CN102876921A - TiC-particle-reinforced titanium-aluminum-molybdenum alloy material by in-situ synthesis and preparation method thereof - Google Patents
TiC-particle-reinforced titanium-aluminum-molybdenum alloy material by in-situ synthesis and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a TiC-particle-reinforced titanium-aluminum-molybdenum alloy material by in-situ synthesis. The alloy material comprises, by mass, 0.2%<=Al<=2.5%, 0.5%<=C<=1.5%, 2.5%<=Mo<=3% and the balance Ti and inevitable impurities. The alloy material is prepared according to a method including: 1) compounding by weighing powdered aluminum, graphite powder, molybdenum powder and titanium powder of a corresponding quantity according to the mass percent; 2) ball-milling and mixing; 3) pressing mixture subjected to ball milling and sieving by means of bidirectional mould pressing; 4) placing a green pressing on a cathode of a vacuum container; 5) regulating the vacuum degree in a furnace; and 6) performing particle bombardment sintering for the pressing and the cathode after argon gas reaches the working gas pressure. Carbon substitutes for part of aluminum to serve as an alloying element to be introduced to alloy, and a means that high-melting-point dispersed TiC particle phases are introduced to reinforce a matrix by solid solution strengthening of C and hollow cathode rapid sintering in-situ reaction, so that the TiC-particle-reinforced titanium-aluminum-molybdenum alloy material which is high in strength and wear resistance and low in cost is obtained.
Description
Technical field
The present invention relates to the synthetic TiC granule intensified titanium-aluminium of a kind of original position-molybdenum alloy material, belong to powder metallurgical technology.The invention still further relates to the preparation method of above-mentioned alloy material.
Background technology
Titanium is a kind of important structural metal that grows up the 1950's, and its fusing point is 1670 ℃.The titanium alloy characteristics such as specific tenacity is high, yield tensile ratio is high because having, solidity to corrosion is good become desirable aerospace engineering structured material and obtain to use widely.
Under the room temperature, titanium alloy has three kinds of matrix, and titanium alloy also just is divided into following three classes: α alloy, (alpha+beta) alloy and beta alloy.China represents with TA, TC, TB respectively.Can be divided into structural titanium alloy and high-temperature titanium alloy (use temperature is greater than 400 ℃) by purposes.Present most popular titanium alloy is industrially pure titanium (TA1, TA2 and TA3), Ti-5Al-2.5Sn (TA7) and Ti-6Al-4V (TC4), the Ti-6Al-4V alloy succeeded in developing of the U.S. in 1954 wherein, because its thermotolerance, intensity, plasticity, toughness, plasticity, weldability, solidity to corrosion and biocompatibility are all better, and becoming trump alloy in the titanium alloy industry, this alloy usage quantity has accounted for 75%～85% of whole titanium alloys.
Along with the great market potential demand in the civilian industry fields such as the develop rapidly of the sophisticated industry technology such as aviation, aerospace, military project and petroleum and petrochemical industries, the research and development of Ti alloy with high performance are subject to unprecedented the attention and development:
(1) high-temperature titanium alloy: successfully be applied in the IMI829 with the solution strengthening of α phase, IMI834 alloy that 500 ~ 600 ℃ of high-temperature titanium alloys in the dual-use aircraft engine have Britain to develop at present, Americanologist is crossed and is sacrificed method exploitation Ti-4242S, the Ti-1100 alloy that fatigue strength improves creep strength, Muscovite BT18Y, BT36 alloy etc., China has developed Ti-5.3Al-4sn-2Zr-1Mo-0.25Si-1Nd (Ti55) and Ti-Al-Sn-Zr-Mo-Nb-Si-1Nd (Ti66).
