CN115894032A - Ti 3 AlC 2 Preparation method of enhanced carbon-based pantograph slide plate - Google Patents
Ti 3 AlC 2 Preparation method of enhanced carbon-based pantograph slide plate Download PDFInfo
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Abstract
The invention discloses a Ti 3 AlC 2 The preparation method of the reinforced carbon-based pantograph pan adopts a mixing mode of kneading, and realizes uniform coating of asphalt by controlling the kneading temperature, the kneading time and the feeding sequence so as to be beneficial to subsequently-formed spherical particles and Ti 3 AlC 2 Uniformly coated outside the particles, and the layered coating structure is similar to a core-shell structure. Such a construction on the one hand avoids reinforcing phasesAgglomeration, on the other hand, can also effectively improve Ti 3 AlC 2 The combination effect of the reinforcing phase and the carbon matrix is enhanced, and the defects of holes, gaps and the like are avoided. The roasting process can fully ensure the cracking of the asphalt and the sintering of each carbon component, and ensure the tight connection of the reinforcing phase and the carbon matrix, thereby ensuring that the finished product obtains ideal mechanical strength and electrical properties. At the same time, ti can be avoided 3 AlC 2 Thereby providing powerful guarantee for the optimization of the electrical property and the current-carrying frictional wear property of the sample.
Description
Technical Field
The invention belongs to the field of pantograph slide plates, and particularly relates to Ti 3 AlC 2 A preparation method of a reinforced carbon-based pantograph slide plate.
Background
Nowadays, rail transit is one of the main transportation modes of modern transportation as an important infrastructure of the country, and is a national economic foundation, strategic, precedent and critical industry. With the gradual progress of the economic integration process of the international market, the rapid and safe transportation mode has a key effect on the input and output of resources and is an indispensable ring for the steady increase of economy. In the estimated 2025 years, the business mileage of railways in China reaches about 16.5 kilometers, wherein high-speed railways (including partial intercity railways) are about 5 kilometers and cover over 50 million cities of people, a '123 high-speed railway trip circle' in China is basically formed, and the requirement of people on good trips is better met. Under the background of the times, the technical development and the localization promotion of rail transit are particularly important. The pantograph slide plate is a current collecting device for the electric tractor to obtain electric energy from a contact net, is an important guarantee for the safe and stable running of rail transit, and is also one of key technologies for the development of rail transit. The severe working environment of the pantograph slide plate requires that the energy loss of the pantograph slide plate is small in the electric energy transmission process, and the pantograph slide plate is not easy to break down and damage in the long-time high-speed moving process of a train, so that the pantograph slide plate not only needs to have excellent electric conductivity, but also needs to have good mechanical properties.
At present, because carbon back combined material has outstanding self-lubricating property, high-speed railway adopts carbon back pantograph slide more. However, two distinct short plates of pure carbon skateboards limit their performance: firstly, the mechanical strength is low, the problem that the block is easy to break and fall off in the using process is caused, and adverse effects are caused on the safe operation of rail transit; and secondly, the resistivity is larger than that of a metal sliding plate, so that more joule heat can be generated during use, and the serious temperature rise can induce arc ablation to damage a contact net and a pantograph sliding plate. In response to the above problems with pure carbon skateboards exposure, numerous scholars have proposed different solutions.
CN113997677A, "preparation method of pantograph pan of baked composite material", proposes to use metal mesh, fiber fabric and mixed fiber to distribute between each other to reinforce the composite material. But the preparation process is more complex, and the problem of poor combination effect of the metal mesh and the carbon substrate exists; in addition, the composite material needs to be roasted and impregnated for multiple times until the impregnation is completed for 3 times and the roasting is completed for 4 times, so that the roasted composite material pantograph slide plate is prepared. The preparation process is too complicated, the production cost is high, and the industrial popularization is not facilitated.
CN107081915A, "a silver-plated carbon fiber reinforced carbon-based pantograph pan", proposes to reinforce a carbon substrate with a copper mesh, silver-plated carbon fibers and chopped carbon fibers. The silver plating process of the carbon fiber in the method relates to processes of sensitization, activation and the like, and the used medicines such as palladium chloride and the like are expensive, the preparation cost is high, and the process is complex and tedious. In addition, after the chopped carbon fibers are introduced into the matrix, the sintering temperature needs to be strictly controlled during roasting, otherwise, the cracking problem is easy to occur, and the samples are directly scrapped.
