CN103225033A - Low-W high-Nb lamellar structure Ti-Al alloy and preparation method thereof - Google Patents
Low-W high-Nb lamellar structure Ti-Al alloy and preparation method thereof Download PDFInfo
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- CN103225033A CN103225033A CN2013101699451A CN201310169945A CN103225033A CN 103225033 A CN103225033 A CN 103225033A CN 2013101699451 A CN2013101699451 A CN 2013101699451A CN 201310169945 A CN201310169945 A CN 201310169945A CN 103225033 A CN103225033 A CN 103225033A
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Abstract
The invention discloses a low-W high-Nb lamellar structure Ti-Al alloy. The low-W high-Nb lamellar structure Ti-Al alloy comprises 45.0-48.0% of Al, 5.0-8.0% of Nb, 0.4-1.0% of W, and the balance Ti, and has a uniform fully-lamellar structure. A preparation method of the alloy comprises the following steps: burdening raw materials comprising Ti, Al, Nb and W according to the above given atom percentages; putting the burdened raw materials in an arc melting furnace, vacuumizing, filling high-purity argon, and adjusting the arc melting furnace for melting to obtain a button ingot; putting the button ingot in a suspension melting furnace, vacuumizing, filling high-purity argon, and carrying out suction casting to obtain a cylindrical test bar; and putting the cylindrical test bar in a Brdigeman directional solidification furnace, vacuumizing, filling high-purity argon, adjusting technological parameters, and carrying out directional solidification of the cylindrical test bar to obtain the low-W high-Nb lamellar structure Ti-Al alloy. The method is easy to operate, can easily realize the industrialization, allows the comprehensive properties of the high-Nb Ti-Al alloy to be breakthrough, and can be widely applied to the aerospace field, the automobile field and the like.
Description
Technical field
The invention belongs to the high performance alloys material and make field, the high niobium lamellar structure of particularly a kind of low tungsten titanium aluminum alloy and preparation method thereof.
Background technology
Along with the development of industrial circles such as aerospace, automobile, people can't further satisfy the requirement to material property pursuing more high-level efficiency and more can being subjected to the restriction of material property ultimate usually during high-performance.Therefore, the development and utilization of type material is extremely urgent.In the superalloy field, compound has low density, high fusing point, specific tenacity and hot strength and advantage such as good oxidation-resistance and creep resistance between hot metal.Therefore, the appearance of compound makes people see new hope between hot metal.People wish by the research of compound between hot metal being excavated more high-level efficiency and more high performance potentiality.Therefore, the research of compound has become in recent years in the Materials science a very active research direction between hot metal.
Between hot metal in the compound, TiAl base alloy is owing to contain metallic bond and covalent linkage in the crystal, make its mechanical property that might have metal and pottery simultaneously concurrently, and produce low density, high rigidity, specific tenacity, specific modulus, hot strength and advantages such as good oxidation-resistance and creep resistance thus.Therefore, TiAl base alloy is considered to a kind of high-temperature structural material that has application potential in other industrial circles such as space flight and aviation and automobile that can replace iron alloy and nickel-base alloy.In TiAl base alloy, δ-TiA1
3The base alloy is because the solid solution scope is too narrow, and therefore the plasticity when room temperature is poor, is difficult to mechanical workout, α
2-Ti
3A1 base alloy exist structural instability and under severe environment and cyclic loading the rimose problem, therefore research focus mainly concentrates at present
γIn the research and development of-TiAl base alloy.This class alloy generally contains 15% α
2-Ti
3A1 is double structure.Therefore, with α
2-Ti
3A1 compares, and this alloy has lower density, higher intensity and good oxidation-resistance.But because this alloy at room temperature is crisp, plasticity is relatively poor, shortcoming such as oxidation-resistance deficiency under the high temperature, thereby limited its widespread use in practice.