(2) structural titanium alloy is to high-strength, high-ductility, high-strength and high ductility, high-modulus and high damage tolerance future development, the requirement of high strength and toughness (is increased to 1275～1373MPa such as intensity in order to adapt to more, specific tenacity is increased to 29～33, Young's modulus is increased to 196GPa), in recent years developed the tough performance beta-titanium alloy of many novel high-strengths, such as the Ti-10V-2Fe-3Al (Ti1023) of the U.S., Ti-15V-3Cr-3Sn-3Al (Ti153), Ti-15Mo-3Al-2.7Nb-0.2Si (β 21S); The Ti-4Al-4Mo-2Sn-0.5Si of Britain (IMI500), the BT22 of SPF00, CR800, SP700 and the USSR (Union of Soviet Socialist Republics) of Japan etc.
The new type high temperature titanium alloy mainly is alpha titanium alloy and alpha+beta titanium alloys at present, generally use and temperature are no more than 600 ℃ under as-annealed condition, alpha+beta titanium alloys can be heat-treated reinforcement, but hardening capacity is lower, fracture toughness property also reduces after strengthening thermal treatment, so the strength property of new type high temperature titanium alloy is far below the tough performance beta-titanium alloy of novel high-strength.Yet the beta-titanium alloy thermostability is relatively poor, should not at high temperature use.Therefore, adopt at present alloying process to be difficult to take into account high-strong toughness energy and resistance toheat by the new titanium alloy material of solution strengthening and the exploitation of thermal treatment Precipitation reinforcement means.
The wild phase that adds high strength, high rigidity in titanium alloy can further improve it than Young's modulus, specific rigidity, mechanical property, fatigue and creep resisting ability, and overcome the shortcomings such as former titanium alloy wear resistance and high-temperature behavior be poor, become the candidate material of superelevation velocity of sound aerospace vehicle and advanced aero engine.Compare with metal whisker reinforced composite with fiber, preparation technology is simple for the granule intensified titanium alloy material, easily realize, prepared material isotropy, and material property is also lower to the susceptibility of the coefficient of thermal expansion mismatch of wild phase and matrix, the more important thing is and to prepare large-scale part with traditional titanium alloy melting and complete processing, significantly reduce the cost of material.On particulates reinforcements was selected, on the one hand for avoiding hot unrelieved stress, the thermal expansivity of enhanced granule phase and matrix should be close; The chemical compatibility of enhanced granule phase and matrix is good on the other hand, to avoid under the hot conditions and titanium alloy substrate generation surface reaction, reduces interface bond strength.Wild phase commonly used has at present: TiB and TiC, and rare earth oxide etc.Adding mutually the material that method makes with traditional enhanced granule compares, original position synthesis particle strengthens titanium alloy material following advantage: preparation technology is simple, easily realize, prepared material isotropy, and material property is low to the susceptibility of the coefficient of thermal expansion mismatch of wild phase and matrix, stable on the mechanics, therefore when hot operation, performance is difficult for degenerating; The interface of wild phase and matrix is clean, does not have the surface reaction thing; Generated in-situ wild phase is evenly distributed in matrix, shows good mechanical property.For example, Shanghai Communications University's metal-base composites National Key Laboratory adopts fusion casting to prepare TiB and TiC reaction in－situ granule intensified titanium aluminum alloy materials.
