CN117025994A - Microalloying method, material and application for improving dynamic performance of titanium alloy - Google Patents
Microalloying method, material and application for improving dynamic performance of titanium alloy Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 165
- 238000000034 method Methods 0.000 title claims abstract description 34
- 239000000463 material Substances 0.000 title abstract description 4
- 239000000956 alloy Substances 0.000 claims abstract description 43
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 35
- 238000001816 cooling Methods 0.000 claims abstract description 27
- 238000005242 forging Methods 0.000 claims abstract description 26
- 230000007704 transition Effects 0.000 claims abstract description 20
- 239000010936 titanium Substances 0.000 claims abstract description 18
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- 235000010627 Phaseolus vulgaris Nutrition 0.000 claims abstract description 7
- 244000046052 Phaseolus vulgaris Species 0.000 claims abstract description 7
- 238000003723 Smelting Methods 0.000 claims abstract description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 238000002156 mixing Methods 0.000 claims abstract description 7
- 238000003825 pressing Methods 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 238000003466 welding Methods 0.000 claims abstract description 7
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 238000005275 alloying Methods 0.000 claims description 16
- 238000004321 preservation Methods 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 229910052746 lanthanum Inorganic materials 0.000 claims description 2
- 238000003754 machining Methods 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 230000000694 effects Effects 0.000 abstract description 13
- 239000012535 impurity Substances 0.000 abstract description 5
- 230000002411 adverse Effects 0.000 abstract description 4
- 230000009286 beneficial effect Effects 0.000 abstract description 3
- 230000003068 static effect Effects 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 238000007670 refining Methods 0.000 description 6
- 230000009466 transformation Effects 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 238000010521 absorption reaction Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 230000001276 controlling effect Effects 0.000 description 2
- 230000003993 interaction Effects 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- 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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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Abstract
The microalloying method, material and application for improving the dynamic performance of the titanium alloy fundamentally refines the grains of the TA15 titanium alloy cast ingot, reduces the adverse effect of impurity elements, and is beneficial to ensuring the structural uniformity of the TA15 titanium alloy bar, so that the titanium alloy has higher static strength and simultaneously obviously improves the dynamic performance of the titanium alloy. Comprising the following steps: (1) Mixing and pressing 0A-level sponge titanium, sponge Zr, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, stacking to form electrodes, welding the electrodes, and performing VAR smelting to form TA15 titanium alloy ingots; (2) Sequentially cogging a TA15 titanium alloy ingot in a single-phase region at 100-200 ℃ above a phase transition point and forging in a two-phase region at 20-50 ℃ below the phase transition point to obtain a forged TA15 titanium alloy bar blank; (3) And (3) preserving the temperature of the TA15 titanium alloy bar blank at 840 ℃ for 2-6 hours, cooling to 500 ℃ in a furnace, and air-cooling to obtain the TA15 titanium alloy bar.
Description
Technical Field
The application relates to the technical field of titanium alloy preparation, in particular to a micro-alloying method for improving the dynamic performance of titanium alloy, and a titanium alloy material manufactured by the micro-alloying method for improving the dynamic performance of titanium alloy and application thereof.
Background
The titanium alloy is stable, light, corrosion-resistant and high-low temperature-resistant, is the most ideal material for equipment, is widely applied to manufacturing gun towers, gun barrels, hatches, missile warheads and the like, and has been widely applied to the field of equipment by military countries such as Meinarussia, and the like, for example, the titanium alloy is applied to M1 'Aibrahm' main battle tanks and M2 'Bradyde' war carts in the United states, so that the maneuverability and the elastic resistance of the war carts are effectively improved; AGM-848H in the United states, a 'battle axe' cruise missile, an inter-continental missile of Ming soldier, an 'X-31A' of Russian, an 'Marscott' supersonic speed anti-naval missile and the like also use titanium alloy, so that the weight of the missile is effectively lightened, the loading ratio is improved, and the striking capacity is improved.
