CN108950303B - Tough titanium alloy and preparation method thereof - Google Patents
Tough titanium alloy and preparation method thereof Download PDFInfo
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Abstract
The invention provides a tough titanium alloy and a preparation method thereof, and the tough titanium alloy comprises, by mass, 5.2-5.5% of Al, 1.6-1.8% of Sn, 2.5-3.3% of Mo, 0.9-1.0% of Cr, 1.7-1.8% of Nb, 2.5-30% of Zr and the balance Ti. The yield strength of the titanium alloy obtained by the invention is as follows: 990.08-1245.97MPa, tensile strength: 1189.56-1385.66 MPa, elongation: 10.61% -8.21%; compared with Ti-6Al-2Zr-2Sn-2Mo-1.5Cr-2Nb titanium alloy, the strength is obviously improved.
Description
Technical Field
The invention relates to the technical field of titanium alloy, in particular to a tough titanium alloy and a preparation method thereof.
Background
The titanium alloy has a series of advantages of high specific strength, high specific modulus, corrosion resistance and the like, has wide application advantages, and is emphasized in various fields of ocean engineering, aerospace, biomedicine, metallurgy, chemical industry, light industry and the like.
The structural titanium alloy has excellent machinability and mechanical properties, and is used for manufacturing parts with high strength and complex shapes in the aerospace industry, such as wing joint structural members of aviation airplanes, connecting frames of airframes and undercarriages, joints of suspended engines and the like, and manufacturing important or key bearing parts with high requirements on strength and durability. However, as for the traditional titanium alloy of an aviation structure, the comprehensive mechanical properties of toughness of the titanium alloy cannot meet increasingly severe industrial service standards.
Disclosure of Invention
In view of the above, the present invention aims to provide a tough titanium alloy and a preparation method thereof. The titanium alloy provided by the invention has excellent comprehensive mechanical properties of strength and toughness, and meets the requirements of titanium alloys for aviation structures.
The invention provides a tough titanium alloy which comprises, by mass, 5.2-6.8% of Al, 1.6-2.5% of Sn, 2.2-3.3% of Mo, 0.9-2.0% of Cr, 1.7-2.3% of Nb, 2.5-50% of Zr and the balance Ti.
Preferably, the tough titanium alloy comprises 5.2-5.5% of Al, 1.6-1.8% of Sn, 2.5-3.3% of Mo, 0.9-1.0% of Cr, 1.7-1.8% of Nb, 2.5-30% of Zr and the balance of Ti.
Preferably, the tough titanium alloy contains a beta phase and an alpha' phase precipitated from the original beta phase.
The invention provides a preparation method of the tough titanium alloy in the technical scheme, which comprises the following steps:
(1) smelting alloy raw materials to obtain an as-cast alloy blank;
(2) carrying out heat preservation treatment on the as-cast alloy blank obtained in the step (1) and then deforming to obtain a densified alloy blank;
(3) and (3) carrying out solution treatment on the compact alloy blank obtained in the step (2) to obtain the tough titanium alloy.
Preferably, the smelting in the step (1) is vacuum arc smelting, and the temperature of the vacuum arc smelting is 2000-2900 ℃.
Preferably, the smelting times in the step (1) are more than 5 times, and each smelting time is more than 1 min.
Preferably, the temperature of the heat preservation treatment in the step (2) is 880-950 ℃, and the time of the heat preservation treatment is 0.5-1.0 h.
Preferably, the deformation in the step (2) is rolling deformation; the total deformation amount of the rolling deformation is 65-70%, and the temperature of the rolling deformation is 880-950 ℃.
Preferably, the rolling deformation is multi-pass rolling, and the reduction of each pass is 2-3 mm;
when multi-pass rolling is adopted, after each pass of rolling, the rolled alloy billet is kept at the rolling deformation temperature for 5-10 min.
Preferably, the heat preservation temperature of the solution treatment in the step (3) is 880-950 ℃, the heat preservation time of the solution treatment is 4-6 min, and the cooling mode of the solution treatment is water quenching.
The invention provides a tough titanium alloy which comprises, by mass, 5.2-5.5% of Al, 1.6-1.8% of Sn, 2.5-3.3% of Mo, 0.9-1.0% of Cr, 1.7-1.8% of Nb, 2.5-30% of Zr and the balance Ti.