Casting and powder metallurgy technology are the main method of preparation titanium alloy material, compare with foundry engieering, and the titanium alloy of powder metallurgy preparation can form shape closely only, and material use efficiency is high, and crystal grain is tiny, homogeneous microstructure, segregation-free.Data shows according to investigations, and the U.S. only aviation accounts for 60 ~ 80% with the titanium part that adopts powder metallurgy process production, and the titanium casting work in-process only account for 20 ~ 25%.In recent years abroad the developing direction that adopts rapid solidification/powder metallurgy technology, granule intensified titanium alloy as new titanium alloy, domesticly also adopt powder metallurgy technology to develop original position synthesis particle to strengthen titanium alloy material.A kind of powder metallurgy titanium alloy of Chinese invention patent and preparation method thereof (CN 101962721 A), propose the powder metallurgy titanium alloy of a kind of argentiferous and boride titanium particle, generated boride titanium particle by in the vacuum heating-press sintering titanium alloy, adding the lanthanum hexaborane reaction in－situ.Chinese invention patent CN 101696474 B have proposed a kind of method for preparing powder metallurgy of rare-earth containing oxide reinforcing phase titanium alloy, rare earth is the form adding with the powder of rare earth hydride, and reaction generates in the deformation process of rare earth oxide strengthening phase after vacuum sintering; Because oxygen is the impurity element in the titanium alloy, the existence of oxygen sharply reduces titanium alloy plasticity, its embrittlement effect is 10 times of aluminium, when oxygen level greater than 0.7% the time, make titanium lose the ability of viscous deformation fully, but in this patent documentation and the principle that generates of undeclared rare earth oxide strengthening phase, and oxide compound easily increases the oxygen impurities content in the alloy when generating.Titanium belongs to a kind of active metal, thereby the preparation of the metallurgical part of titanium alloy powder requires very tight to sintering condition, the required vacuum tightness of traditional vacuum sintering technology is very high, and residual porosity is more in the titanium alloy product of institute's sintering, causes the fatigue property degradation.For obtaining the Ti alloy with high performance sintered metal product, develop new shaping and sintering process (technology such as spray up n., powder injection forming, hot isostatic pressing) and be down to minimum with the porosity in the elimination material or with porosity, the tensile property of material meets or exceeds molten level of forging material.Yet above-mentioned new technology required equipment investment is large, complex process, and manufacturing cost is high, has limited its application development.
Summary of the invention
Technical problem to be solved by this invention is for above-mentioned deficiency of the prior art, provides a kind of original position to synthesize TiC granule intensified titanium-aluminium-molybdenum alloy material and preparation method thereof, the low-cost granule intensified titanium aluminum alloy materials of preparation high-strong toughness.
The technological thought that original position of the present invention is synthesized TiC granule intensified titanium-aluminium-molybdenum alloy material is: aluminium is most widely used α stable element in the titanium alloy, aluminium in the titanium alloy with the substitutional atom mode be present in α mutually in, the adding of aluminium can reduce fusing point and improve beta transus temperature, all plays strengthening effect in room temperature and high temperature.Al has promoted the phase mutual diffusion of Ti with C in sintering process, be conducive to formation and the refinement of TiC Particle Phase.In addition, add the proportion that aluminium also can reduce alloy.But too high addition can occur with Ti
3Al is the α of base
2Ordered solid solution becomes fragile alloy, and thermostability reduces.
Carbon is the clearance type α phase stable element in the titanium alloy, and according to the equivalent thickness of aluminium calculation formula of titanium alloy: the equivalent thickness of aluminium=%Al+%Sn/3+%Zr/6+%Si*4+ (O, C, N) %*10, its effect is 10 times of aluminium.With the interstitial atom mode be present in α mutually in carbon have solid solution strengthening effect far above aluminium, carbon is incorporated in the alloy as alloy element among the present invention, carbon has reduced the content of Al in the alloy to the metalepsy of Al, guarantees that alloy has good plasticity and toughness; Solution strengthening and hollow cathode sintering reaction in－situ by carbon are introduced the means acquisition high strength of high-melting-point disperse TiC Particle Phase reinforcement matrix and the particle enhancing alloy material of wear resisting property.
Molybdenum is most important β phase stable element in the titanium alloy, can dissolve in a large number in the β titanium with substitute mode as β titanium isomorphous element, produce less lattice distortion, therefore, molybdenum element is in reinforced alloys, can keep higher plasticity, the simultaneously adding of molybdenum suppresses the titanium grain growth slowly because of velocity of diffusion, thereby is conducive to the alloy structure refinement.On the impact of titanium linkage force and with the interactional characteristics of titanium, the adding of molybdenum can significantly improve alloy high-temp intensity according to alloying element.
The feasibility of the technology of the present invention thought is:
(1) obdurability of titanium-based alloy material generates the TiC particle strengthening and realizes mutually by carbon replacement part aluminium, control reaction in－situ: replace part aluminium by carbon in the alloy of the present invention and reduce aluminium content, guaranteed that alloy has good plasticity and toughness, this is the relatively low major reason of Al content in the alloy material of the present invention; The intensity of alloy, wear resisting property add quantity of graphite by solution strengthening effect, the change of carbon, and quantity, size and distribution mutually realizes with adjusting hollow cathode sintering process parameter control reaction in－situ generation TiC particle strengthening.According to the Ti-C binary phase diagram, at 920 ℃ of lower Peritectic Reaction: β-Ti that occur
0.6at%.C+ TiC
38at%.Cα-Ti
1.6 at%.C, the carbon atom percentage composition during Peritectic Reaction among α-Ti is 1.6, its mass percent is 0.4%.