In CN113336565A, "a mesocarbon microbeads reinforced carbon-based pantograph pan and a method for preparing the same", it is proposed to improve the interfacial bonding force between the carbon fiber and the carbon matrix by using mesocarbon microbeads. However, the preparation process of the mesocarbon microbeads is complicated and difficult to realize industrial production. Firstly, loading a coal tar pitch raw material into a sealed air-isolated high-pressure reaction kettle, and heating to obtain mesophase pitch; and centrifuging the intermediate phase asphalt and washing with quinoline, and then sequentially carrying out reduced pressure suction filtration and vacuum drying on the precipitate with a small amount of pyridine and absolute ethyl alcohol to obtain the MCMB. The preparation steps are various, and dangerous devices such as a high-pressure reaction kettle are involved, so that the process is to be optimized to realize industrial application.
Disclosure of Invention
The invention provides Ti for overcoming the defects of high resistivity, low mechanical strength and the like of the existing carbon-based pantograph slide plate 3 AlC 2 The preparation method of the enhanced carbon-based pantograph pan is successful in exploring Ti with higher purity which is more suitable for industrial production 3 AlC 2 A preparation process of the powder and the pantograph pan composite material. Ti of the invention 3 AlC 2 The enhanced carbon-based pantograph pan has better conductivity and more excellent current-carrying friction performance.
The invention adopts Ti 3 AlC 2 The method for directly reinforcing the carbon matrix has simple and efficient preparation process, can effectively solve the problems of low strength, high resistivity and the like of the pure carbon material, and can also improve the current-carrying frictional wear performance of the composite material. Ti (titanium) 3 AlC 2 The layered conductive ceramic material is a novel layered conductive ceramic material, has the advantages of both metal and ceramic, has the conductive and heat-conducting properties similar to those of metal, and also has the properties of high strength, high temperature resistance and the like of ceramic, so that the layered conductive ceramic material can better work in a complex and harsh environment. The resistivity of the sliding plate is close to that of metallic iron and far lower than that of a common pure carbon sliding plate, and Ti is adopted 3 AlC 2 The carbon-based pantograph slide plate can be used as a reinforcing phase to effectively improve the problem of higher resistivity of the carbon-based pantograph slide plate. Meanwhile, the high-temperature lubricating performance, the high-temperature stability, the self-repairing performance and the like of the pantograph slide plate can not only be used in harsh and complex working environments of the pantograph slide plate, but also enable the pantograph slide plate to have longer service life, and can greatly promote the progress and development of the domestic carbon-based pantograph slide plate material. But Ti 3 AlC 2 The bonding strength with the carbon substrate is very low and only by mechanical interlocking connection; ti 3 AlC 2 The density difference with the carbon matrix component is large, and the simple mechanical mixing is difficult to ensure the uniform distribution of the components. The preparation process provided by the invention can quickly and effectively solve the problem of Ti 3 AlC 2 Low bonding strength with carbon matrix and uneven distribution, simple process, easy realization and suitability for industrial popularization。
Ti of the invention 3 AlC 2 The preparation method of the reinforced carbon-based pantograph slide plate comprises the following steps:
step 1: respectively weighing scale graphite, pitch coke, carbon black and needle coke raw materials according to the proportion, and sequentially adding the raw materials into a V-shaped mixer from large to small according to the particle size, wherein the mixing time is 60-90min;
and 2, step: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 30min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 20min.
The mesh number of the crystalline flake graphite is 200 meshes, the asphalt coke is respectively compounded by different sizes of 50 meshes, 100 meshes and 150 meshes, the mesh number of the needle coke is 100 meshes, and the Ti is 3 AlC 2 The mesh number of the powder is 300 meshes, and the particle size of the carbon black is 27-40nm.
The raw materials used in the step 1 and the step 2 comprise the following components in percentage by mass:
10% of flake graphite, 50% of asphalt coke, 10% of needle coke, 10% of powdered asphalt and the balance of Ti 3 AlC 2 And carbon black.
Further, the asphalt coke is compounded by 50 meshes, 100 meshes and 150 meshes in different sizes, and the percentage of the asphalt coke is 10%, 30% and 10% respectively.
Further, ti 3 AlC 2 And carbon black in a total amount of 20%, wherein Ti 3 AlC 2 4-16% of the total weight of the carbon black, and the balance of the carbon black.