The TA15 titanium alloy belongs to near alpha titanium alloy with high Al equivalent, has good heat resistance, processability and strong shock resistance, and is applied to parts such as armor plates, missile warheads and the like under high-speed impact. Standard TA15 titanium alloy at 10 -3 Dynamic strength at/s level strain rate is less than 1500MPa, dynamic plasticity is less than 0.25, and impact absorption energy is less than 360J/cm -3 . With the increasing tactical index requirements of protective armor and new generation missiles for a variety of targets, there is an urgent need to further improve impact resistance at high strain rates of TA15 titanium alloys (10 -3 The dynamic strength at the/s level strain rate is more than or equal to 1600MPa, the dynamic plasticity is more than or equal to 0.27, and the impact absorption energy is more than or equal to 410J/cm -3 ). A great deal of research work is also being carried out at home and abroad,the high strain rate impact resistance of the alloy is generally adjusted by regulating and controlling the structure, however, the plasticity and the strength of the alloy are typical contradictors, the strength is necessarily reduced while the plasticity is improved, and vice versa, and the factors required to be controlled for forging and subsequent heat treatment are more, the flow is long, and the process is complex.
Disclosure of Invention
In order to overcome the defects of the prior art, the technical problem to be solved by the application is to provide a microalloying method for improving the dynamic performance of the titanium alloy, which radically refines TA15 titanium alloy cast ingot grains, reduces adverse effects of impurity elements, and is beneficial to ensuring the structural uniformity of TA15 titanium alloy bars, so that the alloy has higher static strength and simultaneously obviously improves the dynamic performance of the titanium alloy.
The technical scheme of the application is as follows: the micro-alloying method for improving the dynamic performance of the titanium alloy comprises the following steps:
(1) Mixing and pressing 0A-level sponge titanium, sponge Zr, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, stacking to form electrodes, welding the electrodes, and performing VAR smelting to form TA15 titanium alloy ingots;
(2) Sequentially cogging a TA15 titanium alloy ingot in a single-phase region at 100-200 ℃ above a phase transition point and forging in a two-phase region at 20-50 ℃ below the phase transition point to obtain a forged TA15 titanium alloy bar blank;
(3) And (3) preserving the temperature of the TA15 titanium alloy bar blank at 840 ℃ for 2-6 hours, cooling to 500 ℃ in a furnace, and air-cooling to obtain the TA15 titanium alloy bar.
The interstitial alloying element O and the eutectoid alloying element Fe can obviously improve the strength level of the titanium alloy, but can also have adverse effect on the plasticity of the titanium alloy. The application adopts a microalloying method and 0A grade titanium sponge to realize the aim of strictly controlling the low content of O element and Fe element in TA15 titanium alloy. On the basis, la element is added, the low solubility of La element in TA15 titanium alloy is utilized to reduce the melting point at the solid-liquid interface, promote the nucleation process and increase the nucleation rate, fundamentally refine the crystal grains of TA15 titanium alloy cast ingots and reduce the forging heat; in addition, la element can be adsorbed at the grain boundary through strong interaction with O element, fe element and Si element in the alloy, the impurity element content in the alloy is reduced, the growth of crystal grains is hindered, the effect of refining the crystal grains is achieved, and the precipitation has strong pinning effect relative to the grain boundary, so that the strength of the alloy is ensured. Therefore, the dynamic performance of the TA15 titanium alloy is remarkably improved.
A titanium alloy material manufactured by the micro-alloying method for improving the dynamic performance of the titanium alloy is also provided.
Also provides the application of the titanium alloy material in preparing equipment.
Drawings
FIG. 1a shows the macroscopic morphology of a TA15 titanium alloy 3 ton grade ingot riser prepared in accordance with the embodiment of the present application.
FIG. 1b shows the microscopic morphology of a bar of 200mm in diameter of TA15 titanium alloy prepared in accordance with the first embodiment of the present application.
Fig. 2a shows the macroscopic morphology of a riser of a 5 ton grade TA15 titanium alloy ingot prepared in example two of the present application.
Fig. 2b shows the microscopic morphology of a TA15 titanium alloy Φ300mm gauge bar prepared according to example two of the present application.
Fig. 3a shows the macroscopic morphology of a 7 ton grade cast riser of TA15 titanium alloy prepared in example three of the present application.
