CN109371283B - High-strength high-toughness Ti5Mo5V5Cr3Al titanium alloy and preparation method thereof - Google Patents
High-strength high-toughness Ti5Mo5V5Cr3Al titanium alloy and preparation method thereof Download PDFInfo
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- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
The invention provides a novel titanium alloy and a processing technology thereof, and particularly provides a titanium alloy with a general formula of Ti5Mo5V5Cr3Al, wherein the main alloy element content (wt%) of the titanium alloy is as follows: 4.5 to 5.5 percent of Mo; v is 4.5 to 5.5 percent; 4.5 to 5.5 percent of Cr; 2.5 to 3.5 percent of Al; the balance being titanium. The alloy has excellent cold and hot processing performance, higher aging strengthening capability and good strong plasticity performance matching, can be used for preparing plates, bars, forgings and other sections, and has great application potential in the fields of aviation, aerospace, petroleum, ships and the like.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a titanium alloy with a general formula of Ti5Mo5V5Cr3Al and a preparation method thereof.
Background
Ti-Mo-V-Cr-Al series titanium alloy is widely applied to the fields of aerospace and the like because of the characteristics of high strength and high toughness. Ti5Mo5V3Al-Cr series titanium alloy which is self-developed in China is a series of near-beta or metastable-beta titanium alloy, wherein the main alloy element content (wt%) of Ti5Mo5V8Cr3Al (the national standard mark is TB2) alloy is as follows: 4.7 to 5.7 percent of Mo; v is 4.7 to 5.7 percent; 7.5 to 8.5 percent of Cr; 2.5 to 3.5 percent of Al; the balance is titanium, and the titanium has better cold forming performance, so the titanium plate is used in the field of aviation and aerospace industry, but the titanium plate has the defects of higher deformation resistance in forging and difficulty in obtaining an ideal forging state tissue structure, thereby limiting the application field of the titanium plate as a forged piece. The main alloy element content (wt%) of Ti5Mo5V2Cr3Al (national standard TB10) alloy is as follows: 4.5 to 5.5 percent of Mo; v is 4.5 to 5.5 percent; 1.5 to 2.5 percent of Cr; 2.5 to 3.5 percent of Al; the balance is titanium, and although the titanium has better hot forging performance, the titanium has poorer cold deformation performance and is not suitable for being used as a cold-rolled sheet. Therefore, the high-strength and high-toughness titanium alloy with excellent forgeability and cold deformation performance better meets and meets the application and assembly requirements of the increasingly expanded aerospace industry field.
Disclosure of Invention
The invention provides a titanium alloy with a general formula of Ti5Mo5V5Cr3Al, which has high aging strengthening characteristic and good cold and hot processing performance.
In one aspect, the present invention provides a titanium alloy having the general formula Ti5Mo5V5Cr3Al, the main alloying elements (wt%): 4.5 to 5.5 percent of Mo; v is 4.5 to 5.5 percent; 4.5 to 5.5 percent of Cr; 2.5 to 3.5 percent of Al; the balance being titanium.
In another aspect, the present invention provides a method for preparing a titanium alloy having the general formula Ti5Mo5V5Cr3Al, comprising the steps of:
firstly, the following ingredients are prepared according to the following proportion (wt%): 4.5 to 5.5 percent of Mo; v is 4.5 to 5.5 percent; 4.5 to 5.5 percent of Cr; 2.5 to 3.5 percent of Al; fe < 0.30%; c < 0.05% N < 0.04%; h, is less than 0.015 percent; o is less than 0.15 percent; the balance being titanium;
secondly, pressing the ingredients into an electrode;
thirdly, smelting the mixture in a vacuum consumable electrode furnace for 3 times to form an ingot with the diameter phi of 420 mm;
fourthly, forging and cogging at 1100 ℃ to obtain a hot forging bar blank with the diameter phi of 180 mm;
fifthly, obtaining a bar with the diameter of 10-100 mm by hot rolling the bar at 980 ℃;
sixthly, preserving the heat for 0.5h at 800-850 ℃, and cooling to room temperature by water;
and seventhly, preserving the heat for 1 to 8 hours at the temperature of 500 to 550 ℃, and cooling the mixture to room temperature in air.