γThe problem that is faced in-TiAl base the alloy is how to improve its comprehensive mechanical property by control alloying constituent and microstructure, and realizes this goal as how fairly simple technology approach.Wherein microstructure is influence
γThe principal element of-TiAl base alloy mechanical property.Studies show that to have tiny and uniform lamellar structure
γ-TiAl alloy has better over-all properties.At present, mainly adopt the technology of directional freeze to improve the titanium aluminum alloy microstructure, obtain lamellar structure, make plus load be parallel to the sheet bed interface.Studies show that plus load is parallel to the sheet bed interface can obtain the comprehensive of best intensity and plasticity, so for some rotatable parts, as engine blade, make be parallel to by force direction
γ-TiAl alloy sheet interlayer orientation is the optimal selection of performance material property advantage.Directional solidification technique is the control of thermal conduction direction when solidifying by utilization, in frozen metal and solidified melt not, set up the thermograde of specific direction, reach control process of setting and solidification path, and control crystalline orientation, eliminate horizontal crystal boundary, obtain the purpose of specific lamella direction, thereby improve other mechanical properties such as its plasticity, fracture toughness property.Therefore, directional solidification technique has become domestic and international research emphasis to compound between first-generation metal, is to accelerate expansion
γ-TiAl is in the technique means of industrialized application.
Document 1(Fu Heng will, Guo Jingjie, Su Yanqing, Liu Lin, Xu Daming, the directional freeze of Li Jinshan .TiAl intermetallic compound and crystal orientation control. the China YouSe Acta Metallurgica Sinica, 2003(13): 797-809.) studies show that: if right
γ-TiAl base alloy is controlled according to the method for common directional freeze, and no matter separating out α earlier still is the β phase mutually, can't guarantee that all final lamellar structure all is parallel to the preferred growth direction of directional freeze.When primary phase is the β phase time, its preferred growth direction is (001), and lamellar structure becomes 0o or 45 with the preferred growth direction of directional freeze.When primary phase is the α phase time, its preferred growth direction is [0001], and the direction of growth of lamellar structure and directional freeze at an angle of 90.
Document 2 (Microstructure control of TiAl alloys containing
βStabilizers by directional solidification, Materials Science and Engineering. A329 – 331, (2002), 13 – 18) studies show that, legal in solidifying at Bridgeman, when nascent β separates out earlier mutually, the possibility that the final lamellar structure that obtains is parallel to the preferred growth direction only is 1/3, and there is 2/3 lamellar structure can become the 45o angle with the preferred growth direction, thereby can't obtain out all parallel lamellar structure, can not prepare alloy sample with best room temperature and high-temperature behavior with the preferred growth direction.
Document 3(Fu Heng will, Li Xinzhong, Liu Chang, Su Yanqing, Li Shuanming, outstanding .Ti-Al Peritectic Alloy directional freeze of Guo Jing and tissue are selected. the China YouSe Acta Metallurgica Sinica, 2005(15): 495-505.) studies show that, the selection of phase determines its stability in the process of setting, and this stability had both depended on the thermodynamics in process of setting, also depends on kinetics.Usually under a given curing condition, the phase that comparatively high temps generates is preferred growth (promptly the highest interface temperature hypothesis) always.Yet nonequilibrium dynamic conditions has great effect equally to the preferential growth of phase, is departing under the bigger drawing velocity of balance and can change form the interface temperature of growth mutually especially, thereby influencing the order according to qualifications of phase.For
γThe alloy directionally solidified process of-TiAl, when
V＜
V Tr The time, the interface growth temperature of β phase is higher than the α phase, so β phase preferred growth; When
V＞
V Tr The time, the interface growth temperature of α phase is higher than β, so α phase preferred growth.
Document 4 (Microstructure evolution of directionally solidified Ti – 46Al – 0.5W – 0.5Si alloy, Journal of Crystal Growth.337, (2011), 52 – 59) studies show that, legal in solidifying at Bridgeman, along with drawing velocity
VVariation, the preferred growth direction of its initial alpha phase also changes thereupon.