Through the kneading process, the asphalt can uniformly coat the components such as asphalt coke, needle coke, crystalline flake graphite, carbon black and the like to form a series of spherical particles with a layered coating structure. At this time, ti is further added 3 AlC 2 Powder, which adheres uniformly to the surface of the spherical particles. Wherein the content of the powdery asphalt is 10 percent, the content is strictly controlled, and the proper amount of the powdery asphalt can help Ti 3 AlC 2 The uniform dispersion of the powder also facilitates the subsequent forming process. However, too much pitch is added and will appear later in the firing processCracking a large amount of components, volatilizing small molecules and ensuring the compactness of the sample.
And 3, step 3: carrying out hot press molding on the powder kneaded in the step 2; adding appropriate amount of kneaded powder into a mold, heating to 120 deg.C, hot pressing at 30MPa for 10min, heating to 150 deg.C, hot pressing at 50MPa for 10min to obtain the final product containing Ti 3 AlC 2 Green compacts of (4);
and 4, step 4: and (4) putting the green body obtained in the step (3) into a roasting furnace filled with argon atmosphere, wherein the roasting temperature is 1200 ℃. The roasting process is to raise the temperature to 400 deg.c in the heating rate of 5 deg.c/h, raise the temperature to 900 deg.c in the heating rate of 4 deg.c/h, raise the temperature to 1200 deg.c in the heating rate of 2 deg.c/h and maintain for 20h. During the roasting process, the pitch encapsulating the components cracks to form pyrolytic carbon of a certain thickness, thereby tightly connecting the individual carbon components together. In addition, the sintering function is also realized in the heat preservation process of 1200 ℃, and finally, the sample obtains good strength. In the following examples of the invention, the calcined Ti powders were prepared to contain 0%, 4%, 8%, 12% and 16% Ti 3 AlC 2 The samples of (a) are designated as A0, A4, A8, A12 and A16, respectively.
Ti used in the invention 3 AlC 2 The powder is prepared by pressureless sintering, and the specific preparation process is as follows:
the raw materials are TiC powder of 200 meshes, al powder of 300 meshes, ti powder of 150 meshes and Sn powder of 325 meshes, and the molar ratio is 2:1.5:1:0.1. ball-milling and mixing the powder, wherein the ball material ratio is 10:1, adding alcohol to immerse, and then, respectively setting the ball milling rotating speed and the ball milling time to be 200r/min and 4h; after ball milling, putting the mixture into a vacuum drying box, vacuumizing the vacuum drying box, and drying the mixture for 2 hours at the temperature of 80 ℃; and filling the dried powder into a corundum burning boat, properly compacting, putting into a tubular furnace, and introducing argon-hydrogen mixed gas, wherein the gas flow is controlled to be 100mL/min in the first 30min and is adjusted to be 50mL/min in the later period. The heating process is that the temperature is increased to 700 ℃ at the speed of 10 ℃/min, the temperature is preserved for 10min, the temperature is increased to 900 ℃ at the speed of 5 ℃/min, the temperature is preserved for 10min, and finally the temperature is increased to 1250 ℃ at the speed of 2 ℃/min, and the temperature is preserved for 10min. Ti synthesized by the preparation method 3 AlC 2 High purity, good appearance, relatively low synthesis temperature and low equipment requirement. To syntheticTi 3 AlC 2 By observing with a scanning electron microscope, synthesized Ti as shown in FIG. 1 3 AlC 2 With a good layered structure, XRD measurements were performed on it, with a calculated purity of 98.23% as shown in fig. 2.
Ti 3 AlC 2 The matching of the granularity of the raw materials and the optimal synthesis process are corresponding during synthesis, and in order to search the optimal synthesis process, the invention respectively searches the heating rate, the heat preservation time and the heat preservation temperature.
The heating rates from room temperature to 700 ℃ are respectively set to be 5 ℃/min, 10 ℃/min and 15 ℃/min, XRD tests show that too high a heating rate can prevent air adsorbed in the raw material powder from timely escaping and oxidizing, but too slow a heating rate can prolong the synthesis time.
The heating rates of 700 ℃ to 900 ℃ are respectively set as 3 ℃/min, 5 ℃/min and 7 ℃/min, and XRD test results show that the synthesized Ti can be obtained when the heating rate is too high 3 AlC 2 The purity is lower, and the temperature rise speed is only 83.56 percent when being 7 ℃/min; but too slow will prolong the synthesis time.