The invention has the beneficial effects that: compared with the existing metastable beta type Ti5Mo5V8Cr3Al (TB2) titanium alloy and near beta type Ti5Mo5V2Cr3Al (TB10) titanium alloy, the Ti5Mo5V5Cr3Al titanium alloy has better hot forging performance and cold bending performance, and the matching of tensile strength and plasticity is best.
Drawings
FIG. 1 is a microstructure of three alloys in example 2 of the present invention.
Detailed Description
The present invention will be described in detail below with reference to the drawings and examples, but the present invention is not limited to the examples.
Example 1: comparison of Hot formability of titanium alloys
Preparing an alloy material according to the following proportion, wherein the main alloy element content (wt%) is as follows: 5.0 parts of Mo; v is 5.0; 5.0 of Cr; 3.0 of Al; 0.11 of Fe; 0.008 of C; n is 0.010; h is 0.0015; 0.10 of O; the balance being titanium. Pressing the mixture into an electrode. And smelting for three times in a vacuum consumable electrode furnace to obtain an ingot. Forging and cogging at 1100 ℃, and rolling into a phi 15mm bar at 980 ℃ to obtain a sample 1.
The chromium content in the alloy was changed to 2.0% and 8.0%, respectively, and the same forming process as that used to prepare sample 1 was used to obtain a phi 15mm bar, and comparative samples 2 and 3 were obtained, respectively.
Samples 1-3 were processed into thermo-compressed samples of phi 8 x 15 mm. The test is carried out on a Gleeble-1500 thermal simulation testing machine, the temperature is increased to 900 ℃ by a heater and is preserved for 3 minutes, and the strain rate is 0.1s-1. The thermal modeling parameter performance of the titanium alloy was obtained for comparison of its hot formability as shown in table 1.
TABLE 1
As can be seen from table 1, sample 1(Ti5Mo5V5Cr3Al titanium alloy) has peak and steady state stresses comparable to comparative sample 2(Ti5Mo5V2Cr3Al titanium alloy) and a temperature sensitivity index comparable to comparative sample 3(Ti5Mo5V8Cr3Al titanium alloy). In addition, sample 1 has the lowest activation energy for thermal deformation. The data show that sample 1 (i.e., the alloy of the present invention) has a low resistance to deformation when hot deformed, requires a low activation energy for thermal deformation, and is less sensitive to temperature changes during thermal deformation. In summary, sample 1 has the most excellent hot workability and is suitable for various types of forged structural members.
Example 2: comparison of Cold formability of titanium alloys
Preparing an alloy material according to the following proportion, wherein the main alloy element content (wt%) is as follows: 5.0 parts of Mo; v is 5.0; 5.0 of Cr; 3.0 of Al; 0.11 of Fe; 0.008 of C; n is 0.010; h is 0.0015; 0.10 of O; the balance being titanium. Pressing the mixture into an electrode. And smelting for three times in a vacuum consumable electrode furnace to obtain an ingot. Forging and cogging at 1100 ℃, and rolling into a phi 15mm bar at 980 ℃ to obtain a sample 4.
The chromium content in the alloy was changed to 2.0% and 8.0%, respectively, and the same forming process as that used to prepare sample 6 was used to obtain a phi 15mm bar, and comparative samples 5 and 6 were obtained, respectively.
Samples 4-6 were processed into 2X 15X 200mm bend angle specimens. Test the bending angle was tested in an FPJ100 tensile materials tester. The bending angle properties of the obtained titanium alloy are shown in table 2.
TABLE 2
| Material | Status of state | Bending angle (°) |
| Sample No. 4 | Water quenching at 800 deg.C for 30min | 150 |
| Comparative sample 5 | Quenching with water at 840 deg.C for 30min | 85 |
| Comparative sample 6 | Water quenching at 760 deg.C for 30min | 160 |
As can be seen from Table 2, sample 4(Ti5Mo5V5Cr3Al titanium alloy) has a similar bend angle to comparative sample 6(Ti5Mo5V8Cr3Al titanium alloy). Comparative sample 5(Ti5Mo5V2Cr3Al titanium alloy) has the smallest bending angle. The data show that both sample 4 and comparative sample 6 can obtain a large bending angle when cold-bending deformation is performed, indicating that the cold-bending deformation performance is excellent. The comparative sample 5 is inferior in cold deformation performance and is not suitable for use as a cold-deformable structural member.