The content of each element is strictly controlled, the mechanical property of the titanium alloy is improved, wherein the eutectoid beta stable element Cr reduces the phase transition temperature of the alloy, the beta phase forming capability of the alloy is enhanced, neutral elements Sn and Zr can be dissolved in alpha phase Ti and beta phase Ti in large quantity, the phase transition temperature of the alloy can be properly reduced by adding Sn and Zr, the Sn reduces the sensitivity of the alloy to hydrogen embrittlement, and the Sn and the Zr play a role in supplementing and strengthening the alloy together, and the alpha stable element Al remarkably strengthens the titanium alloy; the alloy microstructure can also be optimized, and Zr has the performance complementing and improving effects on the Ti alloy. The Zr element added in the invention not only has the function of solid solution strengthening, but also properly reduces the alpha → beta phase transition temperature of the alloy, so that more beta phases are reserved in the alloy, the beta phases are body-centered cubic structures, and have more slip systems compared with the alpha phases of close-packed hexagonal structures, the plasticity is better, the original beta crystal grains of the alloy are refined, the density of the original beta crystal boundary is increased, the dislocation movement is hindered, and the strength is further improved.
The experimental result shows that the yield strength of the titanium alloy obtained by the invention is as follows: 990.08-1245.97MPa, tensile strength: 1189.56-1385.66 MPa, elongation: 10.61% -8.21%; compared with Ti-6Al-2Zr-2Sn-2Mo-1.5Cr-2Nb titanium alloy, the tensile strength is respectively improved by 8.14 percent, 14.33 percent, 18.76 percent, 23.22 percent and 25.97 percent.
Drawings
FIG. 1 is a metallographic optical micrograph of a titanium alloy obtained in example 1;
FIG. 2 is a metallographic optical micrograph of a titanium alloy obtained in example 2;
FIG. 3 is a metallographic optical micrograph of a titanium alloy obtained in example 3;
FIG. 4 is a metallographic optical micrograph of a titanium alloy obtained in example 4;
FIG. 5 is a metallographic optical micrograph of a titanium alloy obtained according to example 5;
FIG. 6 is a graph showing the dimensions of tensile specimens used in the tensile testing of the present invention.
Detailed Description
The invention provides a tough titanium alloy which comprises, by mass, 5.2-6.8% of Al, 1.6-2.5% of Sn, 2.2-3.3% of Mo, 0.9-2.0% of Cr, 1.7-2.3% of Nb, 2.5-50% of Zr and the balance Ti.
The tough titanium alloy comprises 5.2-5.5% of Al, 1.6-1.8% of Sn, 2.5-3.3% of Mo, 0.9-1.0% of Cr, 1.7-1.8% of Nb, 2.5-30% of Zr and the balance of Ti.
The tough titanium alloy provided by the invention comprises 5.2-6.8% of Al, preferably 5.2-5.5%, and more preferably 5.3% by mass. In the present invention, the Al is used to form a delta phase structure of a titanium-aluminum alloy; the element Al greatly improves the stability of alpha phase and the alpha-beta transition temperature, so that the alpha phase which is obtained after quenching in the process of solution treatment is small, the specific strength of the titanium alloy can be greatly improved, and the light weight of the alloy can be realized to a certain extent.
The tough titanium alloy provided by the invention comprises 1.6-2.5% of Sn by mass, preferably 1.6-1.8% of Sn by mass, and more preferably 2.2-2.4% of Sn by mass. In the invention, the solubility of Sn in alpha/beta-Ti is higher, and the Sn reduces the sensitivity of the alloy to hydrogen embrittlement and plays a role in supplementing and strengthening the alloy together with Zr; and Sn and Ti can form hard complex titanium compounds, play a role in resisting abrasion and damage of matching pairs, can effectively solve the problem of serious initial abrasion of the titanium alloy, and greatly prolong the service life. The harmful effect of impurity N can be counteracted, the corrosion resistance of the alloy is improved, and the content of Sn is strictly controlled to avoid the defects that the content of Sn is higher than 4 percent, Ti and Sn hard complex compounds are increased, and the plasticity and the tensile strength of the alloy are reduced.