Document 5(Luo Wen loyalty, Shen Jun, Min Zhixian, Fu Hengzhi.
γThe control of lamellar structure orientation in the-TiAl alloy. Rare Metals Materials and engineering, 2009(38): 495-505.) studies show that, legal in solidifying at seed crystal, the primary phase of high niobium containing titanium aluminium alloy is the α phase time, the lamellar structure that all is parallel to the direction of growth through the final acquisition of solid-state phase changes, but this method will obtain α plane interface growth mutually to seed crystal in and the process of setting strict with the masterbatch composition, so required
G/VValue is big, and production efficiency is lower.
For further excavating the potentiality of alloy comprehensive mechanical property, under the prerequisite that does not influence the alloy comprehensive mechanical property, can optimize by adding alloying element
γThe performance of-TiAl base alloy, it is right to introduce alloying element below
γ-TiAl alloy structure and Effect on Performance.
Document 6(Shen Yong, Ding Xiaofei, Wang Fugang, Tan Yi, Jenn-Ming Yang. high-Nb TiAl-base alloy high-temperature oxidation resistance research. Chinese corrosion and protection journal, 2004(24): studies show that 203-207.) adding Nb in alloy is the effective ways that improve TiAl base intermetallic compound antioxidant property.With general T iAl base alloy phase ratio, high niobium Ti Al alloy is because the adding of high-melting-point constituent element Nb, improved the use temperature of alloy, high-temperature oxidation resistance and creep resistance have been improved, it is low to have density simultaneously, advantages such as crystalline structure is simple have become the important development direction of novel superpower intermetallic compound.
Document 7 (Dendrite core grain refining and interdendritic coarsening behaviour in W-containing
γ-TiAl based alloys. Journal of Alloys and Compounds, 552,2013,213 – 218) studies show that, because W elements can reduce stacking fault energy and rate of diffusion, thereby can stablize lamellar orientation; Simultaneously, W elements can also further improve performances such as intensity, thermostability, creep resistance and oxidation-resistance.But W elements will reduce alloy plasticity because diffusion slowly, generates the B2 phase.
In sum, the titanium aluminum alloy of existing method preparation has intensity and hardness is lower, oxidation-resistance and the relatively poor shortcoming of creep resistance, does not prepare uniform complete lamellar structure as yet, thus the comprehensive mechanical property of alloy a little less than, and complicated process of preparation, production efficiency is low.
Summary of the invention
The object of the present invention is to provide a kind of high niobium lamellar structure of low tungsten titanium aluminum alloy with good oxidation-resistance and creep resistance and preparation method thereof, this alloy has all parallel with direction of growth lamellar structure, and intensity and hardness are higher.
Realize that technical solution of the present invention is: the high niobium lamellar structure of a kind of low tungsten titanium aluminum alloy, described titanium aluminum alloy contains the following component of representing with atomic percent: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, all the other are titanium.
The present invention hangs down the high niobium lamellar structure of tungsten titanium aluminum alloy, and described titanium aluminum alloy has uniform complete lamellar structure.
A kind of method for preparing the high niobium lamellar structure of this low tungsten titanium aluminum alloy, step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent;
Step 2, confected materials in the step 1 is put into arc-melting furnace, vacuumize, charge into high-purity argon gas, electric current and the voltage of regulating arc-melting furnace then carry out melting, obtain the button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, vacuumize, charge into high-purity argon gas, regulate the power of suspension smelting furnace then and inhale casting, obtain cylindrical coupon;
Step 4, the cylindrical coupon of preparation in the step 3 is put into the Bridgeman directional solidification furnace, vacuumize, charge into high-purity argon gas, regulate processing parameter then, cylindrical coupon is carried out directional freeze, obtain the low high niobium lamellar structure of tungsten titanium aluminum alloy.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the atomic percent of raw material described in the step 1 is as follows: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, all the other are titanium and unavoidable impurities element.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the vacuum tightness that vacuumizes described in the step 2 is 0.01～0.03Pa, and described high-purity argon gas to the pressure that charges into is 600～650Pa.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the electric current of arc-melting furnace described in the step 2 is 200～220A, and arc-melting furnace voltage is 2～2.5V.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the vacuum tightness that vacuumizes described in the step 3 is 5～10Pa, and described high-purity argon gas to the pressure that charges into is 0.03～0.04MPa.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the power of suspension smelting furnace described in the step 3 is 20～25KW.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, and the vacuum tightness that vacuumizes described in the step 4 is 0.02～0.05Pa, and described high-purity argon gas to the pressure that charges into is 0.05～0.06Pa.
