ti-Sn based alloy according to any one of claims 1 to 3 having both high damping and excellent mechanical properties, wherein the Ti-Sn based alloy has oriented large grains with a size of 100 to 1000um.
5. The Ti-Sn based alloy with both high damping and excellent mechanical properties as claimed in any one of claims 1 to 3, wherein the Ti-Sn based alloy has a dense twin crystal lamellar structure inside, and the thickness of the lamellar structure is 0.5 to 5um.
6. A method for preparing Ti-Sn based alloy with high damping and excellent mechanical properties as claimed in any one of claims 1 to 5, comprising the steps of:
s1: mixing the raw materials according to the atomic dosage proportion, putting the mixture into a vacuum arc melting furnace for melting, vacuumizing, then filling argon, controlling the pressure in the furnace, and starting arc striking;
s2: slowly adding current to 100A, after the titanium particles and the tin particles on the surface layer are melted, increasing the current to 200A for keeping, and after the metal is in a flowing state, increasing the current to 300A for keeping for 3-5min;
s3: starting electromagnetic stirring, repeatedly smelting the sample obtained in the step S2 at least for 5 times, and preparing a slender round bar sample by adopting a suction casting mould sample;
s4: and (3) putting the round bar sample into a cold crucible directional solidification furnace, heating the round bar sample after vacuumizing, starting directional downward drawing after the melt is overheated to the maximum, and ensuring that the feeding volume and the drawing volume are equal to each other to obtain the Ti-Sn-based alloy.
7. The preparation method according to claim 6, wherein S1 is specifically: putting the mixed raw materials into a crucible, putting the crucible into a vacuum arc melting furnace to prepare for melting, putting another crucible in the middle of the furnace to contain a titanium block, vacuumizing to 6E-3Pa, filling argon, controlling the pressure in the furnace to be-0.05 MPa, and starting arc striking.
8. The production method according to claim 6, wherein the pulling rate in S6 is 0.1 to 200um/S.
9. Use of the Ti-Sn based alloy of any one of claims 1 to 5 having both high damping and excellent mechanical properties in the preparation of a material for suppressing micro-vibrations.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009215650A (en) * | 2008-02-14 | 2009-09-24 | Tokyo Institute Of Technology | Shape memory alloy |
| CN102358925A (en) * | 2011-09-01 | 2012-02-22 | 中国石油大学(北京) | High-strength and high-damping Ti3Sn/TiNi memory alloy composite material |
| CN104651829A (en) * | 2014-12-10 | 2015-05-27 | 湘潭大学 | Preparation methods of biomedical Ti-Sn coating alloy and medical dental alloy |
| CN109777985A (en) * | 2019-03-29 | 2019-05-21 | 华南理工大学 | High-strength and high damping NiTi base composite foam damping material and the preparation method and application thereof |
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- 2022-10-24 CN CN202211300448.6A patent/CN115627385B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009215650A (en) * | 2008-02-14 | 2009-09-24 | Tokyo Institute Of Technology | Shape memory alloy |
| CN102358925A (en) * | 2011-09-01 | 2012-02-22 | 中国石油大学(北京) | High-strength and high-damping Ti3Sn/TiNi memory alloy composite material |
| CN104651829A (en) * | 2014-12-10 | 2015-05-27 | 湘潭大学 | Preparation methods of biomedical Ti-Sn coating alloy and medical dental alloy |
| CN109777985A (en) * | 2019-03-29 | 2019-05-21 | 华南理工大学 | High-strength and high damping NiTi base composite foam damping material and the preparation method and application thereof |
Non-Patent Citations (1)
| Title |
|---|
| WONG, C.R.等: "Low frequency damping and ultrasonic attenuation in Ti3Sn-based alloys", 《JOURNAL OF MATERIALS RESEARCH》, vol. 9, no. 6, pages 1442 * |
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