The tough titanium alloy provided by the invention comprises 2.2-3.3% of Mo, preferably 2.5-3.3% of Mo, and further preferably 2.6-2.8% of Mo according to mass content. In the invention, Mo strengthens beta phase in a solid solution manner, lowers the phase transformation point, enhances the hardenability and further enhances the heat treatment strengthening effect; the addition of Mo also improves the corrosion resistance of the alloy.
The tough titanium alloy provided by the invention comprises 0.9-2.0% of Cr, and more preferably 0.9-1.0%. In the invention, the Cr belongs to eutectoid beta-phase stable elements, not only can broaden a two-phase region, but also can enhance the corrosion resistance of the alloy as a self-passivation metal. The addition of Cr element stabilizes beta phase, and can obviously improve the room temperature strength of the titanium alloy matrix. Cr can reduce the alpha-beta transition temperature and regulate and control the structure composition in the TC titanium alloy. The solubility of Cr in both α -Ti and α -Zr is low. Cr can improve the strength of the titanium alloy, but has a weaker strengthening effect than Sn, and chromium also has an improving effect on the strength creep resistance of the titanium alloy. The addition of Cr not only has strong beta-stabilization effect, but also the beta stabilized by Cr has higher ductility and toughness than other beta-stabilizing elements stabilized by the same crystal form.
The tough titanium alloy provided by the invention comprises 1.7-2.3% of Nb, preferably 1.7-1.8% of Nb, and also preferably 2.1-2.22% of Nb by mass. The addition of a proper amount of Nb in Ti can inhibit the harmful effects of C, Al and N, reduce the hydrogen absorption amount, improve the corrosion resistance and strengthen the alloy.
The tough titanium alloy provided by the invention comprises 2.5-50% of Zr, preferably 2.5-30%, more preferably 5-28%, and even more preferably 8-15% by mass.
In the invention, because the addition of Zr can cause lattice distortion, the defects can cause that in the nucleation process, the number of nucleation points is increased, the nucleation density is increased, and the effect of grain refinement is achieved; the element Zr is added into the titanium substrate, and the neutral element Zr which has little influence on the phase transition temperature and the Ti form an infinite solid solution, so that solid solution strengthening is realized, the passivation potential of the Zr is more negative than that of the Ti, passivation can still occur even in a weak oxidation condition environment, the capability of generating a compact oxide film on the surface is improved, and the corrosion resistance of the titanium substrate is improved.
The tough titanium alloy provided by the invention comprises the balance of Ti in addition to the elements according to the mass content.
In the present invention, the tough titanium alloy contains a beta phase and an alpha' phase precipitated from the original beta phase.
The invention also provides a preparation method of the tough titanium alloy in the technical scheme, which comprises the following steps:
(1) smelting alloy raw materials to obtain an as-cast alloy blank;
(2) carrying out heat preservation treatment on the as-cast alloy blank obtained in the step (1) and then deforming to obtain a densified alloy blank;
(3) and (3) carrying out solution treatment on the compact alloy blank obtained in the step (2) to obtain the tough titanium alloy.
The invention obtains as-cast alloy blank after smelting alloy raw materials. The present invention is not particularly limited in the kind of the alloy raw material, and the alloy raw material well known to those skilled in the art is used to obtain a titanium alloy having a target composition. In the present invention, the alloy raw material preferably includes titanium sponge, zirconium sponge, pure aluminum, pure chromium, high purity vanadium, and high purity tin. The invention has no special limit on the proportion of various alloy raw materials, and the final alloy components can meet the requirements.
