CN102876919B - In-situ synthesis of TiC particle reinforced titanium aluminum alloy material and its preparation method - Google Patents

Abstract

The invention discloses an in-situ synthesized TiC particle-reinforced titanium-aluminum alloy material. The composition mass percentage ratio of the titanium-aluminum alloy material is: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, and the balance For Ti and unavoidable impurities, the above alloy materials are realized by the following methods: 1) Ingredients: Weigh the corresponding amount of aluminum powder, graphite powder and titanium powder according to the above mass percentage; 2) Mix by ball milling; 3) Mix the The mixture after ball milling and sieving passes through the compact of bidirectional molding; 4) Put the green body on the cathode of the vacuum container; 5) Adjust the vacuum degree in the furnace; 6) Particle bombardment of the blank and the cathode after the argon reaches the working pressure Sintering: In the present invention, carbon replaces part of the aluminum as an alloying element and is introduced into the alloy, through the solid solution strengthening of carbon and the rapid sintering of the hollow cathode in situ reaction to introduce high melting point dispersed TiC particles to strengthen the matrix, so as to obtain high strength and wear resistance Low-cost particle reinforced titanium-aluminum alloy material.

Description

In-situ synthesis of TiC particle reinforced titanium aluminum alloy material and its preparation method

technical field

The invention relates to an in-situ synthesized TiC particle reinforced titanium-aluminum alloy material, which belongs to the technical field of powder metallurgy. The present invention also relates to a preparation method of the above-mentioned alloy material.

Background technique

Titanium is an important structural metal developed in the 1950s, with a melting point of 1670°C. Titanium alloys have been widely used as ideal aerospace engineering structural materials due to their high specific strength, high yield ratio, and good corrosion resistance.

At room temperature, titanium alloys have three matrix structures, and titanium alloys are divided into the following three categories: α alloys, (α+β) alloys and β alloys. China is represented by TA, TC, and TB respectively. According to the application, it can be divided into structural titanium alloy and high-temperature titanium alloy (use temperature greater than 400°C). The most widely used titanium alloys are industrial pure titanium (TA1, TA2 and TA3), Ti-5Al-2.5Sn (TA7) and Ti-6Al-4V (TC4), among which Ti-6Al-4V was successfully developed in the United States in 1954 Alloy, because of its good heat resistance, strength, plasticity, toughness, formability, weldability, corrosion resistance and biocompatibility, has become the trump card alloy in the titanium alloy industry. 75% to 85% of all titanium alloys.

With the rapid development of cutting-edge industrial technologies such as aviation, aerospace, and military industry, and the huge potential market demand in civilian industries such as petroleum and chemical industries, the research and development of high-performance titanium alloys has received unprecedented attention and development:

(1) High-temperature titanium alloys: The 500-600°C high-temperature titanium alloys that have been successfully used in military and civil aircraft engines are IMI829 and IMI834 alloys developed in the UK with α-phase solid solution strengthening, and the United States sacrifices fatigue strength to improve The method of creep strength developed Ti-4242S, Ti-1100 alloys, Russia's BT18Y, BT36 alloys, etc., and China developed Ti-5.3Al-4sn-2Zr-1Mo-0.25Si-1Nd (Ti55) and Ti-Al-Sn -Zr-Mo-Nb-Si-1Nd (Ti66).

(2) Structural titanium alloys are developing in the direction of high strength, high plasticity, high strength, high toughness, high modulus and high damage tolerance. ~33, the modulus of elasticity increased to 196GPa), in recent years, many new high-strength and toughness β-titanium alloys have been developed, such as Ti-10V-2Fe-3Al (Ti1023) in the United States, Ti-15V-3Cr-3Sn-3Al (Ti153), Ti-15Mo-3Al-2.7Nb-0.2Si (β21S); British Ti-4Al-4Mo-2Sn-0.5Si (IMI500), Japanese SPF00, CR800, SP700 and former Soviet Union BT22, etc.