Fig. 3b shows the microscopic morphology of a TA15 titanium alloy Φ300mm gauge bar prepared in example three of the present application.
FIG. 4 is a flow chart of a method of microalloying to improve dynamic properties of titanium alloys in accordance with the present application.
Detailed Description
As shown in fig. 4, the micro-alloying method for improving the dynamic performance of the titanium alloy comprises the following steps:
(1) Mixing and pressing 0A-level sponge titanium, sponge Zr, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, stacking to form electrodes, welding the electrodes, and performing VAR smelting to form TA15 titanium alloy ingots;
(2) Sequentially cogging a TA15 titanium alloy ingot in a single-phase region at 100-200 ℃ above a phase transition point and forging in a two-phase region at 20-50 ℃ below the phase transition point to obtain a forged TA15 titanium alloy bar blank;
(3) And (3) preserving the temperature of the TA15 titanium alloy bar blank at 840 ℃ for 2-6 hours, cooling to 500 ℃ in a furnace, and air-cooling to obtain the TA15 titanium alloy bar.
The interstitial alloying element O and the eutectoid alloying element Fe can obviously improve the strength level of the titanium alloy, but can also have adverse effect on the plasticity of the titanium alloy. The application adopts a microalloying method and adopts 0A-level titanium sponge with low content of O element and Fe element to realize the control of low mass percentages of the O element and the Fe element in the TA15 titanium alloy. On the basis, la element is added, the low solubility of La element in TA15 titanium alloy is utilized to reduce the melting point at the solid-liquid interface, promote the nucleation process and increase the nucleation rate, fundamentally refine the crystal grains of TA15 titanium alloy cast ingots and reduce the forging heat; in addition, la element can be adsorbed at the grain boundary through strong interaction with O element, fe element and Si element in the alloy, the impurity element content in the alloy is reduced, the growth of crystal grains is hindered, the effect of refining the crystal grains is achieved, and the precipitation has strong pinning effect relative to the grain boundary, so that the strength of the alloy is ensured. Therefore, the dynamic performance of the TA15 titanium alloy is remarkably improved.
Preferably, in the step (1), the TA15 titanium alloy ingot is composed of the following components in percentage by mass: 5.1 to 7.1 percent of Al, 0.5 to 2.5 percent of Mo, 0.8 to 2.5 percent of V, 1.5 to 2.5 percent of Zr, 0.05 to 0.25 percent of La, less than or equal to 0.06 percent of Fe, less than or equal to 0.01 percent of Si, less than or equal to 0.06 percent of O, less than or equal to 0.02 percent of C, less than or equal to 0.01 percent of N, less than or equal to 0.03 percent of H, and the balance of Ti.
Preferably, in the step (1), the granularity of the grade 0A titanium sponge is 3-12.7 mm.
Preferably, in the step (2), the cooling speed of cooling along with the furnace is 0.5 ℃/min-2 ℃/min.
Preferably, in the step (1), the TA15 titanium alloy ingot is composed of the following components in percentage by mass: 6.95% of Al, 2.0% of Mo, 2.35% of V, 2.35% of Zr, 0.08% of La, 0.04% of Fe, 0.008% of Si, 0.04% of O, 0.01% of C, 0.008% of N, 0.001% of H and the balance of Ti; in the step (2), a TA15 titanium alloy 3-ton cast ingot is subjected to 2-fire single-phase region cogging forging at 100-200 ℃ above a phase transition point, and is subjected to 4-fire two-phase region drawing forging at 20-50 ℃ below the phase transition point in sequence, so as to obtain a forged TA15 titanium alloy bar blank with the specification of phi 100 mm; in the step (3), the TA15 titanium alloy bar blank is subjected to furnace cooling to 500 ℃ after heat preservation for 1.5 hours at 840 ℃, and is subjected to air cooling, so that the TA15 titanium alloy bar is obtained.