In the invention, the smelting is preferably vacuum arc smelting, and the temperature of the vacuum arc smelting is preferably 2000-2900 ℃, more preferably 2200-2400 ℃, and most preferably 2250-2300 ℃; the smelting time is preferably 3-5 min, and more preferably 4 min. In the invention, the vacuum degree of the vacuum arc melting is preferably 0.04-0.05 MPa, and the vacuum arc melting is carried out under the condition of argon. When vacuum arc melting is adopted, the invention preferably firstly pumps the vacuum degree in the furnace chamber to 9 x 10-3Introducing argon gas below Pa; the introduction amount of the argon is enough to satisfy the amount of the ionized gas for arc melting. In the invention, the current of the vacuum arc melting is preferably 400-450 mA, and more preferably 420-435 mA. The invention is specific to the vacuum arc meltingThe embodiments are not particularly required and may be those known to those skilled in the art. The invention adopts the mode of firstly vacuumizing and then introducing argon gas, can firstly prevent a large amount of hydrogen and oxygen absorption and nitrogen absorption of Ti and Zr under the condition of high temperature, and can also provide ionized gas for arc melting. In the invention, the number of times of smelting is preferably 5 or more, and more preferably 6 to 10 times, and an as-cast alloy billet is obtained after smelting. In the present invention, when the melting is repeatedly performed, the melting is preferably performed in a vacuum arc melting furnace; specifically, the method comprises the following steps: smelting a metal raw material in an electric arc smelting furnace to obtain a smelting liquid; and then cooling to obtain a casting blank, turning over the casting blank, smelting, obtaining a smelting solution again, cooling the smelting solution again to obtain the casting blank, repeating the process for more than 5 times to ensure that the obtained as-cast blank has uniform components.
During smelting, beta phase preferentially nucleates and grows in the process of converting a smelting liquid into a solid state to obtain a beta phase blank, and a foundation is provided for separating out alpha 'and alpha' martensite phases from an original beta phase during subsequent solid solution treatment.
Before smelting, the alloy raw materials are preferably subjected to ultrasonic cleaning; the present invention does not require special embodiments of the ultrasonic cleaning, and may be practiced as is known to those skilled in the art.
After the as-cast alloy blank is obtained, the as-cast alloy blank is deformed after heat preservation treatment to obtain a densified alloy blank. According to the invention, the thermal insulation treatment is carried out on the as-cast alloy blank firstly, and then the deformation treatment is carried out, so that the titanium alloy ingot can keep a higher temperature in the deformation process, and the thermal deformation is realized. The invention adopts thermal deformation to preferably eliminate casting defects, compact the titanium alloy structure, refine grains, generate a large amount of dislocation, improve the mechanical property of the alloy in the rolling direction and obviously improve the tensile strength in particular.
In the invention, the temperature of the heat preservation treatment is preferably 880-950 ℃, more preferably 885-920 ℃, and more preferably 890-900 ℃. In the present invention, the heat-preserving time of the solution treatment is preferably 0.5 to 1.0 hour, and more preferably 35 to 45 min. In the present invention, the cooling method of the solution treatment is preferably water quenching. The present invention does not require any particular embodiment of the solution treatment, and embodiments known to those skilled in the art may be used. In the present invention, the heat preservation process of the solution treatment is preferably performed under a protective atmosphere, specifically, an argon protective atmosphere. By adopting the solid solution treatment, the solid solution temperature is low, the solid solution time is long, Zr can be solid-dissolved in the alloy matrix in the solid solution treatment, and the metastable beta phase of the physical cubic structure can be retained, so that the mechanical property of the alloy is improved, and the tensile strength of the titanium alloy is improved.
After the heat preservation treatment, the titanium alloy ingot after heat preservation is deformed to obtain a compact alloy blank. In the invention, the deformation is preferably rolling deformation, and the total deformation amount of the rolling deformation is preferably 65-70%, and more preferably 66-68%; the rolling deformation temperature is preferably 880-950 ℃, and is further preferably 885-920 ℃, and is consistent with the temperature in the heat preservation treatment process. In the present invention, the deformation treatment refines metastable β -phase grains and generates a large number of dislocations, contributing to an improvement in alloy strength.
In the invention, the rolling deformation is further preferably multi-pass rolling, and the deformation amount of each pass is preferably 2-3 mm; the invention has no special requirement on the rolling times of the multi-pass rolling so as to finish the target deformation. When the alloy billet is rolled for multiple times, after each rolling, the temperature of the rolled alloy billet is preferably kept for 5-10 min, and more preferably 6-8 min at the rolling deformation temperature. The present invention does not require special embodiments of the rolling deformation, and can be implemented as is well known to those skilled in the art.