At present, the new high-temperature titanium alloys are mainly α-titanium alloys and α+β-titanium alloys, which are generally used in the annealed state and the temperature does not exceed 600°C. α+β-titanium alloys can be strengthened by heat treatment, but their hardenability is low. The fracture toughness is also reduced, so the strength performance of the new high-temperature titanium alloy is much lower than that of the new high-strength toughness performance beta titanium alloy. However, β-titanium alloys have poor thermal stability and are not suitable for use at high temperatures. Therefore, the new titanium alloy materials developed by alloying technology through solid solution strengthening and heat treatment aging precipitation strengthening are difficult to balance high strength, toughness and heat resistance.

Adding high-strength and high-rigidity reinforcing phases to titanium alloys can further improve its specific elastic modulus, specific stiffness, mechanical properties, fatigue and creep resistance, and overcome the shortcomings of the original titanium alloys such as poor wear resistance and high temperature performance. , has become a candidate material for hypersonic spacecraft and advanced aero-engines. Compared with fiber and whisker reinforced composite materials, the preparation process of particle reinforced titanium alloy materials is simple, easy to realize, the prepared materials are isotropic, and the material properties are less sensitive to the thermal expansion coefficient mismatch between the reinforcement phase and the matrix , and more importantly, large-size parts can be prepared by traditional titanium alloy melting and processing technology, which significantly reduces the cost of materials. In the selection of particle-reinforced phase, on the one hand, in order to avoid thermal residual stress, the thermal expansion coefficient of the reinforced particle phase and the matrix should be similar; Interfacial reaction occurs, reducing the interfacial bonding strength. Currently commonly used reinforcement phases are: TiB and TiC, and rare earth oxides. Compared with the material prepared by the traditional reinforced particle phase addition method, the in-situ synthesized particle-reinforced titanium alloy material has the following advantages: the preparation process is simple, easy to realize, the prepared material is isotropic, and the material properties have no effect on the thermal expansion of the reinforcing phase and the matrix. The sensitivity to coefficient mismatch is low and mechanically stable, so the performance is not easy to degrade when working at high temperature; the interface between the reinforcement phase and the matrix is clean, and there is no interface reactant; the in-situ generated reinforcement phase is evenly distributed in the matrix, showing excellent performance. mechanical properties. For example, the State Key Laboratory of Metal Matrix Composites of Shanghai Jiaotong University prepared TiB and TiC in-situ reaction particle-reinforced titanium-aluminum alloy materials by melting and casting.

Casting and powder metallurgy technology are the main methods of preparing titanium alloy materials. Compared with casting technology, titanium alloy prepared by powder metallurgy can have near-net shape, high material utilization rate, fine grain, uniform structure and no segregation. According to survey data, in the United States, only 60-80% of the titanium parts produced by powder metallurgy are used in aviation, while the semi-finished products of titanium castings only account for 20-25%. In recent years, foreign countries have adopted rapid solidification/powder metallurgy technology and particle-reinforced titanium alloy as the development direction of new titanium alloys, and domestic powder metallurgy technology has also been used to develop in-situ synthetic particle-reinforced titanium alloy materials. A Chinese invention patent of a powder metallurgy titanium alloy and its preparation method (CN 101962721 A), proposes a powder metallurgy titanium alloy containing silver and titanium boride particles, by adding lanthanum hexaboride to the vacuum hot pressing sintered titanium alloy In situ reaction to generate titanium boride particles. Chinese invention patent CN 101696474 B proposes a powder metallurgy preparation method for titanium alloys containing rare earth oxide strengthening phase. The rare earth is added in the form of rare earth hydride powder, and the rare earth oxide strengthening phase reacts during the deformation process after vacuum sintering Oxygen is an impurity element in titanium alloys. The presence of oxygen makes the plasticity of titanium alloys decrease sharply, and its embrittlement effect is 10 times that of aluminum. When the oxygen content is greater than 0.7%, titanium completely loses the ability of plastic deformation, but This patent document does not explain the principle of the formation of rare earth oxide strengthening phase, and the formation of oxides tends to increase the content of oxygen impurities in the alloy. Titanium is an active metal, so the preparation of titanium alloy powder metallurgy parts requires very strict sintering conditions. The traditional vacuum sintering process requires a high degree of vacuum, and the sintered titanium alloy products have many residual pores, which leads to fatigue. Performance is severely degraded. In order to obtain high-performance titanium alloy powder metallurgy products, new forming and sintering processes (spray molding, powder injection molding, hot isostatic pressing, etc.) are developed to eliminate or minimize the porosity in the material. The elongation performance reaches or even exceeds the level of forging materials. However, the equipment investment required by the above-mentioned new technology is large, the process is complicated, and the manufacturing cost is high, which limits its application and development.

