A chromium boride-based cermet material, its preparation method and application

Abstract

The present invention discloses a chromium boride-based cermet material, a preparation method thereof and an application. The chromium boride-based cermet material uses chromium boride as the hard phase and FeCrNiAlTi high-entropy alloy as the binder phase. The preparation method of the cermet material is to obtain FeCrNiAlTi high-entropy alloy powder through mechanical alloying, ball-mill and mix the FeCrNiAlTi high-entropy alloy powder and CrB2 powder, and then perform spark plasma sintering. The chromium boride-based cermet material obtained by the present invention uses FeCrNiAlTi high-entropy alloy as the binder phase, improves the toughness of the cermet material, and makes up for the disadvantage of the large brittleness of pure chromium boride ceramics. The cermet material obtained by the present invention not only has good molten aluminum corrosion resistance, but also has excellent mechanical properties, can meet industrial use, does not contain strategic metals such as Co and W, and has a relatively low cost, which is beneficial to large-scale production.

Description

Technical Field

[0001] The present invention belongs to the technical field of cermet material preparation, and particularly relates to a chromium boride-based cermet material, a preparation method thereof, and an application thereof. Background Art

[0002] During the smelting of aluminum alloys, the forming of aluminum products, and hot dip aluminizing, the molten aluminum will come into contact with components such as crucibles, rollers, bushings, and sink rolls and cause erosion, thus leading to a series of problems such as shortened service life of components, reduced quality of aluminum products, and increased production costs. Therefore, it is very necessary to explore materials with excellent molten aluminum corrosion resistance. Among the overall materials, high melting point metals such as W, Mo, and Nb have excellent molten aluminum corrosion resistance, but they are expensive; intermetallic compounds can improve the molten aluminum corrosion resistance, but their brittleness limits their application range; ceramics have excellent molten aluminum corrosion resistance, but poor thermal shock resistance; cermet materials combine the advantages of metals and ceramics, not only having excellent molten aluminum corrosion resistance but also good impact resistance. Summary of the Invention

[0003] Aiming at the deficiencies of the prior art, the first object of the present invention is to provide a chromium boride-based cermet material. The chromium boride-based cermet material provided by the present invention has both excellent mechanical properties and good molten aluminum corrosion resistance.

[0004] The second object of the present invention is to provide a preparation method of a chromium boride-based cermet material.

[0005] The third object of the present invention is to provide an application of a chromium boride-based cermet material.

[0006] In order to achieve the above-mentioned invention objects, the present invention provides the following technical solutions:

[0007] The present invention provides a chromium boride-based cermet material, wherein the chromium boride-based cermet material uses chromium boride as the hard phase and FeCrNiAlTi high-entropy alloy as the binder phase, and the mass percentage of the FeCrNiAlTi high-entropy alloy in the cermet material is 10%-20%.

[0008] The chromium diboride-based (CrB2-FeCrNiAlTi) cermet material provided by the present invention uses chromium diboride as the hard phase and FeCrNiAlTi high-entropy alloy as the binder phase. Among them, CrB2 can resist liquid metal corrosion, wear resistance, and high-temperature oxidation, but its sintering performance is poor. In the present invention, the addition of the FeCrNiAlTi binder phase can reduce the sintering temperature of the ceramic and inhibit the growth of ceramic grains. Secondly, the FeCrNiAlTi binder phase will form a liquid phase during the sintering process and has good wettability with the ceramic, which can fill the voids between the ceramics and improve the overall density of the cermet, thereby improving the sintering performance of CrB2 and enhancing the overall toughness of the material. With the cooperation of the two, the obtained cermet material has both excellent mechanical properties and good molten aluminum corrosion resistance.

[0009] In the present invention, the binder phase used is an FeCrNi-based high-entropy alloy. The FeCrNi-based high-entropy alloy perfectly combines good performance and low cost. The addition of Al and Ti can improve its strength and molten aluminum corrosion resistance. The inventor found that the addition of the FeCrNiAlTi binder phase will form phases with different Vickers hardness in the cermet, thereby generating toughening mechanisms such as crack deflection and increasing the overall toughness of the cermet. Secondly, during the molten aluminum corrosion process, the corrosion layer of pure chromium diboride ceramic will fall off when it grows to a certain thickness, and the aluminum liquid will penetrate into the deep part of the ceramic along the pores in the ceramic. The Al element is radially distributed in the ceramic. However, the cermet added with the FeCrNiAlTi binder phase of the present invention is gradually eroded during the erosion process of the aluminum liquid, and the formed corrosion layer can hinder the diffusion of the Al element to a certain extent, thereby greatly improving the molten aluminum corrosion resistance.