After the densified alloy billet is obtained, the invention carries out solid solution treatment on the densified alloy billet to obtain the tough titanium alloy. In the invention, the heat preservation temperature of the solution treatment is preferably 880-950 ℃, more preferably 885-920 ℃, and more preferably 890-900 ℃; the heat preservation time of the solution treatment is preferably 4-6 min, and more preferably 5 min. In the present invention, the cooling method of the solution treatment is preferably water quenching, and more preferably water quenching in water at room temperature. The present invention does not require any particular embodiment of the solution treatment, and embodiments known to those skilled in the art may be used. In the present invention, the heat preservation process of the solution treatment is preferably performed under a protective atmosphere, specifically, an argon protective atmosphere. In the present invention, the solution treatment traps as much metastable beta phase as possible, producing a small amount of alpha "martensite phase and alpha' martensite phase; a small amount of alpha' phase can properly reduce the elastic modulus of the alloy, has little influence on the mechanical property index of the alloy, beta phase is a body-centered cubic structure, has more slip systems compared with the alpha phase of a close-packed hexagonal structure, and shows better plasticity, the original beta crystal grains of the alloy are refined, the density of the original beta crystal grain boundary is increased, the dislocation movement is hindered, and the strength is further improved.
After the solution treatment, the surface oxide skin of the titanium alloy after the solution treatment is preferably removed, so that the high-strength corrosion-resistant titanium alloy is obtained. The invention preferably adopts a grinding mode to remove the surface scale.
In order to further illustrate the present invention, the following detailed description will be made of the tough titanium alloy and the preparation method thereof provided by the present invention with reference to the examples, but they should not be construed as limiting the scope of the present invention.
Example 1
Weighing 76.058g of industrial-grade sponge titanium, 10.326g of sponge zirconium, 6g of high-purity aluminum, 2g of high-purity tin, 2g of high-purity molybdenum, 1.5g of chromium and 2g of niobium wire, soaking the materials into absolute ethyl alcohol for ultrasonic cleaning, drying the materials after ultrasonic cleaning, placing the materials into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and pumping the vacuum degree in the furnace cavity to 8 multiplied by 10 to obtain the vacuum degree-3And (2) below Pa, introducing high-purity argon as a protective gas (the vacuum degree is 0.04-0.05 MPa) before arc melting, then performing arc temperature of about 2500 ℃ during each melting, performing melting time of about 3 minutes after each melting, cooling to obtain an ingot after each melting, performing turnover treatment on the ingot to perform melting, and repeatedly melting the cast ingot and turning the ingot for 9 times to ensure that the finally obtained ingot is uniform in component.
And then heating the taken alloy ingot to a rolling temperature and preserving heat for 60 minutes, wherein the rolling temperature is 930 ℃, the rolling is multi-pass rolling deformation, the reduction of each pass is about 2mm, after each pass of rolling, the alloy ingot is placed into a muffle furnace to be reheated to 900 ℃ and preserved heat for 10 minutes, and the alloy ingot is made into an alloy plate with the final deformation of 65 percent. After the final pass rolling, carrying out solution treatment: and re-heating to 930 ℃, preserving heat for 5 minutes, then rapidly quenching in room-temperature water, taking out the alloy plate after the alloy plate is completely cooled, finely polishing off an oxide layer on the surface of the alloy ingot, cleaning and air-drying the alloy ingot to obtain the tough titanium alloy.
Metallographic structure observation is carried out on the titanium alloy obtained in the example, and as shown in fig. 1, the obtained high-toughness titanium alloy is composed of a beta phase and a small amount of alpha 'and alpha' phases separated from the original beta phase, wherein original beta phase grains are relatively coarse, and original beta grain boundaries do not exist in the shown area.
Example 2
Weighing 66.438g of industrial-grade sponge titanium, 20.214g of sponge zirconium, 6g of high-purity aluminum, 2g of high-purity tin, 2g of high-purity molybdenum, 1.5g of chromium and 2g of niobium wire, soaking the materials into absolute ethyl alcohol, cleaning by ultrasonic waves, drying in the air, placing the materials into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and pumping the vacuum degree in a furnace cavity to 8 multiplied by 10 according to the alloy components of Ti-20Zr-6Al-2Sn-2Mo-1.5Cr-2Nb (mass percent)-3And (2) below Pa, introducing high-purity argon as a protective gas (the vacuum degree is 0.04-0.05 MPa) before arc melting, then performing arc melting at the temperature of about 2900 ℃ for each time, performing melting for about 3 minutes, cooling to obtain an ingot after each melting, performing turnover treatment on the ingot to perform melting, and repeatedly melting the cast ingot and turning the ingot for 7 times to ensure that the finally obtained ingot is uniform in component.