Contents of the invention

The technical problem to be solved by the present invention is to provide an in-situ synthesized TiC particle-reinforced titanium-aluminum alloy material and a preparation method thereof to prepare high-strength toughness and low-cost particle-reinforced titanium-aluminum alloy material.

The technical idea of the in-situ synthesis of TiC particles reinforced titanium-aluminum alloy material of the present invention is that aluminum is the most widely used α-stable element in titanium alloys, and aluminum in titanium alloys exists in the α-phase in the form of substituting atoms. The addition of aluminum can Lowering the melting point and increasing the β-transition temperature can strengthen both at room temperature and high temperature. Al promotes the interdiffusion of Ti and C during the sintering process, which is beneficial to the formation and refinement of TiC particle phase. In addition, adding aluminum can also reduce the specific gravity of the alloy. However, if the addition amount is too high, there will be α ₂ ordered solid solution based on Ti ₃ Al, which will make the alloy brittle and reduce the thermal stability.

Carbon is an interstitial α-phase stable element in titanium alloys. According to the calculation formula of aluminum equivalent of titanium alloys: aluminum equivalent=%Al+%Sn/3+%Zr/6+%Si*4+(O,C,N)% *10, its effect is 10 times that of aluminum. Carbon existing in the alpha phase in the form of interstitial atoms has a solid solution strengthening effect much higher than that of aluminum. In the present invention, carbon is introduced into the alloy as an alloying element, and the substitution effect of carbon on Al reduces the content of Al in the alloy, ensuring that the alloy It has good plasticity and toughness; high-strength and wear-resistant particle-reinforced titanium-aluminum alloy materials are obtained by introducing high-melting point dispersed TiC particles into the matrix through solid-solution strengthening of carbon and in-situ reaction of hollow cathode sintering.

The feasibility of the technical thought of the present invention is:

(1) The strength and toughness of the titanium-based alloy material is achieved by substituting carbon for part of the aluminum and controlling the in-situ reaction to generate TiC particle strengthening phase: in the alloy of the present invention, the aluminum content is reduced by substituting part of the aluminum with carbon, which ensures that the alloy has good plasticity and toughness. It is an important reason for the relatively low Al content in the alloy material of the present invention; the strength and wear resistance of the alloy are strengthened by solid solution strengthening of carbon, changing the amount of added graphite and adjusting the hollow cathode sintering process parameters to control in-situ reaction to generate TiC particles The number, size and distribution of phases can be realized. According to the Ti-C binary phase diagram, the peritectic reaction occurs at 920°C: β-Ti _0.6at%.C +TiC _38at%.C ↔α-Ti _{1.6 at%.C} , during the peritectic reaction, the The carbon atom percentage is 1.6, and its mass percentage is 0.4%.

(2) The advantage of selecting TiC particles as the reinforcing phase of the material of the present invention: compared with TiB, TiC particles have a high melting point (3433° C.), are closest to the density and thermal expansion coefficient of titanium and have the same Poisson’s ratio, tensile strength and The elastic modulus is 4 times that of titanium, and the affinity with titanium is good, and it can increase the wear resistance of titanium.