[0010] Of course, in the present invention, the selection and mass fraction of the binder phase are crucial. For example, when the mass fraction of the binder phase is too small, it is not enough to affect the performance of the cermet; when the mass fraction of the binder phase is too large, the Vickers hardness of the cermet will further decrease. More importantly, during the molten aluminum corrosion process, large pieces of the binder phase will be exposed in the aluminum liquid, greatly reducing the molten aluminum corrosion resistance of the cermet. If the composition of the binder phase is not reasonably selected, if the melting point of the selected binder phase is too high, a high sintering temperature is required, increasing the sintering difficulty; if the wettability between the selected binder phase and the ceramic is poor, the sintered cermet has a low density or even cannot be formed; if the selected binder phase itself has poor molten aluminum corrosion resistance, the aluminum liquid is very likely to corrode the binder phase first, reducing the overall molten aluminum corrosion resistance of the cermet.

[0011] In a preferred embodiment, in the binder phase, by molar ratio: Fe:Cr:Ni:Al:Ti = 1:1:1:0.2 - 1:0.2 - 1.

[0012] Preferably, the average corrosion rate of the chromium boride-based cermet material is 8.46×10 -4 -4.29×10 -4 mm / h, the Vickers hardness is 1453.32 - 1786.78 HV, and the fracture toughness is 5.92 - 10.5 MPa·m 1 / 2 .

[0013] The present invention provides a preparation method of a chromium boride-based cermet material resistant to molten aluminum corrosion. The CrB2 powder and FeCrNiAlTi high-entropy alloy powder are ball-milled to obtain a mixed powder, and the mixed powder is sintered by spark plasma sintering to obtain the chromium boride-based cermet material. The temperature of the spark plasma sintering is 1300 - 1500 °C.

[0014] The chromium boride-based cermet material of the present invention can sinter the cermet material at a lower temperature by ball-milling and activating the CrB2 powder and FeCrNiAlTi high-entropy alloy powder, and then performing spark plasma sintering, so as to obtain a cermet material with excellent properties.

[0015] Preferably, the particle size of the CrB2 powder is 1 - 3 μm.

[0016] Controlling the particle size of the CrB2 powder within the above range results in the highest density of the finally obtained cermet. If the particle size of the raw material is too large, the density of the sintered cermet will decrease. If the particle size is too small, the surface activity is high, which is not conducive to ball-milling dispersion, and will also lead to a decrease in performance.

[0017] Preferably, the purity of the CrB2 powder ≥ 99.9%.

[0018] The inventors found that in the present invention, only by ball-milling the CrB2 powder and FeCrNiAlTi high-entropy alloy powder can a cermet material with excellent properties be obtained. If the CrB2 powder is directly ball-milled with Fe powder, Cr powder, Ni powder, Al powder, and Ti powder, the required cermet material cannot be obtained. The inventors found that if directly using elemental powders for ball-milling and mixing, on the one hand, it will cause the volatilization of Al, and on the other hand, the sintered cermet material will contain single phases of iron and nickel, thus reducing the performance of the cermet.

[0019] Preferably, the ball-milling method is wet ball-milling. The rotation speed of the wet ball-milling is 240 - 260 r / min, the wet ball-milling time is 3 - 5 h, the ball-to-material ratio is 3 - 5:1, and the process control agent for the wet ball-milling is absolute ethanol.

[0020] Preferably, the mixed powder is dried at 80 - 100 °C for 12 - 15 h under the condition of a vacuum degree of -0.08 to -0.1 MPa, and then subjected to spark plasma sintering.

[0021] Preferably, the heating rate of the spark plasma sintering is 50-100 °C / min, the holding time is 5-15 min, and the pressure is 30-50 MPa.

[0022] Preferably, the process for obtaining the FeCrNiAlTi high-entropy alloy powder is as follows: Fe powder, Cr powder, Ni powder, Al powder, and Ti powder are proportioned according to the design ratio and subjected to wet ball milling, and then dried to obtain the powder. The rotation speed of the wet ball milling is 280-320 r / min, the wet ball milling time is 60-80 h, the ball-to-material ratio is 8-10:1, and the process control agent for the wet ball milling is anhydrous ethanol.

[0023] The inventor found that during the mechanical alloying process, the parameters of the ball milling need to be effectively controlled. If the ball milling speed is too low, it is not sufficient to break the metal elemental particles, thus failing to achieve the effect of mechanical alloying. If the ball milling time is insufficient, complete mechanical alloying cannot be achieved. The ball-to-material ratio also has a great influence on the mechanical alloying process. By using the ball-to-material ratio within the scope of the present invention, mechanical alloying can be well realized. If the ball-to-material ratio is too low, the collision efficiency between the grinding balls and the powder particles will decrease, which will reduce the efficiency of mechanical alloying or even prevent mechanical alloying from occurring. If the ball-to-material ratio is too high, the probability of collision between the grinding balls will increase, which will also reduce the collision frequency between the grinding balls and the powder, and is not conducive to mechanical alloying.