The present invention prepares the method for the high niobium lamellar structure of this low tungsten titanium aluminum alloy, processing parameter described in the step 4 comprises heating power, soaking time, drawing velocity, thermograde, wherein heating power is 25～30KW, Heating temperature is 1550～1600 ℃, soaking time is 25～30min, drawing velocity is 20～35 μ m/s, and thermograde is 10～20K/mm.
Principle of the present invention is: in low tungsten high niobium containing titanium aluminium alloy preparation process, utilize the Bridgeman method to carry out directional freeze, by improving drawing velocity
V(20～35 μ m/s) makes the primary phase (β of high niobium containing titanium aluminium alloy (Ti-(45～48) Al-(5～8) Nb-(0.4～1) W)
→α) its preferred growth direction ([0001]
→[11
0]) changes.Primary phase becomes α phase under the nonequilibrium situations mutually by the β under the equilibrium state, and the preferred growth direction also becomes [11 by [0001]
0] direction.When primary phase was β, its preferred growth direction was [001], and lamellar structure becomes 0o or 45 with the preferred growth direction of directional freeze, can not obtain all parallel with preferred growth direction lamellar structure.When primary phase is the α phase time, its preferred growth direction is [0001], lamellar structure all with the preferred growth direction of directional freeze at an angle of 90.When the preferred growth direction of primary phase is become with [0001] perpendicular [11
0] direction then can obtain all parallel with preferred growth direction lamellar structure, prepares the high niobium containing titanium aluminium alloy sample with high-performance.
Remarkable advantage compared with prior art of the present invention: 1. this alloy can obtain all parallel with preferred growth direction lamellar structure, further improves comprehensive mechanical property; 2. have performances such as good oxidation-resistance and creep resistance; 3. legal in solidifying at Bridgeman, by improving drawing velocity
VMake the primary phase and the preferred growth direction thereof of high niobium containing titanium aluminium alloy change, simple and reliable process, significantly improve preparation efficiency.
Description of drawings
Fig. 1 is the preparation flow synoptic diagram of the low high niobium lamellar structure of the tungsten titanium aluminum alloy of the present invention.
Embodiment
The present invention hangs down the high niobium lamellar structure of tungsten titanium aluminum alloy, described titanium aluminum alloy contains the following component of representing with atomic percent: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, all the other are Ti and unavoidable impurities element, and described titanium aluminum alloy has uniform complete lamellar structure.
In conjunction with the accompanying drawings 1, the present invention prepares the method for the low high niobium lamellar structure of tungsten titanium aluminum alloy, and step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent, the atomic percent of described raw material is as follows: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, and all the other are titanium, and the unavoidable impurities element;
Step 2, confected materials in the step 1 is put into arc-melting furnace, being evacuated to vacuum tightness is 0.01～0.03Pa, charging into high-purity argon gas to pressure is 600～650Pa, the electric current of regulating arc-melting furnace then is 200～220A, arc-melting furnace voltage is 2～2.5V, carry out melting, obtain the button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, being evacuated to vacuum tightness is 5～10Pa, charging into high-purity argon gas to pressure is 0.03～0.04MPa, and the power of regulating suspension smelting furnace then is that 20～25KW inhales casting, obtains cylindrical coupon;
Step 4, with in the step 3 preparation cylindrical coupon put into the Bridgeman directional solidification furnace, being evacuated to vacuum tightness is 0.02～0.05Pa, charging into high-purity argon gas to pressure is 0.05～0.06Pa, regulate processing parameter then: heating power is 25～30KW, and Heating temperature is 1550～1600 ℃, and soaking time is 25～30min, drawing velocity is 20～35 μ m/s, thermograde is 10～20K/mm, and cylindrical coupon is carried out directional freeze, obtains the low high niobium lamellar structure of tungsten titanium aluminum alloy.