(3) Realization conditions for in-situ reaction to generate TiC particle reinforcement phase: the in-situ synthesis of TiC reinforcement phase is sintered by hollow cathode between Ti and graphite (C), and its reaction formula is: Ti+C→TiC. When selecting the reinforcement phase for in-situ generation of composite materials, it is usually judged through thermodynamic analysis whether the reinforcement phase can be automatically generated in the matrix by adding substances, and the criterion for judging is whether the change of Gibbs free energy of the reaction is less than zero. Another condition to consider is the reaction enthalpy of formation, which represents the thermal effect of the reaction. The reaction formation enthalpy △H and the Gibbs free energy △G of the reaction formula were calculated using the data in the literature. When the reaction temperature T<1939K, the formula △H and △G can be expressed as follows:

ΔH=-184571.8+5.024T-2.425×10 ^-3 T ² -1.958×10 ⁶ /T (1)

ΔG=-184571.8+41.382T-5.024TlnT+2.425×10 ^-3 T ² -9.79×10 ⁵ /T (2)

Calculation results show that within the sintering temperature range of the present invention (1250~1500°C), the standard Gibbs free energy change value (ΔG) and reaction formation enthalpy (ΔH) of the reaction are always far below zero, and the adiabatic temperature of the reaction is 3210K, exceeding The empirical criterion for the spontaneous maintenance of the reaction is Tad>2500K. This shows that the exothermic reaction can be maintained automatically, that is, a self-propagating high-temperature synthesis reaction occurs, saving energy.

(4) The advantages of TiC particle reinforcement phase synthesized by in situ reaction of hollow cathode sintering. The powder metallurgy sintering temperature is crucial to the microstructure and properties of sintered products. It is generally believed that the higher the temperature, the better the sintering effect of the sintered product. The specific manifestations are: the sintered body is more dense, the number of powder particle bonding sites increases, and the shape of the pores is rounded. However, long-term high-temperature action is also accompanied by side effects such as increased grain size and increased shrinkage of sintered parts. Hollow cathode plasma sintering is an emerging powder metallurgy sintering technology. It uses the hollow cathode effect when glow discharge is generated under vacuum conditions to generate high-density and high-energy ion bombardment on the cathode surface. The thermal effect of ion bombardment can make the cathode material It is rapidly heated to a very high temperature, its sintering temperature can reach 3000°C, and the heating rate can reach 100°C/s. Rapid heating to high temperature is conducive to the activation of grain boundary and lattice diffusion and inhibition of surface diffusion, which is beneficial to the densification process of the material, and at the same time inhibits the growth of internal grains, reduces the porosity, and enables the material to obtain a higher sintered density. The effect of rapid sintering at high temperature. In addition, hollow cathode sintering uses high-energy particles to bombard powder products to directly heat without special heating elements. Its equipment is small in size, convenient in temperature control, low in energy consumption, and has the characteristics of vacuum sintering, which can obtain high-quality sintering products. Therefore, the hollow cathode sintering technology is a good in-situ synthesized TiC particle reinforced titanium aluminum alloy material sintering method.

Based on the technical idea of the above invention, the technical solution of the present invention is: an in-situ synthesized TiC particle reinforced titanium-aluminum alloy material, the titanium-aluminum alloy material is composed of the following components in mass percentage: 0.2%≤Al≤2.5% , 0.5%≤C≤1.5%, the balance is Ti and unavoidable impurities.

The unavoidable impurity content is controlled below 0.5%. The Al and C are respectively provided by aluminum powder and graphite powder.