The holding time of 700 ℃ and 900 ℃ is respectively set to be 0min, 5min, 10min and 15min, and XRD tests show that the short holding time can directly cause the synthesized Ti 3 AlC 2 The purity is low; and the heat preservation time of more than 10min has little effect on improving the purity.
The final synthesis temperature is respectively set to 1200 ℃, 1250 ℃, 1300 ℃ and 1350 ℃, and XRD tests show that the purity is obviously reduced when the synthesis temperature is lower than 1250 ℃, and the purity of the synthesis at 1200 ℃ is only 85.32%; whereas a synthesis temperature above 1250 ℃ has little effect on the improvement of purity.
The invention has the beneficial effects that:
1. the invention uses Ti which has the advantages of both ceramics and metals 3 AlC 2 As a reinforcing phase, ti 3 AlC 2 The unique bonding mode endows the material with good electric and thermal conductivity, and the electric conductivity of the material is close to that of metallic iron; in addition, ti 3 AlC 2 Also has the good properties of ceramics, low density, high elastic modulus and low thermal expansion coefficientAnd (4) counting. But also has a layered structure similar to graphite, and is a very ideal reinforcing phase of the carbon-based pantograph pan material.
2. Ti prepared by the invention 3 AlC 2 The powder is prepared by simple process, which only comprises three steps of raw material mixing, high-temperature synthesis, crushing and sieving. And the shape of the powder is stable and good through SEM observation, and the powder is an obvious layered structure. The purity of the product is calculated to reach 98.23 percent by XRD, the synthesis temperature is only 1250 ℃, the preparation process is simple and efficient, and the large-scale production is convenient.
3. In the invention, a mixing mode of kneading is adopted, and uniform coating of asphalt is realized by controlling the kneading temperature, the kneading time and the feeding sequence so as to be beneficial to subsequently-formed spherical particles and Ti 3 AlC 2 Uniformly coated outside the particles, and the layered coating structure is similar to a core-shell structure. Such a structure makes it possible, on the one hand, to avoid the agglomeration of the reinforcing phase and, on the other hand, to improve Ti effectively 3 AlC 2 The combination effect of the reinforcing phase and the carbon matrix is enhanced, and defects such as holes, gaps and the like are avoided.
4. The roasting process in the invention can fully ensure the cracking of the asphalt and the sintering of each carbon component, and ensure the tight connection of the reinforcing phase and the carbon matrix, thereby ensuring that the finished product obtains ideal mechanical strength and electrical properties. At the same time, ti can be avoided 3 AlC 2 Thereby providing powerful guarantee for the optimization of the electrical property and the current-carrying frictional wear property of the sample.
Drawings
FIG. 1 is Ti prepared 3 AlC 2 SEM image of the powder.
FIG. 2 is Ti prepared 3 AlC 2 XRD pattern of the powder.
FIG. 3 is a diagram of the morphology of powders under different kneading processes.
Fig. 4 is an XRD pattern of a 12.
Fig. 5 is an SEM image of a 12.
Fig. 6 is a fracture view of a 12.
FIG. 7 shows the sample at 10A/cm 2 Average coefficient of friction at current of。
FIG. 8 shows the sample concentration at 10A/cm 2 Wear rate under current.
Fig. 9 is a surface Raman spectrum before and after the a12 current-carrying frictional wear test.
Fig. 10 is an SEM image of the surface after a12 current-carrying wear test.
Detailed Description
The technical solution of the present invention is further illustrated by the following specific examples.
Example 1:
1. weighing flake graphite, pitch coke, carbon black and needle coke according to the designed mass ratio; respectively weighing scale graphite, pitch coke, carbon black, needle coke and other raw materials, and sequentially adding the raw materials into a V-shaped mixer from large to small according to the particle size, wherein the mixing time is 60-90min. The mesh number of the flake graphite in the components is 200 meshes, and the proportion is 10 percent; the coke mesh number of the asphalt is respectively 50 meshes, 100 meshes and 150 meshes, and the ratio of the coke mesh number to the coke mesh number is respectively 10%, 30% and 10%; the needle coke mesh number is 100 meshes, and the proportion is 10%. The balance being Ti 3 AlC 2 And carbon black.