Principle of the present invention is: in low tungsten high niobium containing titanium aluminium alloy preparation process, utilize the Bridgeman method to carry out directional freeze, by improving drawing velocity
V(20～35 μ m/s) makes the primary phase (β of high niobium containing titanium aluminium alloy (Ti-(45～48) Al-(5～8) Nb-(0.4～1) W)
→α) and preferred growth direction ([0001]
→[11
0]) changes.Primary phase becomes α phase under the nonequilibrium situations mutually by the β under the equilibrium state, and the preferred growth direction also becomes [11 by [0001]
0] direction.When primary phase was β, its preferred growth direction was [001], and lamellar structure becomes 0o or 45 with the preferred growth direction of directional freeze, can not obtain all parallel with preferred growth direction lamellar structure.When primary phase is the α phase time, its preferred growth direction is [0001], lamellar structure all with the preferred growth direction of directional freeze at an angle of 90.When the preferred growth direction of primary phase is become with [0001] perpendicular [11
0] direction then can obtain all parallel with preferred growth direction lamellar structure, prepares the high niobium containing titanium aluminium alloy sample with high-performance.
Embodiment 1
The preparation method of the high niobium lamellar structure of a kind of low tungsten titanium aluminum alloy, step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent, take by weighing, prepare Ti according to composition proportion
49.6Al
45Nb
5W
0.4Composition; Wherein the purity of titanium, aluminium, niobium, tungsten is 99.99%;
Step 2, confected materials in the step 1 is put into arc-melting furnace, be evacuated to 0.03Pa, charge into high-purity argon gas to 650Pa, the electric current of regulating arc-melting furnace then is that 220A, voltage are 2.5V, carries out melting with this understanding, and preparing composition is Ti
49.6Al
45Nb
5W
0.4The button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, be evacuated to 10Pa, charge into high-purity argon gas to 0.04MPa, the power of regulating suspension smelting furnace then is 25KW, be that the silica tube of Ф 4 mm is inhaled casting with diameter with this understanding, preparing composition is Ti
49.6Al
45Nb
5W
0.4Cylindrical coupon;
Step 4, with in the step 3 preparation cylindrical coupon put into the Bridgeman directional solidification furnace, take out rough vacuum earlier to 5Pa, back pumping high vacuum charges into high-purity argon gas to 0.06Pa to 0.05Pa, regulates processing parameter then, at heating power is 25KW, Heating temperature is 1550 ℃, and soaking time is 25min, and drawing velocity is 20 μ m/s, thermograde is under the condition of 10K/mm cylindrical coupon to be carried out directional freeze, obtains the low high niobium lamellar structure of tungsten titanium aluminum alloy Ti
49.6Al
45Nb
5W
0.4
Embodiment 2
The preparation method of the high niobium lamellar structure of a kind of low tungsten titanium aluminum alloy, step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent, take by weighing, prepare Ti according to composition proportion
47.3Al
46Nb
6W
0.7Composition; Wherein the purity of titanium, aluminium, niobium, tungsten is 99.99%;
Step 2, confected materials in the step 1 is put into arc-melting furnace, be evacuated to 0.02Pa, charge into high-purity argon gas to 620Pa, the electric current of regulating arc-melting furnace then is that 210A, voltage are 2.2V, carries out melting with this understanding, and preparing composition is Ti
47.3Al
46Nb
6W
0.7The button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, be evacuated to 8Pa, charge into high-purity argon gas to 0.035MPa, the power of regulating suspension smelting furnace then is 22KW, be that the silica tube of Ф 4 mm is inhaled casting with diameter with this understanding, preparing composition is Ti
47.3Al
46Nb
6W
0.7Cylindrical coupon;