Or in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: 7.05% of Al, 2.42% of Mo, 2.33% of V, 2.43% of Zr, 0.14% of La, 0.04% of Fe, 0.007% of Si, 0.035% of O, 0.01% of C, 0.007% of N, 0.001% of H and the balance of Ti; in the step (2), a TA15 titanium alloy 5-ton cast ingot is sequentially subjected to 2-fire single-phase region cogging at 100-200 ℃ above a phase transition point, 3-fire two-phase region upsetting forging and 2-fire two-phase region drawing forging at 20-50 ℃ below the phase transition point, and a forging state TA15 titanium alloy bar blank with the specification of phi 300mm is obtained; in the step (3), the TA15 titanium alloy bar blank is subjected to heat preservation at 840 ℃ for 4 hours, and then air cooling is carried out to obtain the TA15 titanium alloy bar.
Or in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: 6.97% of Al, 1.93% of Mo, 2.47% of V, 2.30% of Zr, 0.22% of La, 0.05% of Fe, 0.03% of O, 0.01% of C, 0.007% of N, 0.003% of H and the balance of Ti; in the step (2), a TA15 titanium alloy 7-ton cast ingot is subjected to single-phase region cogging at 100-200 ℃ above a phase transition point and two-phase region forging at 20-50 ℃ below the phase transition point in sequence to obtain a forged TA15 titanium alloy bar blank with the specification of phi 300 mm; in the step (3), the TA15 titanium alloy bar blank is subjected to furnace cooling to 500 ℃ after heat preservation for 4 hours at 840 ℃, and is subjected to air cooling and then is subjected to machining to obtain the TA15 titanium alloy bar.
A titanium alloy material manufactured by the micro-alloying method for improving the dynamic performance of the titanium alloy is also provided.
Also provides the application of the titanium alloy material in preparing equipment.
Compared with the prior art, the rolling method of the titanium alloy material has the following beneficial effects:
(1) The microalloying method adopted by the method controls the mass percent of O in the TA15 titanium alloy to be less than or equal to 0.06 percent and the mass percent of Fe to be less than or equal to 0.06 percent. Meanwhile, la element with the mass percentage of 0.05-0.25% is added, and the La element can be strongly interacted with O element, fe element and Si element in the alloy to be adsorbed at the grain boundary, so that the impurity element content in the alloy is reduced, the growth of grains is hindered to achieve the effect of refining the grains, and the precipitates have strong pinning effect relative to the grain boundary, thereby ensuring the strength of the alloy.
(2) According to the application, the alloy composition design is optimized, and the proper amount of La element is added into the TA15 titanium alloy to refine the crystal grains of the cast ingot, so that the deformation of the alloy is more sufficient and uniform, and the structural uniformity of the bar of the TA15 titanium alloy is ensured.
(3) The method of the application obviously improves the dynamic performance of the TA15 titanium alloy on the premise of ensuring the strength. The strength and dynamic plasticity are well matched. The static tensile strength of the prepared TA15 titanium alloy is more than or equal to 980MPa, the dynamic strength is more than or equal to 1600MPa, the dynamic plasticity is more than or equal to 0.27, and the impact absorption energy is more than or equal to 410J/cm -3 。
Specific embodiments of the present application are described in detail below.
Example 1
The method of the present embodiment comprises the steps of:
step one, mixing 0A-level sponge titanium, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, pressing, stacking to form electrodes, welding the electrodes, and then performing VAR smelting to form TA15 titanium alloy ingots; the TA15 titanium alloy cast ingot comprises the following components in percentage by mass: 6.95% of Al, 2.0% of Mo, 2.35% of V, 2.35% of Zr, 0.08% of La, 0.04% of Fe, 0.008% of Si, 0.04% of O, 0.01% of C, 0.008% of N, 0.001% of H and the balance of Ti. The granularity of the 0A-level titanium sponge is 3-12.7 mm.
Step two, sequentially performing cogging forging on the TA15 titanium alloy 3-ton cast ingot prepared in the step one in a 2-fire single-phase region at 100-200 ℃ above the transformation point, and performing drawing forging on the TA15 titanium alloy in a 4-fire two-phase region at 20-50 ℃ below the transformation point to obtain a forged TA15 titanium alloy bar blank with the specification of phi 100 mm.