(2) select the TiC particle as the advantage of material reinforcement phase of the present invention: to compare with TiB, TiC particle fusing point high (3433 ℃), approach the most with the density of titanium, thermal expansivity and have an identical Poisson's ratio, tensile strength and Young's modulus are 4 times of titanium, good again with the affinity of titanium, and can increase the wear resistance of titanium.
(3) reaction in－situ generates the realization condition of TiC particle strengthening phase: the original position of TiC wild phase is synthetic to be to utilize the hollow cathode sintering between Ti and the graphite (C) synthetic, and its reaction formula is: Ti+C → TiC.When selecting the strengthening phase of in-situ composite, usually judge wild phase by thermomechanical analysis first, whether can in matrix, automatically generate by adding material, the standard of judgement is whether the variation of Gibbs free energy of reaction is less than zero.The condition that another one need to be considered is enthalpy produced in chemical reaction, the heat effect of its representative reaction.Utilize the data of document to calculate enthalpy produced in chemical reaction △ H and the reaction Gibbs free energy △ G of this reaction formula, when temperature of reaction T＜1939K, its formula △ H and △ G can be expressed as follows:
ΔH=-184571.8+5.024T-2.425×10
-3T
2-1.958×10
6/T （1）
ΔG=-184571.8+41.382T-5.024TlnT+2.425×10
-3T
2-9.79×10
5/T （2）
Calculation result shows in sintering range of the present invention (1250 ~ 1500 ℃), the standard Gibbs free energy change value (Δ G) of reaction and enthalpy produced in chemical reaction (Δ H) are always much smaller than zero, the adiabatic temperature of this reaction is 3210K, and surpassing reaction can the spontaneous experience criterion Tad＞2500K that keeps.This illustrates that this thermopositive reaction can make reaction keep automatically and carry out, and the self propagating high temperature building-up reactions namely occurs, and saves the energy.
(4) advantage of the synthetic TiC particle strengthening phase of hollow cathode sintering reaction in－situ.Powder metallurgy sintered temperature is most important to the structure property of sintered article.It is generally acknowledged, the sintering effect of the higher then sintered article of temperature is better.Be in particular in: sintered compact is densification more, and the powder particle combining site increases, the pore shape rounding.But high temperature action also has been accompanied by the side effects such as grain-size is grown up, sintered part contraction increase for a long time.The hollow cathode discharge plasma sintering is as a kind of emerging powder metallurgy sintered technology, it utilizes the hollow cathode effect when producing glow discharge under the vacuum condition, produce very highdensity macro-energy ion bombardment at cathode surface, the heat effect of ion bombardment can make cathode material be rapidly heated to very high temperature, its sintering temperature can reach 3000 ℃, and temperature rise rate can reach 100 ℃/s.Quickly heating up to high temperature is conducive to activate crystal boundary and lattice diffusion and suppresses surface diffusion, thereby the densification process that is conducive to material suppresses the growth of inner crystal grain simultaneously, reduces porosity, make material obtain higher sintered density, the effect of the Fast Sintering that reaches a high temperature.In addition, the hollow cathode sintering utilizes high energy particle to the bombardment of pulverulent product and direct heating and do not need special heating unit, and its equipment volume is little, and temperature control is convenient, energy consumption is few, and have the characteristics of vacuum sintering, can obtain high-quality sintered article.Therefore, the hollow cathode sintering technology is the synthetic TiC granule intensified titanium-aluminium of a kind of good original position-molybdenum alloy material sintering method.