The preparation method (hollow cathode sintering method) of the above-mentioned in-situ synthesis of TiC particle reinforced titanium aluminum alloy material comprises the following steps:

1) Ingredients: Weigh the corresponding amount of aluminum powder, graphite powder and titanium powder according to the following mass percentage: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, and the balance is Ti; the powder particle size of the above components For: aluminum powder: 300~500 mesh, graphite powder: 800~2000 mesh, titanium powder: 300~500 mesh;

2) Ball milling and mixing: Put the above-mentioned powder into a ball milling tank according to the ball-to-material ratio of 5:1. At a speed of 250~350r/min, the ball milling tank is ball milled for 1~2h under an argon protective atmosphere, and then the ball milled mixture is passed through 100-mesh sieve specified in GB/T6005;

3) Pass the ball-milled and sieved mixture in step 2) through a bidirectional molded compact, and the molding pressure is 400-600Mpa;

4) An anode and a hollow cathode are set in the vacuum chamber. The anode is the shell of the vacuum container. The hollow cathode is composed of the above-mentioned pressed blank and a graphite plate that can play a role in heat insulation. The distance between the blanks placed on the cathode is 10~20mm;

5) Select commercially pure argon as the sputtering gas, pump the vacuum to the limit in the furnace, then fill it with high-purity argon as a protective gas, and adjust the flow of argon to make the working pressure in the furnace reach 10-50Pa;

6) After the argon gas reaches the working pressure, turn on the workpiece power supply, carry out particle bombardment on the blank and cathode, and sinter at a temperature of 1350~1550°C for 2~6 hours.

In order to get rid of the impurities in the furnace, between the step 5) and the step 6), further steps are included:

(1) Particle bombardment of the billet and cathode for 20 minutes;

(2) Adjust the air pressure to the ultimate vacuum to discharge the impurities generated by particle bombardment;

(3) If impurities still remain in the furnace cavity, continue to perform steps (1) and (2) until the sintering of the titanium alloy is fully satisfied.

The step 5) working pressure in the furnace is realized by the following methods:

(1) First turn on the mechanical pump and the molecular pump in sequence to pump the vacuum in the furnace to the limit;

(2) Then fill the protective gas with high-purity argon, and adjust the argon flow to make the pressure in the furnace reach the required working pressure;

(3) After stabilization, evacuate to the ultimate vacuum degree again, repeat the above steps until the content of impurity gases such as oxygen in the furnace reaches the minimum.

The effect of the present invention is that: the present invention breaks through the traditional thinking of using carbon as an impurity element in titanium alloys, and proposes a new idea of introducing carbon into the alloy as a beneficial alloying element. The substitution of carbon for Al reduces the amount of Al in the alloy. content to ensure that the alloy has good plasticity and toughness; through solid solution strengthening of carbon and hollow cathode sintering in situ reaction to introduce high melting point dispersed TiC particles to strengthen the matrix, obtain low-cost particle-reinforced titanium aluminum with high strength and wear resistance Alloy materials.

The invention proposes a hollow cathode sintering method to realize high-temperature rapid sintering of in-situ TiC particles reinforced titanium-aluminum alloy materials, the density of the sintered material reaches 97%, and overcomes the shortcomings of titanium alloys such as poor wear resistance and low elastic modulus. Expanding the application of titanium alloy materials in aerospace and civil industries will have a huge boost.

Detailed ways

Example 1

The preparation method (hollow cathode sintering method) of the present invention for in-situ synthesis of TiC particles reinforced titanium-aluminum alloy material comprises the following steps:

1) Ingredients: Titanium-aluminum alloy material is Ti-0.2%Al-0.5%C. Weigh 300-mesh aluminum powder, 800-mesh graphite powder and 300-mesh titanium powder according to the alloy ratio.

2) Ball milling and mixing: put the above-mentioned powder into a ball milling tank at a ball-to-material ratio of 5:1, and mill at a speed of 350r/min for 1h. In order to prevent the powder from oxidation during the ball milling process, the ball milling jar is filled with argon gas for protection. Then pass the ball-milled mixture through the 100-mesh sieve specified in GB/T6005.