The difference in microstructure of the three alloys in this state is the main cause of the difference in cold deformation properties, as shown in fig. 1. As can be seen from fig. 1, both sample 4 and comparative sample 6 have a single β -phase structure, and the structure of comparative sample 5 is a dispersed distribution of acicular martensite and β -phase matrix composition. According to the characteristic that the plastic deformation of metal is easy from close-packed hexagonal phase, body-centered cubic phase to face-centered cubic phase, the titanium alloy mainly comprises alpha phase and beta phase, wherein the beta phase has a body-centered cubic structure, and the alpha phase has a close-packed hexagonal structure, so that the beta phase is easy to be plastically deformed compared with the alpha phase. The martensite phase and the alpha phase have the same structure and are also in a close-packed hexagonal structure. Therefore, the formation of martensite phase increases the deformation resistance of the alloy during plastic deformation, and the existence of the second phase during cold deformation leads to the adverse effects of inconsistent strain, nonuniform structure, and high deformation resistance. Thus, sample 4 (i.e., the alloy of the present invention) and comparative sample 6 had more excellent cold deformation properties than comparative sample 5.
In conclusion, the titanium alloy has the characteristics of excellent cold forming performance of Ti5Mo5V8Cr3Al alloy and excellent hot forming performance of Ti5Mo5V2Cr3Al alloy, and is an ideal titanium alloy structural material suitable for cold and hot deformation processing.
Example 3: mechanical property comparison of titanium alloys
Preparing an alloy material according to the following proportion, wherein the main alloy element content (wt%) is as follows: 5.0 parts of Mo; v is 5.0; 5.0 of Cr; 3.0 of Al; 0.11 of Fe; 0.008 of C; n is 0.010; h is 0.0015; 0.10 of O; the balance being titanium. Pressing the mixture into an electrode. And smelting for three times in a vacuum consumable electrode furnace to obtain an ingot. Forging and cogging at 1100 ℃, rolling into a bar with the diameter of 15mm at 980 ℃, preserving heat at 800 ℃ for 30 minutes, water quenching, preserving heat at 520 ℃ for 8 hours, and air cooling to obtain a sample 7.
The chromium content of the alloy was changed to 2.0% and 8.0%, respectively, and comparative samples 8 and 9 were obtained by applying the same preparation process as that of sample 7.
Sample 7 and comparative samples 8 and 9 were processed into conventional tensile specimens of Φ 5 mm. The tests were carried out on an AG50KNE tester. The mechanical properties of the titanium alloys are shown in table 3. The results show that sample 7 has the best match of tensile strength and plastic properties. The comparative sample 8 has poor plasticity under a high-strength state; comparative sample 9, although having better plastic properties, has lower strength than the other two alloys. In comprehensive comparison, sample 7 (i.e., the alloy of this item) has better age strengthening ability and the best plasticity performance in a high-strength state.
TABLE 3
Example 4: comparison of mechanical Properties of alloys
The gold material is mixed according to the following proportion, and the main alloy element content (wt%) is as follows: 5.0 parts of Mo; v is 5.0; 5.0 of Cr; 3.0 of Al; 0.11 of Fe; 0.008 of C; n is 0.010; h is 0.0015; 0.10 of O; the balance being titanium. Pressing the mixture into an electrode. And smelting for three times in a vacuum consumable electrode furnace to obtain an ingot. Forging and cogging at 1100 ℃, rolling into a bar with the diameter of 15mm at 980 ℃, preserving heat at 800 ℃ for 30 minutes, water quenching, preserving heat at 520 ℃ for 8 hours, and air cooling to obtain a sample 10.