Technological thought based on foregoing invention, technical scheme of the present invention is: a kind of original position is synthesized TiC granule intensified titanium-aluminium-molybdenum alloy material, described alloy material is made of the component of following mass percent: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, 2.5%≤Mo≤3%, surplus are Ti and inevitable impurity.
Described inevitable foreign matter content is controlled at below 0.5%.And described Al, C, Mo are provided by aluminium powder, Graphite Powder 99, molybdenum powder respectively.
Above-mentioned original position is synthesized preparation method's (hollow cathode sintering method) of TiC granule intensified titanium-aluminium-molybdenum alloy material, may further comprise the steps:
1) batching: the aluminium powder, Graphite Powder 99, molybdenum powder and the titanium valve that take by weighing respective amount by following mass percent: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, 2.5%≤Mo≤3%, surplus are Ti; The powder size of above-mentioned each component is: aluminium powder: 300 ~ 500 orders, Graphite Powder 99: 800 ~ 2000 orders, molybdenum powder: 300 ~ 600 orders, titanium valve: 300 ~ 500 orders;
2) ball milling mixes: above-mentioned powder is packed in the 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 the argon shield atmosphere, then compound behind the ball milling is crossed 100 mesh sieves of GB/T6005 regulation;
3) with step 2) in the pressed compact of the compound of ball milling after sieving by two-way mold pressing, described molding pressure is 400 ~ 600Mpa;
4) anode and hollow cathode are set in vacuum chamber, anode is the vacuum vessel housing, and hollow cathode is by the above-mentioned pressed compact material of making and can play the heat-blocking action graphite cake and consist of, and the blank distance each other that is placed on the negative electrode is 10 ~ 20mm;
5) choosing the technical pure argon gas is sputter gas, and vacuum tightness in the stove is evacuated to the limit, then is filled with the shielding gas high-purity argon gas, regulates argon flow amount and makes the interior operating air pressure of stove reach 10 ~ 50Pa;
6) open the workpiece power supply after argon gas reaches operating air pressure, blank and negative electrode are carried out particle bombardment, sintering is 2 ~ 6 hours under 1350 ~ 1550 ℃ of temperature.
In order to get rid of impurity in the stove, between described step 5) and step 6), also comprise step:
(1) blank and negative electrode are carried out particle bombardment, and lasting 20min;
(2) with air pressure adjustment to limit vacuum tightness, discharge because the impurity that particle bombardment produces;
(3) if still residual in the furnace chamber have impurity, then continue performing step (1), (2), until fully satisfy the sintering of titanium alloy.
Operating air pressure is realized by following methods in the described step 5) stove:
(1) opens at first successively mechanical pump, molecular pump, vacuum tightness in the stove is evacuated to the limit;
(2) then be filled with the shielding gas high-purity argon gas, regulate argon flow amount and make the operating air pressure that the stove internal gas pressure reaches to be needed;
(3) after stable, again be pumped to final vacuum, repeat above-mentioned steps, until the foreign gas content such as the interior oxygen of stove reach minimum.
Effect of the present invention is: the present invention breaks through tradition with the thought binding of carbon as the titanium alloy impurity element, proposed carbon is incorporated into new approaches in the alloy as useful alloy element, carbon has reduced the content of Al in the alloy to the metalepsy of Al, guarantees that alloy has good plasticity and toughness; Solution strengthening and hollow cathode sintering reaction in－situ by carbon are introduced the means that high-melting-point disperse TiC Particle Phase is strengthened matrix, and the low-cost particle that obtains high strength and wear resisting property strengthens alloy material; The favourable alloy structure refinement of the adding of molybdenum can significantly improve alloy high-temp intensity.
The present invention proposes the hollow cathode sintering method and realize the high temperature Fast Sintering of the synthetic TiC granule intensified titanium-aluminium of original position-molybdenum alloy material, the density of agglomerated material reaches 97%, and having overcome the shortcomings such as titanium alloy wears no resistance, Young's modulus is low, application will have huge pushing effect in fields such as aerospace and civilian industries to enlarging titanium alloy material.