And then heating the taken alloy ingot to a rolling temperature and preserving heat for 50 minutes, wherein the rolling temperature is 920 ℃, the rolling is multi-pass rolling deformation, the thickness of the finally obtained plate is 5mm, the reduction of each pass is about 2mm, after each pass of rolling, the finally obtained plate is placed into a muffle furnace to be reheated to 920 ℃ and preserved heat for 10 minutes, and the alloy ingot is made into an alloy plate with the final deformation of 65 percent. After the final pass rolling, carrying out solution treatment: and (3) reheating to 920 ℃, keeping the temperature for 5 minutes, then rapidly quenching in room-temperature water, taking out the alloy plate after the alloy plate is completely cooled, finely polishing off an oxide layer on the surface of the alloy ingot, cleaning and air-drying the alloy ingot to obtain the tough titanium alloy.
Metallographic structure observation is carried out on the titanium alloy obtained in the example, and as shown in fig. 2, the obtained high-toughness titanium alloy is composed of a beta phase and a small amount of alpha ' and alpha ' phases separated from the original beta phase, wherein original beta phase grains are relatively coarse, original beta grain boundaries are not in the shown area, and alpha ' martensite phases separated from the original beta phase are refined.
Example 3
Weighing 56.987g of industrial-grade sponge titanium, 29.821g of sponge zirconium, 6g of high-purity aluminum, 2g of high-purity tin, 2g of high-purity molybdenum, 1.5g of chromium and 2g of niobium wire, soaking the materials into absolute ethyl alcohol, cleaning by ultrasonic waves, drying in the air, placing the materials into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and pumping the vacuum degree in a furnace cavity to 8 multiplied by 10 according to the alloy components of Ti-30Zr-6Al-2Sn-2Mo-1.5Cr-2Nb (mass percent)-3And (2) below Pa, introducing high-purity argon as a protective gas (the vacuum degree is 0.04-0.05 MPa) before arc melting, then performing arc temperature of about 2500 ℃ during each melting, performing melting time of about 3 minutes after each melting, cooling to obtain an ingot after each melting, performing turnover treatment on the ingot to perform melting, and repeatedly melting the cast ingot and turning the ingot for 10 times to ensure that the finally obtained ingot is uniform in component.
And then heating the taken alloy ingot to a rolling temperature and preserving heat for 45 minutes, wherein the rolling temperature is 910 ℃, the rolling is multi-pass rolling deformation, the reduction of each pass is about 2mm, after each pass of rolling, the alloy ingot is placed into a muffle furnace to be reheated to 910 ℃ and preserved heat for 10 minutes, and the alloy ingot is made into an alloy plate with the final deformation of 50 percent. After the final pass rolling, carrying out solution treatment: and reheating to 910 ℃, preserving heat for 5 minutes, then rapidly quenching in room-temperature water, taking out after the alloy plate is completely cooled, finely polishing off an oxide layer on the surface of the alloy ingot, cleaning and air-drying to obtain the tough titanium alloy.
Metallographic structure observation is performed on the titanium alloy obtained in the example, and as shown in fig. 3, it can be seen that the obtained high-toughness titanium alloy consists of a beta phase and a small amount of alpha 'and alpha "phases precipitated from the original beta phase, wherein original beta phase grains are refined, incomplete original beta grain boundaries exist in the shown area, and alpha' and alpha" martensite phases precipitated from the original beta phase are refined.
Example 4
Weighing 46.561g of industrial-grade sponge titanium, 40.061g of sponge zirconium, 6g of high-purity aluminum, 2g of high-purity tin, 2g of high-purity molybdenum, 1.5g of chromium and 2g of niobium wire, soaking the materials into absolute ethyl alcohol, cleaning by ultrasonic waves, drying in the air, placing the materials into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and pumping the vacuum degree in a furnace cavity to 8 multiplied by 10 according to the alloy components of Ti-40Zr-6Al-2Sn-2Mo-1.5Cr-2Nb (mass percent)-3And (2) below Pa, introducing high-purity argon as a protective gas (the vacuum pressure reaches 0.04-0.05 MPa) before arc melting, then performing arc melting at the temperature of about 2500 ℃ for each time, performing melting for about 3 minutes, cooling to obtain an ingot after each time of melting is finished, performing turnover treatment on the ingot to perform melting, and repeatedly melting the cast ingot and turning over the ingot for 6 times to ensure that the finally obtained ingot is uniform in component.