The chromium content of the alloy was changed to 2.0% and 8.0%, respectively, and the same forming process as that used to prepare sample 6 was used to obtain a phi 15mm rod. Keeping the temperature of the alloy with the Cr content of 2.0 percent at 840 ℃ for 30 minutes, water quenching, keeping the temperature at 550 ℃ for 5 hours, and air cooling to obtain a comparative sample 11; the alloy with 8.0% Cr is quenched by water at 760 ℃ for 30 minutes, and then cooled by air at 490 ℃ for 14 hours to obtain comparative sample 12.
Sample 10 and comparative samples 11 and 12 were processed into conventional tensile specimens of Φ 5 mm. The tests were carried out on an AG50KNE tester. The mechanical properties obtained are shown in table 4.
The results show that the Ti5Mo5V5Cr3Al titanium alloy of the present invention, sample 10, had a better match of tensile strength and plasticity properties by aging the strength of the three alloys to the same strength level (about 1400MPa) through different heat treatment processes. When the strength of a comparative sample 11(Ti5Mo5V2Cr3Al titanium alloy) reaches 1400MPa, the plasticity is poor; although the comparative sample 12 has better strength and plasticity performance matching, the aging strengthening is difficult, the strength is improved to about 1400MPa, the time is required to be 14 hours, the time is far more than that of other two alloys, and the operability is poor from the industrial production perspective.
TABLE 4
In conclusion, the Ti5Mo5V5Cr3Al titanium alloy combines the advantages of the existing near-beta alloy Ti5Mo5V2Cr3Al and the metastable beta type Ti5Mo5V8Cr3Al titanium alloy, has equivalent or even better hot forging performance than the Ti5Mo5V2Cr3Al alloy, and simultaneously has the cold deformation performance which is comparable to the Ti5Mo5V8Cr3Al titanium alloy. In addition, the Ti5Mo5V5Cr3Al titanium alloy has strong aging strengthening capability, better plasticity performance in a high-strength state and excellent matching of strong plasticity performance, thereby being a titanium alloy structural material which can be deformed by cold and hot working and has excellent comprehensive performance.
The above embodiments describe the technical solutions of the present invention in detail. It will be clear that the invention is not limited to the described embodiments. Based on the embodiments of the present invention, those skilled in the art can make various changes, but any changes equivalent or similar to the present invention are within the protection scope of the present invention.
Claims (2)
1. A titanium alloy having a general formula of Ti5Mo5V5Cr3Al, wherein the titanium alloy has a formula in which the alloying elements are present in the formula (wt%): 5.0 percent of Mo, 5.0 percent of V, 5.0 percent of Cr, 3.0 percent of Al, 0.11 percent of Fe and the balance of titanium; 0.008 percent of C, 0.010 percent of N, 0.0015 percent of H and 0.10 percent of O;
the preparation method of the titanium alloy comprises the following steps:
1) the materials are prepared according to the following proportion (wt%): 5.0 percent of Mo, 5.0 percent of V, 5.0 percent of Cr, 3.0 percent of Al, 0.11 percent of Fe, 0.008 percent of C, 0.010 percent of N, 0.0015 percent of H, 0.10 percent of O and the balance of titanium;
2) pressing the mixture obtained in the step 1) into an electrode;
3) casting the electrode obtained in the step 2) into a ingot;
4) forging the cast ingot obtained in the step 3) into a bar blank; forging and cogging at 1100 ℃ to obtain a hot forging bar blank with the diameter phi of 180 mm;
5) hot rolling the bar billet obtained in the step 4) into a bar; hot rolling the blank at 980 ℃ to obtain a bar with the diameter of 10-100 mm;
6) cooling the bar material obtained in the step 5) to room temperature; the cooling is carried out by keeping the temperature at 800-850 ℃ for 0.5h and cooling to room temperature by water;
7) heating the bar obtained in the step 6) at 500-550 ℃, preserving heat for 1-8 hours, and then air cooling to room temperature.
2. The titanium alloy of claim 1, wherein said ingot of step 3) is melted into an ingot with a diameter of Φ 420mm in a vacuum consumable electrode furnace 3 times.
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