Embodiment
Embodiment 1
Original position of the present invention is synthesized preparation method's (hollow cathode sintering method) of TiC granule intensified titanium-aluminium-molybdenum alloy material, may further comprise the steps:
1) batching: alloy material is Ti-0.2%Al-2.7%Mo-0.5%C.Proportioning according to alloy takes by weighing 300 purpose aluminium powders, 800 purpose Graphite Powder 99s, 600 purpose molybdenum powders and 300 purpose titanium valves.
2) ball milling mixes: above-mentioned powder is packed in the ball grinder by ratio of grinding media to material 5:1, and at rotating speed 350r/min, Ball-milling Time 1h.For preventing powder oxidation in mechanical milling process, ball grinder passes into argon shield.Then compound behind the ball milling is crossed 100 mesh sieves of GB/T6005 regulation.
3) with step 2) in the pressed compact of the compound of ball milling after sieving by two-way mold pressing, described molding pressure is 400Mpa.
4) anode and hollow cathode are set in vacuum chamber, hollow cathode is by the above-mentioned pressed compact material of making and can play the heat-blocking action graphite cake and consist of, and the blank distance each other that is placed on the negative electrode is 10mm.
5) choosing the technical pure argon gas is sputter gas, and vacuum tightness in the stove is evacuated to the limit, then is filled with the shielding gas high-purity argon gas, regulates argon flow amount and makes the stove internal gas pressure reach 10Pa.Hollow cathode discharge plasma sintering and vacuum sintering furnace, sintering process need could realize under certain operating air pressure.Operating air pressure is realized by following methods in the stove:
(1) opens at first successively mechanical pump, molecular pump, vacuum tightness in the stove is evacuated to the limit;
(2) then be filled with the shielding gas high-purity argon gas, regulate argon flow amount and make the operating air pressure that the stove internal gas pressure reaches to be needed;
(3) after stable, again be pumped to final vacuum, repeat above-mentioned steps, until the foreign gas content such as the interior oxygen of stove reach minimum.
6) open the workpiece power supply after argon gas reaches operating air pressure, blank and negative electrode are carried out particle bombardment, sintering is 2 hours under 1550 ℃ of temperature.
In above-mentioned steps 5) and step 6) between, also comprise step:
(1) blank and negative electrode are carried out particle bombardment, and lasting 20min;
(2) with air pressure adjustment to limit vacuum tightness, discharge because the impurity that particle bombardment produces;
(3) if still residual in the furnace chamber have impurity, then continue performing step (1), step (2), until fully satisfy the sintering of titanium alloy.
The bending strength of the Ti-0.2%Al-2.7%Mo of employing aforesaid method preparation-0.5%C alloy is 685Mpa, and relative density is 95%.
Embodiment 2
The present embodiment is identical with embodiment 1, and different is that the prepared alloy material of step 1) is Ti-0.6%Al-2.5%Mo-1.5%C.Proportioning according to alloy takes by weighing 500 purpose aluminium powders, 1500 purpose Graphite Powder 99s, 400 purpose molybdenum powders and 500 purpose titanium valves; From step 2) different be at rotating speed 300r/min, Ball-milling Time 1.5h; Different from step 3) is that used molding pressure is 600Mpa; Different from step 4) is that the blank distance each other that is placed on the negative electrode is 20mm; Different from step 5) is regulates argon flow amount and makes that operating air pressure reaches 30Pa in the stove; Different from step 6) is under 1350 ℃ of temperature sintering 6 hours, all the other are all with to implement 1 identical.Adopting the bending strength of the alloy material Ti-0.6%Al-2.5%Mo-1.5%C of aforesaid method preparation is 825Mpa, and relative density is 95%.
Embodiment 3
The present embodiment is identical with embodiment 1, and different is that the prepared alloy material of step 1) is Ti-1.5%Al-2.8%Mo-1.0%C.Proportioning according to alloy takes by weighing 400 purpose aluminium powders, 2000 purpose Graphite Powder 99s, 300 purpose molybdenum powders and 400 purpose titanium valves; From step 2) different be at rotating speed 250r/min, Ball-milling Time 2h; Different from step 3) is that used molding pressure is 500Mpa; Different from step 4) is that the blank distance each other that is placed on the negative electrode is 15mm; Different from step 5) is regulates argon flow amount and makes that operating air pressure reaches 50Pa in the stove; Different from step 6) is under 1450 ℃ of temperature sintering 4 hours, all the other are all with to implement 1 identical.Adopting the bending strength of the alloy material Ti-1.5%Al-2.8%Mo-1.0%C of aforesaid method preparation is 900Mpa, and relative density is 96%.