Step 4, with in the step 3 preparation cylindrical coupon put into the Bridgeman directional solidification furnace, take out rough vacuum earlier to 4Pa, back pumping high vacuum charges into high-purity argon gas to 0.05Pa to 0.04Pa, regulates processing parameter then, at heating power is 28KW, Heating temperature is 1570 ℃, and soaking time is 28min, and drawing velocity is 25 μ m/s, thermograde is under the condition of 15K/mm cylindrical coupon to be carried out directional freeze, obtains the low high niobium lamellar structure of tungsten titanium aluminum alloy Ti
47.3Al
46Nb
6W
0.7
Embodiment 3
The preparation method of the high niobium lamellar structure of a kind of low tungsten titanium aluminum alloy, step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent, take by weighing, prepare Ti according to composition proportion
43Al
48Nb
8W
1Composition; Wherein the purity of titanium, aluminium, niobium, tungsten is 99.99%;
Step 2, confected materials in the step 1 is put into arc-melting furnace, be evacuated to 0.01Pa, charge into high-purity argon gas to 600Pa, the electric current of regulating arc-melting furnace then is that 200A, voltage are 2V, carries out melting with this understanding, and preparing composition is Ti
43Al
48Nb
8W
1The button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, be evacuated to 5Pa, charge into high-purity argon gas to 0.03MPa, the power of regulating suspension smelting furnace then is 20KW, be that the silica tube of Ф 4 mm is inhaled casting with diameter with this understanding, preparing composition is Ti
43Al
48Nb
8W
1Cylindrical coupon;
Step 4, with in the step 3 preparation cylindrical coupon put into the Bridgeman directional solidification furnace, take out rough vacuum earlier to 2Pa, back pumping high vacuum charges into high-purity argon gas to 0.05Pa to 0.02Pa, regulates processing parameter then, at heating power is 30KW, Heating temperature is 1600 ℃, and soaking time is 30min, and drawing velocity is 35 μ m/s, thermograde is under the condition of 20K/mm cylindrical coupon to be carried out directional freeze, obtains the low high niobium lamellar structure of tungsten titanium aluminum alloy Ti
43Al
48Nb
8W
1
The high niobium lamellar structure of the low tungsten titanium aluminum alloy of the present invention's preparation can obtain all parallel with preferred growth direction lamellar structure, further improves comprehensive mechanical property; Have performances such as good oxidation-resistance and creep resistance simultaneously; In addition, legal in solidifying at Bridgeman, by improving drawing velocity
VMake the primary phase and the preferred growth direction thereof of high niobium containing titanium aluminium alloy change, simple and reliable process, significantly improve preparation efficiency.
Claims (10)
1. the high niobium lamellar structure of low tungsten titanium aluminum alloy, it is characterized in that: described titanium aluminum alloy contains the following component of representing with atomic percent: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, all the other are titanium.
2. the high niobium lamellar structure of low tungsten according to claim 1 titanium aluminum alloy, it is characterized in that: described titanium aluminum alloy has uniform complete lamellar structure.
3. method for preparing the high niobium lamellar structure of low tungsten as claimed in claim 1 titanium aluminum alloy is characterized in that step is as follows:
Step 1, raw material titanium, aluminium, niobium, tungsten are prepared burden according to given atomic percent;
Step 2, confected materials in the step 1 is put into arc-melting furnace, vacuumize, charge into high-purity argon gas, electric current and the voltage of regulating arc-melting furnace then carry out melting, obtain the button ingot;
Step 3, with in the step 2 preparation the button ingot put into suspension smelting furnace, vacuumize, charge into high-purity argon gas, regulate the power of suspension smelting furnace then and inhale casting, obtain cylindrical coupon;
Step 4, the cylindrical coupon of preparation in the step 3 is put into the Bridgeman directional solidification furnace, vacuumize, charge into high-purity argon gas, regulate processing parameter then, cylindrical coupon is carried out directional freeze, obtain the low high niobium lamellar structure of tungsten titanium aluminum alloy.
4. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3, it is characterized in that the atomic percent of raw material described in the step 1 is as follows: aluminium 45.0%～48.0%, niobium 5.0%～8.0%, tungsten 0.4%～1.0%, all the other are titanium.
5. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3 is characterized in that the vacuum tightness that vacuumizes described in the step 2 is 0.01～0.03Pa, and described high-purity argon gas to the pressure that charges into is 600～650Pa.
6. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3 is characterized in that the electric current of arc-melting furnace described in the step 2 is 200～220A, and arc-melting furnace voltage is 2～2.5V.
7. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3 is characterized in that the vacuum tightness that vacuumizes described in the step 3 is 5～10Pa, and described high-purity argon gas to the pressure that charges into is 0.03～0.04MPa.
8. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3 is characterized in that the power of suspension smelting furnace described in the step 3 is 20～25KW.
9. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3 is characterized in that the vacuum tightness that vacuumizes described in the step 4 is 0.02～0.05Pa, and described high-purity argon gas to the pressure that charges into is 0.05～0.06Pa.
10. the method for the low high niobium lamellar structure of the tungsten titanium aluminum alloy of preparation according to claim 3, it is characterized in that, processing parameter described in the step 4 comprises heating power, soaking time, drawing velocity, thermograde, wherein heating power is 25～30KW, Heating temperature is 1550～1600 ℃, soaking time is 25～30min, and drawing velocity is 20～35 μ m/s, and thermograde is 10～20K/mm.
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| CN104878444A (en) * | 2015-05-13 | 2015-09-02 | 南京理工大学 | Preparation method of TiAl-base alloy monocrystal |
| CN106868338A (en) * | 2015-12-10 | 2017-06-20 | 南京理工大学 | Enhanced tungstenic high niobium containing titanium aluminium alloy of one kind orientation and preparation method thereof |
| CN112916831A (en) * | 2021-01-25 | 2021-06-08 | 中国科学院金属研究所 | Preparation method of gamma-TiAl alloy with lamellar interface preferred orientation and fine lamellar characteristics |
| CN114780899A (en) * | 2021-11-23 | 2022-07-22 | 兰州大学 | Method for regulating and controlling full eutectic structure and performance of non-eutectic component eutectic high-entropy alloy |
| CN114780899B (en) * | 2021-11-23 | 2024-05-14 | 兰州大学 | Method for obtaining full eutectic structure and regulating performance of eutectic high-entropy alloy with non-eutectic component |
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| CN104878444A (en) * | 2015-05-13 | 2015-09-02 | 南京理工大学 | Preparation method of TiAl-base alloy monocrystal |
| CN106868338A (en) * | 2015-12-10 | 2017-06-20 | 南京理工大学 | Enhanced tungstenic high niobium containing titanium aluminium alloy of one kind orientation and preparation method thereof |
| CN112916831A (en) * | 2021-01-25 | 2021-06-08 | 中国科学院金属研究所 | Preparation method of gamma-TiAl alloy with lamellar interface preferred orientation and fine lamellar characteristics |
| CN114780899A (en) * | 2021-11-23 | 2022-07-22 | 兰州大学 | Method for regulating and controlling full eutectic structure and performance of non-eutectic component eutectic high-entropy alloy |
| CN114780899B (en) * | 2021-11-23 | 2024-05-14 | 兰州大学 | Method for obtaining full eutectic structure and regulating performance of eutectic high-entropy alloy with non-eutectic component |
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