3) Pass the ball-milled and sieved mixture in step 2) through a bidirectional molded compact, and the molded pressure is 400Mpa.

4) An anode and a hollow cathode are set in the vacuum chamber. The hollow cathode is composed of the above-mentioned pressed blank and a graphite plate that can play a role in heat insulation. The distance between the blanks placed on the cathode is 10mm.

5) Select commercially pure argon as the sputtering gas, evacuate the vacuum in the furnace to the limit, then fill it with high-purity argon as a protective gas, and adjust the flow rate of argon to make the pressure in the furnace reach 10Pa. For hollow cathode plasma sintering and vacuum sintering furnaces, the sintering process can only be realized under a certain working pressure. The working pressure in the furnace is achieved by the following methods:

(1) First turn on the mechanical pump and the molecular pump in sequence to pump the vacuum in the furnace to the limit;

(2) Then fill the protective gas with high-purity argon, and adjust the argon flow to make the pressure in the furnace reach the required working pressure;

(3) After stabilization, evacuate to the ultimate vacuum degree again, repeat the above steps until the content of impurity gases such as oxygen in the furnace reaches the minimum.

6) After the argon gas reaches the working pressure, turn on the workpiece power supply, carry out particle bombardment on the blank and cathode, and sinter at a temperature of 1550°C for 2 hours.

Between step 5) and step 6) above, further steps are included:

(1) Particle bombardment of the billet and cathode for 20 minutes;

(2) Adjust the air pressure to the ultimate vacuum to discharge the impurities generated by particle bombardment;

(3) If impurities still remain in the furnace cavity, continue to perform steps (1) and (2) until the sintering of the titanium alloy is fully satisfied.

The bending strength of the Ti-0.2%Al-0.5%C alloy prepared by the above method is 670Mpa, and the relative density is 94%.

Example 2

This example is the same as Example 1, except that the titanium-aluminum alloy material prepared in step 1) is Ti-0.6%Al-1.5%C. Weigh 500-mesh aluminum powder, 1500-mesh graphite powder and 500-mesh titanium powder according to the ratio of the alloy; the difference from step 2) is that the speed is 300r/min, and the ball milling time is 1.5h; the difference from step 3) is the mold used The pressure is 600Mpa; the difference from step 4) is that the distance between the blanks placed on the cathode is 20mm; the difference from step 5) is that the argon flow is adjusted to make the working pressure in the furnace reach 30Pa; the difference from step 6) It was sintered at a temperature of 1350° C. for 6 hours, and all the others were the same as in Implementation 1. The titanium-aluminum alloy material Ti-0.6%Al-1.5%C prepared by the above method has a flexural strength of 850Mpa and a relative density of 97%.

Example 3

This example is the same as Example 1, except that the titanium-aluminum alloy material prepared in step 1) is Ti-1.5%Al-1.0%C. Weigh 400-mesh aluminum powder, 2000-mesh graphite powder and 400-mesh titanium powder according to the ratio of the alloy; the difference from step 2) is that the rotation speed is 250r/min, and the ball milling time is 2h; the difference from step 3) is the molding pressure used It is 500Mpa; the difference from step 4) is that the distance between the blanks placed on the cathode is 15mm; the difference from step 5) is that the argon flow is adjusted to make the working pressure in the furnace reach 50Pa; the difference from step 6) is Sintering at a temperature of 1450° C. for 4 hours, and the rest are the same as in Embodiment 1. The titanium-aluminum alloy material Ti-1.5%Al-1.0%C prepared by the above method has a flexural strength of 780Mpa and a relative density of 95%.