And thirdly, preserving the temperature of the TA15 titanium alloy bar blank prepared in the second step for 1.5 hours at 840 ℃, cooling to 500 ℃ in a furnace, and adding the TA15 titanium alloy bar after air cooling.
The mechanical performance parameters of the TA15 titanium alloy bars prepared in the embodiment are shown in table 1.
TABLE 1
As can be seen from Table 1, the strength and plasticity of the TA15 titanium alloy obtained in this example are superior to those of the comparative example prepared from the conventional components, and the TA15 titanium alloy has good strength and dynamic plasticity matching property. The 1/2R of the riser of the example 1 and the riser of the comparative example are subjected to grain size statistics, and as can be seen from FIG. 1a, the grains on the surface of the riser of the TA15 titanium alloy cast ingot prepared in the example 1 are fine and uniform, the size is 0.3-1.5 cm, and compared with the conventional components, the grain size of the riser of the TA15 titanium alloy cast ingot prepared in the example 1 has larger size span, the size is 0.2-3.5 cm, and the obvious refining effect is shown; from fig. 1b, it can be seen that the microstructure of the TA15 titanium alloy bar prepared in example 1 is very fine, uniform and free of precipitation of La, the content of equiaxed alpha phase is 30-45%, the size is 4-9 micrometers, and compared with the content of equiaxed alpha phase in the conventional TA15 titanium alloy bar prepared by using the conventional components, the content of equiaxed alpha phase is 45-55%, and the size is 10-35 micrometers, which indicates that the grain size of the TA15 titanium alloy can be significantly refined by adopting the microalloying method of the application, and the existence state of La element in the TA15 titanium alloy matrix is unchanged during forging and heat treatment.
Example two
The method of the present embodiment comprises the steps of:
step one, mixing 0A-level sponge titanium, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, pressing, stacking to form electrodes, welding the electrodes, and then performing VAR smelting to form TA15 titanium alloy ingots; the TA15 titanium alloy cast ingot comprises the following components in percentage by mass: 7.05% of Al, 2.42% of Mo, 2.33% of V, 2.43% of Zr, 0.14% of La, 0.04% of Fe, 0.007% of Si, 0.035% of O, 0.01% of C, 0.007% of N, 0.001% of H and the balance of Ti. The granularity of the 0A-level titanium sponge is 3-12.7 mm.
Step two, sequentially cogging a TA15 titanium alloy 5-ton cast ingot prepared in the step one in a 2-fire single-phase region at 100-200 ℃ above a transformation point, upsetting and forging in a 3-fire two-phase region and drawing and forging in a 2-fire two-phase region at 20-50 ℃ below the transformation point, and obtaining a forged TA15 titanium alloy bar blank with the specification of phi 300 mm.
And thirdly, preserving the temperature of the TA15 titanium alloy bar blank prepared in the second step for 4 hours at 840 ℃, and then air-cooling to obtain the TA15 titanium alloy bar.
The mechanical property parameters of the TA15 titanium alloy bars prepared in the example are shown in Table 2.
TABLE 2
As can be seen from Table 2, the strength and plasticity of the TA15 titanium alloy obtained in the example are superior to those of the comparative example prepared by the traditional components, and the TA15 titanium alloy has good strength and dynamic plasticity matching property. The 1/2R of the riser of the example 2 and the riser of the comparative example are subjected to grain size statistics, and as can be seen from FIG. 2a, the grains on the surface of the riser of the TA15 titanium alloy cast ingot prepared in the example 2 are fine and uniform, the size is 0.2-1.0 cm, and compared with the conventional components, the surface of the riser of the TA15 titanium alloy cast ingot prepared in the conventional components has larger grain span, the size is 0.2-3.5 cm, and the obvious refining effect is shown; from fig. 2b, it can be seen that the microstructure of the TA15 titanium alloy bar prepared in example 2 is very fine, uniform and free of precipitation of La, the content of the equiaxed alpha phase is 30-45%, the size is 4-8 micrometers, and compared with the content of the equiaxed alpha phase in the conventional TA15 titanium alloy bar prepared by the conventional components, the content of the equiaxed alpha phase is 45-55%, and the size is 10-35 micrometers, which indicates that the grain size of the TA15 titanium alloy can be significantly refined by adopting the microalloying method of the application, and the existence state of La element in the TA15 titanium alloy matrix is not changed during forging and heat treatment.