2. Pouring the mixed powder into a kneading machine for kneading, and kneading for 20min at 90 ℃; adding 100 mesh powdered asphalt, and kneading at 130 deg.C for 30min; finally adding Ti with the mass fraction of 0%, 4%, 8%, 12% and 16% to 300 meshes 3 AlC 2 Kneading the powder at 120 deg.C for 20min. Through the kneading process, the asphalt can uniformly coat the components such as asphalt coke, needle coke, crystalline flake graphite, carbon black and the like to form a series of spherical particles. At this time, ti is further added 3 AlC 2 Powder, which adheres uniformly to the surface of the spherical particles. Wherein the content of the powdery asphalt is 10 percent, the content is strictly controlled, and the proper amount of the powdery asphalt can help Ti 3 AlC 2 The uniform dispersion of the powder also facilitates the subsequent forming process. However, when too much asphalt is added, a large amount of components are cracked and small molecules are volatilized in the subsequent roasting process, and the compactness of the sample cannot be ensured.
Example 2: kneading process
A first group: pouring the mixed powder obtained in the step 1 into a kneading machineKneading in a machine, namely kneading for 20min at 90 ℃, adding 100-mesh powdery asphalt, and kneading for 20min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 20min.
Second group: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 30min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 20min.
Third group: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 20min at 140 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 20min.
And a fourth group: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 30min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 30min.
And a fifth group: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 30min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 130 deg.C for 20min.
Kneading temperature and time after adding powdery asphalt and Ti 3 AlC 2 The kneading temperature and time after the powder is added can directly influence the shape and size of the particles with the layered wrapping structure after kneading. The particles obtained by analyzing each embodiment are found to have irregular particle shapes or larger particle sizes due to overhigh kneading temperature and overlong kneading time, so that the particles are not in full contact, and the green body cannot obtain better compactness in a hot pressing link. However, if the kneading temperature is too low and the kneading time is not sufficient, particles having a layered coating structure cannot be formed, and the bonding strength and uniform distribution of the reinforcing phase and the carbon matrix cannot be ensured. The density analysis of the hot-press formed green bodies of the same component after different kneading processes according to the above embodiments is combined to determine that the second group has the best morphology of the obtained layer-shaped wrapping structure, as shown in fig. 3, and the obtained green bodies have the highest density,the degree of densification is best.
Hot-press molding the kneaded powder; adding a proper amount of kneaded powder into a mold, heating to 120 ℃, then hot-pressing at 30MPa for 10min, heating to 150 ℃, then hot-pressing at 50MPa for 10min to obtain Ti with different mass fractions 3 AlC 2 A green compact of (2).
The green body was placed in a roasting furnace filled with argon atmosphere at a roasting temperature of 1200 ℃. The roasting process is to raise the temperature to 400 deg.c in the heating rate of 5 deg.c/h, raise the temperature to 900 deg.c in the heating rate of 4 deg.c/h, raise the temperature to 1200 deg.c in the heating rate of 2 deg.c/h and maintain for 20h. During the roasting process, the pitch encapsulating the components cracks to form pyrolytic carbon of a certain thickness, thereby tightly connecting the individual carbon components together. In addition, the sintering function is also realized in the heat preservation process of 1200 ℃, and finally, the sample obtains good strength. Finally, the roasted Ti with the content of 0 percent, 4 percent, 8 percent, 12 percent and 16 percent 3 AlC 2 The samples of (a) are designated as A0, A4, A8, A12 and A16, respectively.
Example 3: roasting process
A first group: the roasting process is that the temperature is increased to 400 ℃ at the temperature rising speed of 6 ℃/h, then the temperature is increased to 900 ℃ at the temperature rising speed of 4 ℃/h, finally the temperature is increased to 1200 ℃ at the temperature rising speed of 2 ℃/h, and the temperature is kept for 20h. XRD (X-ray diffraction) test is carried out on the pantograph slide plate material prepared by the roasting process, and the result shows that part of Ti 3 AlC 2 Oxidation takes place.
Second group: the roasting process is that the temperature is increased to 400 ℃ at the temperature increasing speed of 5 ℃/h, then the temperature is increased to 900 ℃ at the temperature increasing speed of 4 ℃/h, finally the temperature is increased to 1200 ℃ at the temperature increasing speed of 2 ℃/h, and the temperature is kept for 20h. XRD and SEM tests are carried out on the pantograph sliding plate material prepared by the roasting process, and XRD results shown in figure 4 show that Ti is not contained 3 AlC 2 Oxidation and decomposition occurred, and Ti was found by SEM picture 3 AlC 2 And the carbon matrix are tightly combined as shown in fig. 5.