Embodiment 4
The present embodiment is identical with embodiment 1, and different is that the prepared alloy material of step 1) is Ti-2.5%Al-3%Mo-1.5%C.Proportioning according to alloy takes by weighing 500 purpose aluminium powders, 2000 purpose Graphite Powder 99s, 500 purpose molybdenum powders and 400 purpose titanium valves; From step 2) different be at rotating speed 300r/min, Ball-milling Time 2h; Different from step 3) is that used molding pressure is 450Mpa; Different from step 4) is that the blank distance each other that is placed on the negative electrode is 15mm; Different from step 5) is regulates argon flow amount and makes that operating air pressure reaches 35Pa in the stove; Different from step 6) is under 1480 ℃ of temperature sintering 4 hours, all the other are all with to implement 1 identical.Adopting the bending strength of the alloy material Ti-2.5%Al-2.7%Mo-1.5%C of aforesaid method preparation is 905Mpa, and relative density is 97%.
Claims (6)
1. an original position is synthesized TiC granule intensified titanium-aluminium-molybdenum alloy material, it is characterized in that: described alloy material is made of the component of following mass percent: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, 2.5%≤Mo≤3%, surplus are Ti and inevitable impurity.
2. original position according to claim 1 is synthesized TiC granule intensified titanium-aluminium-molybdenum alloy material, and it is characterized in that: described inevitable foreign matter content is controlled at below 0.5%.
3. original position according to claim 1 is synthesized TiC granule intensified titanium-aluminium-molybdenum alloy material, and it is characterized in that: described Al, C, Mo are provided by aluminium powder, Graphite Powder 99, molybdenum powder respectively.
4. the preparation method of the synthetic TiC granule intensified titanium-aluminium of an original position-molybdenum alloy material is characterized in that may further comprise the steps:
1) batching: the aluminium powder, Graphite Powder 99, molybdenum powder and the titanium valve that take by weighing respective amount by following mass percent: 0.2%≤Al≤2.5%, 0.5%≤C≤1.5%, 2.5%≤Mo≤3%, surplus are Ti; The powder size of above-mentioned each component is: aluminium powder: 300 ~ 500 orders, Graphite Powder 99: 800 ~ 2000 orders, molybdenum powder: 300 ~ 600 orders, titanium valve: 300 ~ 500 orders;
2) ball milling mixes: above-mentioned powder is packed in the 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 the argon shield atmosphere, then compound behind the ball milling is crossed 100 mesh sieves of GB/T6005 regulation;
3) with step 2) in the pressed compact of the compound of ball milling after sieving by two-way mold pressing, described molding pressure is 400 ~ 600Mpa;
4) anode and hollow cathode are set in vacuum chamber, anode is the vacuum vessel housing, and hollow cathode is by the above-mentioned pressed compact material of making and can play the heat-blocking action graphite cake and consist of, and the blank distance each other that is placed on the negative electrode is 10 ~ 20mm;
5) choosing the technical pure argon gas is sputter gas, and vacuum tightness in the stove is evacuated to the limit, then is filled with the shielding gas high-purity argon gas, regulates argon flow amount and makes the interior operating air pressure of stove reach 10 ~ 50Pa;
6) open the workpiece power supply after argon gas reaches operating air pressure, blank and negative electrode are carried out particle bombardment, sintering is 2 ~ 6 hours under 1350 ~ 1550 ℃ of temperature.
5. original position according to claim 4 is synthesized the preparation method of TiC granule intensified titanium-aluminium-molybdenum alloy material, it is characterized in that: between described step 5) and step 6), also comprise step:
(1) blank and negative electrode are carried out particle bombardment, and lasting 20min;
(2) with air pressure adjustment to limit vacuum tightness, discharge because the impurity that particle bombardment produces;
(3) if still residual in the furnace chamber have impurity, then continue performing step (1), (2), until fully satisfy the sintering of titanium alloy.