Example III
The method of the present embodiment comprises the steps of:
step one, mixing 0A-level sponge titanium, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, pressing, stacking to form electrodes, welding the electrodes, and then performing VAR smelting to form TA15 titanium alloy ingots; the TA15 titanium alloy cast ingot comprises the following components in percentage by mass: 6.97% of Al, 1.93% of Mo, 2.47% of V, 2.30% of Zr, 0.22% of La, 0.05% of Fe, 0.03% of O, 0.01% of C, 0.007% of N, 0.003% of H and the balance of Ti. The granularity of the 0A-level titanium sponge is 3-12.7 mm.
Step two, cogging a single-phase region of the TA15 titanium alloy 7-ton cast ingot prepared in the step one at 100-200 ℃ above the transformation point and forging a two-phase region of the cast ingot at 20-50 ℃ below the transformation point in sequence to obtain a forged TA15 titanium alloy bar blank with the specification of phi 300 mm.
And thirdly, preserving the temperature of the TA15 titanium alloy bar blank prepared in the second step for 4 hours at 840 ℃, cooling to 500 ℃ in a furnace, and adding the TA15 titanium alloy bar after air cooling.
The mechanical property parameters of the TA15 titanium alloy bars prepared in the example are shown in Table 3.
TABLE 3 Table 3
As can be seen from Table 3, the strength and plasticity of the TA15 titanium alloy obtained in this example are superior to those of the comparative examples prepared from the conventional components, and the TA15 titanium alloy has good strength and dynamic plasticity matching property. As can be seen from Table 3, the strength and plasticity of the TA15 titanium alloy obtained in this example are superior to those of the comparative example prepared from the conventional components, and the TA15 titanium alloy has good strength and dynamic plasticity matching property. The 1/2R of the riser of the example 3 and the riser of the comparative example are subjected to grain size statistics, and as can be seen from FIG. 3a, the grains on the surface of the riser of the TA15 titanium alloy cast ingot prepared in the example 3 are fine and uniform, the size is 0.1-0.8 cm, and compared with the conventional components, the surface of the riser of the TA15 titanium alloy cast ingot prepared in the conventional components has larger grain span, the size is 0.2-3.5 cm, and the obvious refining effect is shown; from fig. 3b, it can be seen that the microstructure of the TA15 titanium alloy bar prepared in example 3 is very fine, uniform and free of precipitation of La, the content of the equiaxed alpha phase is 30-45%, the size is 2-8 micrometers, and compared with the content of the equiaxed alpha phase in the conventional TA15 titanium alloy bar prepared by the conventional components, the content of the equiaxed alpha phase is 45-55%, and the size is 10-35 micrometers, which indicates that the grain size of the TA15 titanium alloy can be significantly refined by adopting the microalloying method of the application, and the existence state of La element in the TA15 titanium alloy matrix is not changed during forging and heat treatment.
The present application is not limited to the preferred embodiments, but can be modified in any way according to the technical principles of the present application, and all such modifications, equivalent variations and modifications are included in the scope of the present application.
Claims (9)
1. The micro-alloying method for improving the dynamic performance of the titanium alloy is characterized by comprising the following steps of: which comprises the following steps:
(1) Mixing and pressing 0A-level sponge titanium, sponge Zr, al-Mo intermediate alloy, al-V intermediate alloy, aluminum beans and Al-La intermediate alloy, stacking to form electrodes, welding the electrodes, and performing VAR smelting to form TA15 titanium alloy ingots;
(2) Sequentially cogging a TA15 titanium alloy ingot in a single-phase region at 100-200 ℃ above a phase transition point and forging in a two-phase region at 20-50 ℃ below the phase transition point to obtain a forged TA15 titanium alloy bar blank;
(3) And (3) preserving the temperature of the TA15 titanium alloy bar blank at 840 ℃ for 2-6 hours, cooling to 500 ℃ in a furnace, and air-cooling to obtain the TA15 titanium alloy bar.