Third group: the roasting process is that the temperature is increased to 400 ℃ at the temperature increasing speed of 5 ℃/h, then the temperature is increased to 900 ℃ at the temperature increasing speed of 6 ℃/h, finally the temperature is increased to 1200 ℃ at the temperature increasing speed of 2 ℃/h, and the temperature is kept for 20h. Prepared by the roasting processSEM test is carried out on the prepared pantograph pan material, and Ti is found through SEM pictures 3 AlC 2 The bonding with the carbon matrix is not tight, and more pores exist in the interface.
And a fourth group: the roasting process is that the temperature is increased to 400 ℃ at the temperature increasing speed of 5 ℃/h, then the temperature is increased to 900 ℃ at the temperature increasing speed of 4 ℃/h, finally the temperature is increased to 1200 ℃ at the temperature increasing speed of 4 ℃/h, and the temperature is kept for 20h. SEM test is carried out on the pantograph pan material prepared by the roasting process, and SEM test shows that more pores exist in the composite material.
And a fifth group: the roasting process is that the temperature is increased to 400 ℃ at the temperature increasing speed of 5 ℃/h, then the temperature is increased to 900 ℃ at the temperature increasing speed of 4 ℃/h, finally the temperature is increased to 1300 ℃ at the temperature increasing speed of 2 ℃/h, and the temperature is kept for 20h. SEM test of the pantograph pan material prepared by the roasting process shows that the further extension of the heat preservation time does not obviously improve Ti through SEM pictures 3 AlC 2 The bonding effect with the carbon substrate and the inside of the carbon substrate increases the cost and the period of the preparation.
A sixth group: the roasting process is that the temperature is increased to 400 ℃ at the temperature increasing speed of 5 ℃/h, then the temperature is increased to 900 ℃ at the temperature increasing speed of 4 ℃/h, finally the temperature is increased to 1200 ℃ at the temperature increasing speed of 2 ℃/h, and the temperature is kept for 30h. SEM test of the pantograph pan material prepared by the roasting process shows that the further extension of the heat preservation time does not obviously improve Ti through SEM pictures 3 AlC 2 The bonding effect with the carbon substrate and the inside of the carbon substrate increases the cost and the period of the preparation.
The roasting process of the carbon-based pantograph pan material is directly related to the components of the carbon-based pantograph pan material, and the roasting processes of the carbon-based pantograph pan materials with different components are greatly different. Extremely complex physical and chemical reactions can occur in the roasting process, and carbon-based pantograph pan materials with different components need to be scientifically researched to determine the most appropriate roasting process, so that the final sample performance is ensured to be excellent.
And (4) analyzing results:
analysis of the properties of the A0-A16 samples revealed that Ti is accompanied by 3 AlC 2 The resistivity of the composite material is obviously reduced by adding the (C),this is mainly due to Ti 3 AlC 2 Excellent conductivity, and the resistivity is close to that of metallic iron. The Shore hardness of the composite material also shows an increasing trend, and Ti is fully reflected 3 AlC 2 Higher hardness and strength ceramic properties. The flexural strength and impact toughness of the composite material follow the Ti 3 AlC 2 Shows a tendency of increasing first and then decreasing, because the crack encounters the hard phase Ti during propagation in the mechanical property test 3 AlC 2 A bypass phenomenon occurs, as shown in fig. 6, thereby slowing the propagation speed of the crack and also consuming more energy; in addition, the crack can be propagated in the expansion process, so that more micro-cracks are generated, the stress concentration is reduced, and the crack expansion speed is reduced. However, the problem of agglomeration inevitably occurs when too much Ti is added, which affects the Ti strengthening phase 3 AlC 2 Exerting its excellent strengthening effect. As can be seen from an analysis of the current-carrying friction coefficient and the wear rate, ti is contained in an amount of 12wt% 3 AlC 2 The composite material of (A) has a minimum coefficient of friction and wear rate, as shown in FIGS. 7 and 8, at 10A/cm 2 The current-carrying friction coefficient under the current density of (1) is only 0.13, and the wear rate is only 8.46mg/km, which is more excellent than that of a pure carbon sample. Part of Ti of the surface can be known by Raman analysis before and after the surface is worn 3 AlC 2 Is changed into corresponding oxide TiO 2 And Al 2 O 3 As shown in fig. 9. In the process of a current-carrying friction and wear test, the formation of oxides can effectively reduce the direct contact between friction pairs, and a good lubricating and antifriction effect is achieved. The surface lubricating film is composed of the carbon film and the oxidation film, and the surface covering lubricating film is more complete as shown in figure 10, so that the lubricating film has excellent current-carrying frictional wear performance.