Example 4

This example is the same as Example 1, except that the titanium-aluminum alloy material prepared in step 1) is Ti-2.5%Al-1.5%C. Weigh 500-mesh aluminum powder, 2000-mesh graphite powder and 400-mesh titanium powder according to the proportion of the alloy; the difference from step 2) is that the rotation speed is 300r/min, and the ball milling time is 2h; the difference from step 3) is the molding pressure used It is 450Mpa; the difference from step 4) is that the distance between the blanks placed on the cathode is 15mm; the difference from step 5) is to adjust the argon flow to make the working pressure in the furnace reach 35Pa; the difference from step 6) is Sintering at a temperature of 1480° C. for 4 hours, the rest are the same as in Implementation 1. The titanium-aluminum alloy material Ti-2.5%Al-1.5%C prepared by the above method has a flexural strength of 920Mpa and a relative density of 95%.

Claims (6)

1. the synthetic TiC granule intensified titanium aluminum alloy materials of original position, is characterized in that: described Ti-Al alloy material is made up of the component of following quality percentage: 0.2%≤Al≤2.5%, and 0.5%≤C≤1.5%, surplus is Ti and inevitable impurity.

2. the synthetic TiC granule intensified titanium aluminum alloy materials of original position according to claim 1, is characterized in that: described inevitable foreign matter content is controlled at below 0.5%.

3. the synthetic TiC granule intensified titanium aluminum alloy materials of original position according to claim 1, is characterized in that: described Al, C are provided by aluminium powder, Graphite Powder 99 respectively.

4. a preparation method for the synthetic TiC granule intensified titanium aluminum alloy materials of original position, is characterized in that comprising the following steps:

1) batching: the aluminium powder, Graphite Powder 99 and the titanium valve that take respective amount by following mass percent: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, surplus is Ti; The powder size of above-mentioned each component is: aluminium powder: 300 ~ 500 orders, Graphite Powder 99: 800 ~ 2000 orders, titanium valve: 300 ~ 500 orders;

2) ball milling mixes: above-mentioned powder is packed in ball grinder by ratio of grinding media to material 5:1, and at rotating speed 250 ~ 350r/min, ball grinder is ball milling 1 ~ 2h under argon shield atmosphere, then compound after ball milling is crossed to 100 mesh sieves of GB/T6005 regulation;

3) by step 2) in the compound of ball milling after sieving by the pressed compact of two-way mold pressing, described molding pressure is 400 ~ 600Mpa;

4) anode and hollow cathode are set in vacuum chamber, anode is vacuum vessel housing, and hollow cathode is by the above-mentioned pressed compact material of making and can play heat-blocking action graphite cake and form, and being placed on blank on negative electrode distance is each other 10 ~ 20mm;

5) choosing technical pure argon gas is sputter gas, and vacuum tightness in stove is evacuated to the limit, is then filled with shielding gas high-purity argon gas, regulates argon flow amount to make operating air pressure in stove reach 10 ~ 50Pa;

6) after argon gas reaches operating air pressure, open workpiece power supply, blank and negative electrode are carried out to particle bombardment, sintering 2 ~ 6 hours at 1350 ~ 1550 ℃ of temperature.

5. the preparation method of the synthetic TiC granule intensified titanium aluminum alloy materials of original position according to claim 4, is characterized in that: between described step 5) and step 6), also comprise step:

(1) blank and negative electrode are carried out to particle bombardment, and lasting 20min;

(2) by air pressure adjustment to final vacuum, discharge due to particle bombardment produce impurity;

(3), if still remain impurity in furnace chamber, continue execution step (1), (2), until fully meet the sintering of titanium alloy.

6. the preparation method of the synthetic TiC granule intensified titanium aluminum alloy materials of original position according to claim 4, is characterized in that: in described step 5) stove, operating air pressure is realized by following methods:

(1) open first successively mechanical pump, molecular pump, vacuum tightness in stove is evacuated to the limit;

(2) be then filled with shielding gas high-purity argon gas, regulate argon flow amount to make stove internal gas pressure reach the operating air pressure needing;

(3) after stable, be again pumped to final vacuum, repeat above-mentioned steps, until the foreign gas content such as the interior oxygen of stove reach minimum.