6. original position according to claim 4 is synthesized the preparation method of TiC granule intensified titanium-aluminium-molybdenum alloy material, it is characterized in that: operating air pressure is realized by following methods in the described step 5) stove:
(1) opens at first successively mechanical pump, molecular pump, vacuum tightness in the stove is evacuated to the limit;
(2) then be filled with the shielding gas high-purity argon gas, regulate argon flow amount and make the operating air pressure that the stove internal gas pressure reaches to be needed;
(3) after stable, again be pumped to final vacuum, repeat above-mentioned steps, until the foreign gas content such as the interior oxygen of stove reach minimum.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103526074A (en) * | 2013-09-25 | 2014-01-22 | 中南大学 | TiC particle reinforced Ti-Mo-Hf composite material and preparation method |
| CN109055818A (en) * | 2018-09-10 | 2018-12-21 | 江苏大学 | A kind of preparation method of the Ti-24Nb-4Zr-7.9Sn alloy of Cu alloying |
| CN114058902A (en) * | 2021-11-23 | 2022-02-18 | 西安稀有金属材料研究院有限公司 | High-hardness titanium-based composite material and preparation method thereof |
| CN115261657A (en) * | 2022-08-03 | 2022-11-01 | 南京铖联激光科技有限公司 | Preparation method and preparation device of high-temperature alloy |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61110734A (en) * | 1984-11-02 | 1986-05-29 | Shinroku Saito | Manufacture of titanium composite material |
| CN1621184A (en) * | 2004-12-30 | 2005-06-01 | 西北有色金属研究院 | Powder metallurgy method of granule intensified titanium-base compound material |
| JP2007084865A (en) * | 2005-09-21 | 2007-04-05 | Kobe Steel Ltd | alpha-beta TYPE TITANIUM ALLOY SUPERIOR IN MACHINABILITY AND HOT WORKABILITY |
| CN102343436A (en) * | 2011-09-23 | 2012-02-08 | 常熟市华德粉末冶金有限公司 | In-situ sintered dispersion particle-reinforced warm-compacting powder metallurgy material and preparation method thereof |
-
2012
- 2012-09-27 CN CN201210370474.6A patent/CN102876921B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61110734A (en) * | 1984-11-02 | 1986-05-29 | Shinroku Saito | Manufacture of titanium composite material |
| CN1621184A (en) * | 2004-12-30 | 2005-06-01 | 西北有色金属研究院 | Powder metallurgy method of granule intensified titanium-base compound material |
| JP2007084865A (en) * | 2005-09-21 | 2007-04-05 | Kobe Steel Ltd | alpha-beta TYPE TITANIUM ALLOY SUPERIOR IN MACHINABILITY AND HOT WORKABILITY |
| CN102343436A (en) * | 2011-09-23 | 2012-02-08 | 常熟市华德粉末冶金有限公司 | In-situ sintered dispersion particle-reinforced warm-compacting powder metallurgy material and preparation method thereof |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103526074A (en) * | 2013-09-25 | 2014-01-22 | 中南大学 | TiC particle reinforced Ti-Mo-Hf composite material and preparation method |
| CN109055818A (en) * | 2018-09-10 | 2018-12-21 | 江苏大学 | A kind of preparation method of the Ti-24Nb-4Zr-7.9Sn alloy of Cu alloying |
| CN114058902A (en) * | 2021-11-23 | 2022-02-18 | 西安稀有金属材料研究院有限公司 | High-hardness titanium-based composite material and preparation method thereof |
| CN115261657A (en) * | 2022-08-03 | 2022-11-01 | 南京铖联激光科技有限公司 | Preparation method and preparation device of high-temperature alloy |
| CN115261657B (en) * | 2022-08-03 | 2023-02-28 | 南京铖联激光科技有限公司 | Preparation method and preparation device of high-temperature alloy |
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