2. The method for micro-alloying for improving dynamic properties of a titanium alloy according to claim 1, wherein: in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: 5.1 to 7.1 percent of Al, 0.5 to 2.5 percent of Mo, 0.8 to 2.5 percent of V, 1.5 to 2.5 percent of Zr, 0.05 to 0.25 percent of La, less than or equal to 0.06 percent of Fe, less than or equal to 0.01 percent of Si, less than or equal to 0.06 percent of O, less than or equal to 0.02 percent of C,
n is less than or equal to 0.01%, H is less than or equal to 0.03%, and the balance is Ti.
3. The method for micro-alloying for improving dynamic properties of a titanium alloy according to claim 2, wherein: in the step (1), the granularity of the 0A grade titanium sponge is 3-12.7 mm.
4. A microalloying method for improving dynamic properties of titanium alloys according to claim 3, wherein: in the step (2), the cooling speed of cooling along with the furnace is 0.5-2 ℃/min.
5. The method for micro-alloying for improving dynamic properties of a titanium alloy according to claim 1, wherein: in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: 6.95% of Al, 2.0% of Mo, 2.35% of V, 2.35% of Zr, 0.08% of La, 0.04% of Fe, 0.008% of Si, 0.04% of O, 0.01% of C, 0.008% of N, 0.001% of H and the balance of Ti; in the step (2), a TA15 titanium alloy 3-ton cast ingot is subjected to 2-fire single-phase region cogging forging at 100-200 ℃ above a phase transition point, and is subjected to 4-fire two-phase region drawing forging at 20-50 ℃ below the phase transition point in sequence, so as to obtain a forged TA15 titanium alloy bar blank with the specification of phi 100 mm; in the step (3), the TA15 titanium alloy bar blank is subjected to furnace cooling to 500 ℃ after heat preservation for 1.5 hours at 840 ℃, and is subjected to air cooling, so that the TA15 titanium alloy bar is obtained.
6. The method for micro-alloying for improving dynamic properties of a titanium alloy according to claim 1, wherein: in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: 7.05% of Al, 2.42% of Mo, 2.33% of V, 2.43% of Zr, 0.14% of La, 0.04% of Fe, 0.007% of Si, 0.035% of O, 0.01% of C, 0.007% of N, 0.001% of H and the balance of Ti; in the step (2), a TA15 titanium alloy 5-ton cast ingot is sequentially subjected to 2-fire single-phase region cogging at 100-200 ℃ above a phase transition point, 3-fire two-phase region upsetting forging and 2-fire two-phase region drawing forging at 20-50 ℃ below the phase transition point, and phi 300mm is obtained
A standard forged TA15 titanium alloy bar stock; in the step (3), the TA15 titanium alloy bar blank is subjected to heat preservation at 840 ℃ for 4 hours, and then air cooling is carried out to obtain the TA15 titanium alloy bar.
7. The method for micro-alloying for improving dynamic properties of a titanium alloy according to claim 1, wherein: in the step (1), the TA15 titanium alloy cast ingot consists of the following components in percentage by mass: al 6.97%, mo 1.93%, V2.47%, zr 2.30%, la 0.22%,
0.05% of Fe, 0.03% of O, 0.01% of C, 0.007% of N, 0.003% of H and the balance of Ti;
in the step (2), a TA15 titanium alloy 7-ton cast ingot is subjected to single-phase region cogging at 100-200 ℃ above a phase transition point and two-phase region forging at 20-50 ℃ below the phase transition point in sequence to obtain a forged TA15 titanium alloy bar blank with the specification of phi 300 mm; in the step (3), the TA15 titanium alloy bar blank is subjected to furnace cooling to 500 ℃ after heat preservation for 4 hours at 840 ℃, and is subjected to air cooling and then is subjected to machining to obtain the TA15 titanium alloy bar.
8. A titanium alloy material produced by the microalloying method for improving dynamic properties of a titanium alloy according to any one of claims 1 to 7.
9. Use of the titanium alloy material according to claim 8 in manufacturing equipment.
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