And then heating the taken alloy ingot to a rolling temperature and preserving heat for 40 minutes, wherein the rolling temperature is 900 ℃, the rolling is multi-pass rolling deformation, the reduction of each pass is about 2mm, after each pass of rolling, the alloy ingot is placed into a muffle furnace to be reheated to 900 ℃ and preserved heat for 10 minutes, and the alloy ingot is made into an alloy plate with the final deformation of 65 percent. After the final pass rolling, carrying out solution treatment: and re-heating to 900 ℃, preserving heat for 5 minutes, then rapidly quenching in room-temperature water, taking out the alloy plate after the alloy plate is completely cooled, finely polishing off an oxide layer on the surface of the alloy ingot, cleaning and air-drying the alloy ingot to obtain the tough titanium alloy.
Metallographic structure observation is carried out on the titanium alloy obtained in the example, and as shown in fig. 4, the obtained high-toughness titanium alloy is composed of a beta phase and a small amount of alpha ' and alpha ' phases separated from the original beta phase, wherein original beta phase grains are refined, complete original beta grain boundaries exist in the shown area, and alpha ' martensite phases separated from the original beta phase are further refined.
Example 5
Weighing 36.523g of industrial-grade sponge titanium, 49.875g of sponge zirconium, 6g of high-purity aluminum, 2g of high-purity tin, 2g of high-purity molybdenum, 1.5g of chromium and 2g of niobium wire, soaking the materials into absolute ethyl alcohol, cleaning by ultrasonic waves, drying in the air, placing the materials into a water-cooled copper crucible of a non-consumable vacuum arc melting furnace, and pumping the vacuum degree in a furnace cavity to 8 multiplied by 10 according to the alloy components of Ti-50Zr-6Al-2Sn-2Mo-1.5Cr-2Nb (mass percent)-3And (2) below Pa, after introducing high-purity argon as a protective gas before arc melting, wherein the arc temperature is about 2500 ℃ during each melting, the melting time is about 3 minutes, after each melting, cooling to obtain an ingot, turning the ingot over for melting, and repeatedly melting the cast ingot by the melting-casting and turning the ingot over for 8 times to ensure that the finally obtained ingot is uniform in components.
And then heating the taken alloy ingot to a rolling temperature and preserving heat for 30 minutes, wherein the rolling temperature is 890 ℃, the rolling is multi-pass rolling deformation, the reduction of each pass is about 2mm, after each pass of rolling, the alloy ingot is placed into a muffle furnace to be reheated to 890 ℃ and preserved heat for 10 minutes, and the alloy ingot is made into an alloy plate with the final deformation of 65 percent. After the final pass rolling, carrying out solution treatment: and re-heating to 890 ℃, preserving heat for 5 minutes, then rapidly quenching in room-temperature water, taking out the alloy plate after the alloy plate is completely cooled, finely polishing off an oxide layer on the surface of the alloy ingot, cleaning and air-drying the alloy ingot to obtain the tough titanium alloy.
Metallographic structure observation is carried out on the titanium alloy obtained in the example, and as shown in fig. 5, the obtained high-toughness titanium alloy is composed of a beta phase and a small amount of alpha ' and alpha ' phases separated from the original beta phase, wherein original beta phase grains are further refined, a plurality of original beta grain boundaries are completely present in the area, and alpha ' martensite phases separated from the original beta phase are further refined.
Comparative example 1
An alloy composition of Ti-6Al-2Zr-2Sn-2Mo-1.5Cr-2Nb titanium alloy was prepared in the manner of example 1.
Examples 1 to 5 and comparative examples were each prepared by wire cuttingTensile specimens (national standard: GBT228-2002) were cut out of the titanium alloy of example 1, and the tensile specimens were shown in FIG. 6. At least 5 tensile specimens were cut out of each sample to ensure reproducibility of the data, and the measurement was carried out using a room temperature uniaxial tensile test with an Instron5982 universal material tester (manufacturer: Instron, usa) whose tensile displacement was monitored all the way with a extensometer, the tensile rate being set at 5 × 10-3s-1And performing a tensile test to obtain data related to the mechanical properties, wherein the test results are shown in table 1.