TABLE 1 basic Properties of the samples
Claims (9)
1. Ti 3 AlC 2 The preparation method of the reinforced carbon-based pantograph slide plate is characterized by comprising the following steps:
step 1: respectively weighing scale graphite, pitch coke, carbon black and needle coke raw materials according to the proportion, and sequentially adding the raw materials into a V-shaped mixer from large to small according to the particle size, wherein the mixing time is 60-90min;
step 2: pouring the mixed powder obtained in the step 1 into a kneading machine for kneading, firstly kneading for 20min at 90 ℃, then adding 100-mesh powdery asphalt, and kneading for 30min at 130 ℃; finally adding Ti 3 AlC 2 Kneading the powder at 120 deg.C for 20min;
and step 3: carrying out hot press molding on the powder kneaded in the step 2; adding appropriate amount of kneaded powder into a mold, heating to 120 deg.C, hot pressing at 30MPa for 10min, heating to 150 deg.C, hot pressing at 50MPa for 10min to obtain the final product containing Ti 3 AlC 2 The green compact of (a);
and 4, step 4: and (4) putting the green body obtained in the step (3) into a roasting furnace filled with argon atmosphere, wherein the roasting temperature is 1200 ℃.
2. The method of claim 1, wherein:
the raw materials used in the step 1 and the step 2 comprise the following components in percentage by mass:
10% of flake graphite, 50% of asphalt coke, 10% of needle coke, 10% of powdered asphalt and the balance of Ti 3 AlC 2 And carbon black.
3. The method of claim 2, wherein:
the mesh number of the crystalline flake graphite is 200 meshes, the mesh number of the needle coke is 100 meshes, and the Ti 3 AlC 2 The mesh number of the powder is 300 meshes, and the particle size of the carbon black is 27-40nm.
4. The production method according to claim 2, characterized in that:
the asphalt coke is compounded by 50 meshes, 100 meshes and 150 meshes in different sizes, and the proportion of the asphalt coke is 10%, 30% and 10% respectively.
5. The method of claim 2, wherein:
Ti 3 AlC 2 and carbon black in a total amount of 20%, wherein Ti 3 AlC 2 4-16% of carbon black and the balance of carbon black.
6. The method of claim 1, wherein:
in the step 4, the roasting process is to raise the temperature to 400 ℃ at the temperature raising speed of 5 ℃/h, then to raise the temperature to 900 ℃ at the temperature raising speed of 4 ℃/h, finally to raise the temperature to 1200 ℃ at the temperature raising speed of 2 ℃/h, and then to preserve the temperature for 20h.
7. The method of claim 1, wherein:
the Ti 3 AlC 2 The powder is prepared by a pressureless sintering method and comprises the following steps:
TiC powder of 200 meshes, al powder of 300 meshes, ti powder of 150 meshes and Sn powder of 325 meshes are mixed by ball milling, and the ball-to-material ratio is 10:1, adding alcohol to immerse, and then ball-milling at a rotating speed and for 4 hours at 200 r/min; after the ball milling is finished, putting the mixture into a vacuum drying box, vacuumizing the vacuum drying box, and drying the mixture for 2 hours at the temperature of 80 ℃; filling the dried powder into a corundum burning boat, compacting, putting into a tubular furnace, introducing argon-hydrogen mixed gas, heating to 1250 ℃, and sintering to obtain Ti 3 AlC 2 And (3) powder.
8. The method of claim 7, wherein:
the mol ratio of TiC powder, al powder, ti powder and Sn powder is 2:1.5:1:0.1.
9. the method of claim 7, wherein:
the heating process is that the temperature is increased to 700 ℃ at the speed of 10 ℃/min, the temperature is preserved for 10min, the temperature is increased to 900 ℃ at the speed of 5 ℃/min, the temperature is preserved for 10min, and finally the temperature is increased to 1250 ℃ at the speed of 2 ℃/min, and the temperature is preserved for 10min.
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