TABLE 1 mechanical Property test and grain size results of titanium alloys obtained in examples 1-5 and comparative example 1
As is apparent from Table 1, the titanium alloys obtained in examples 1 to 5 had yield strengths as compared with the actually measured Ti-6Al-2Zr-2Sn-2Mo-1.5Cr-2Nb titanium alloy in the titanium alloy obtained in the present invention: 990.08-1245.97MPa, tensile strength: 1189.56-1385.66 MPa, elongation: 10.61% -8.21%; the strength of the titanium alloy obtained in the embodiments 1-5 is improved by 8.14%, 14.33%, 18.76%, 23.22% and 25.97% compared with that of Ti-6Al-2Zr-2Sn-2Mo-1.5Cr-2Nb titanium alloy, so that the strength is obviously improved, the plasticity is not obviously reduced, the comprehensive mechanical property is improved, and the toughness change trend can be reflected from the side surface.
The embodiment can show that the mechanical property of the titanium alloy is improved by controlling the content of each element, the strength and the toughness of the titanium alloy are obviously improved, and the titanium alloy meets the requirements of aviation components.
The foregoing is merely a preferred embodiment of the invention and is not intended to limit the invention in any manner. It should be noted that, for those skilled in the art, without departing from the principle of the present invention, several improvements and modifications can be made, and these improvements and modifications should also be construed as the protection scope of the present invention.
Claims (4)
1. A tough titanium alloy comprises, by mass, 6% of Al, 2% of Sn, 2% of Mo, 1.5% of Cr, 2% of Nb, 50% of Zr and the balance of Ti;
the preparation method of the tough titanium alloy comprises the following steps:
(1) smelting alloy raw materials to obtain an as-cast alloy blank;
(2) carrying out heat preservation treatment on the as-cast alloy blank obtained in the step (1) and then deforming to obtain a densified alloy blank;
(3) carrying out solution treatment on the compact alloy blank obtained in the step (2) to obtain a tough titanium alloy;
the smelting in the step (1) is vacuum arc smelting, and the temperature of the vacuum arc smelting is 2000-2900 ℃;
the temperature of the heat preservation treatment in the step (2) is 880-950 ℃, and the time of the heat preservation treatment is 0.5-1.0 h;
the deformation in the step (2) is rolling deformation; the total deformation amount of the rolling deformation is 65-70%, and the temperature of the rolling deformation is 880-950 ℃;
the heat preservation temperature of the solution treatment in the step (3) is 880-950 ℃, the heat preservation time of the solution treatment is 4-6 min, and the cooling mode of the solution treatment is water quenching;
the tough titanium alloy contains a beta phase and an alpha' phase precipitated from the original beta phase.
2. The method for preparing the tough titanium alloy of claim 1, which is characterized by comprising the following steps:
(1) smelting alloy raw materials to obtain an as-cast alloy blank;
(2) carrying out heat preservation treatment on the as-cast alloy blank obtained in the step (1) and then deforming to obtain a densified alloy blank;
(3) carrying out solution treatment on the compact alloy blank obtained in the step (2) to obtain a tough titanium alloy;
the smelting in the step (1) is vacuum arc smelting, and the temperature of the vacuum arc smelting is 2000-2900 ℃;
the temperature of the heat preservation treatment in the step (2) is 880-950 ℃, and the time of the heat preservation treatment is 0.5-1.0 h;
the deformation in the step (2) is rolling deformation; the total deformation amount of the rolling deformation is 65-70%, and the temperature of the rolling deformation is 880-950 ℃;
the heat preservation temperature of the solution treatment in the step (3) is 880-950 ℃, the heat preservation time of the solution treatment is 4-6 min, and the cooling mode of the solution treatment is water quenching.
3. The production method according to claim 2, wherein the number of times of melting in the step (1) is 5 or more, and each melting time is 1min or more.
4. The preparation method according to claim 2, wherein the rolling deformation is multi-pass rolling, and the reduction of each pass is 2-3 mm;
when multi-pass rolling is adopted, after each pass of rolling, the rolled alloy billet is kept at the rolling deformation temperature for 5-10 min.
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