[0024] Further preferably, the particle sizes of the Fe powder, Cr powder, Ni powder, Al powder, and Ti powder are all 1-3 μm.

[0025] Controlling the particle sizes of the Fe powder, Cr powder, Ni powder, Al powder, and Ti powder within the above range results in the highest density of the finally obtained cermet. If the particle size of the raw material is too large, the density of the sintered cermet will decrease. If the particle size is too small, the surface activity is high, which is not conducive to ball milling and dispersion, and will also lead to a decrease in performance.

[0026] Further preferably, the purities of the Fe powder, Cr powder, Ni powder, Al powder, and Ti powder are all ≥99.9%.

[0027] Further preferably, the drying is carried out under the condition that the vacuum degree is -0.08 to -0.1 MPa, the drying temperature is 80-100 °C, and the drying time is 12-15 h.

[0028] The present invention also provides an application of the chromium diboride-based cermet material, using the chromium diboride-based cermet material as a refractory aluminum corrosion-resistant material.

[0029] Beneficial effects:

[0030] In the present invention, FeCrNiAlTi high-entropy alloy is used as the bonding phase. The main purpose is to enhance the toughness of the cermet, make up for the large brittleness of pure chromium diboride ceramic, so that it not only has good molten aluminum corrosion resistance, but also has certain mechanical properties to meet industrial use. Preparing the cermet bulk material by ball milling and spark plasma sintering has the following advantages: First, ball milling can make the powder mixture more uniform, providing favorable conditions for subsequent sintering; Second, spark plasma sintering can sinter the cermet material at a lower temperature, which is beneficial to energy saving; Third, spark plasma sintering can quickly sinter the cermet material, improving production efficiency; Finally, spark plasma sintering can sinter a dense cermet bulk, obtaining a cermet material with excellent properties. The bonding phases of traditional cermet materials are mostly single elements such as Co, Nb, and Mo. Among them, Co is a strategic metal, while Nb and Mo are relatively expensive. The FeCrNiAlTi high-entropy alloy used in the present invention not only does not contain strategic metals, but also has easily available raw materials and relatively low costs, which can meet the requirements of industrial production.

[0031] The present invention provides a chromium diboride-based cermet material resistant to molten aluminum corrosion and its preparation method. The preparation process is simple, the raw materials are easily available, the cost is low, and it can meet industrial production. Brief Description of the Drawings

[0032] In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the following briefly introduces the drawings used in the description of the embodiments. The following described drawings are only some embodiments of the present invention. For those of ordinary skill in the art, without creative efforts, other drawings can be obtained based on these drawings.

[0033] Figure 1 It is the XRD pattern of the FeCrNiAlTi high-entropy alloy powder involved in Example 3 of the present invention.

[0034] Figure 2 It is the scanning electron microscope images of the corrosion interfaces of the cermet material specimens in Example 3 of the present invention in molten aluminum at 700 °C for 3 days, 6 days, 9 days, 12 days, and 15 days. Figure 2 Among them, (a)-(e) respectively correspond to the scanning electron microscope images of the corrosion interfaces at 3 days, 6 days, 9 days, 12 days, and 15 days of corrosion.

[0035] Figure 3 It is the curve graph of the change of the matrix thickness loss of the cermet material specimens in Example 3 of the present invention in molten aluminum at 700 °C with the corrosion time.

[0036] Figure 4 It is the curve graph of the change of the average corrosion rate of the cermet material specimens in Example 3 of the present invention in molten aluminum at 700 °C with the corrosion time.

[0037] Figure 5 It is the curve graph showing the variation relationship of the corrosion layer thickness of the cermet material sample in Example 3 of the present invention in Al liquid at 700°C with the corrosion time;

[0038] Figure 6 It is the hardness curve graph of chromium diboride-based cermet materials with different binder phase contents in Examples 1-3 of the present invention with the increase of the FeCrNiAlTi high-entropy alloy binder phase content;

[0039] Figure 7 It is the fracture toughness curve graph of chromium diboride-based cermet materials with different binder phase contents in Examples 1-3 of the present invention with the increase of the FeCrNiAlTi high-entropy alloy binder phase content. Detailed implementation manners

[0040] The following combines the accompanying drawings in the embodiments of the present invention to clearly and completely describe the technical solutions in the embodiments of the present invention. The described embodiments are only a part of the embodiments of the present invention, not all of the embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those of ordinary skill in the art without creative efforts belong to the protection scope of the present invention.

[0041] The following combines specific embodiments to detail the chromium diboride-based cermet material resistant to molten aluminum corrosion and its preparation method provided by the present invention, but they cannot be understood as limiting the protection scope of the present invention.

[0042] Example 1

[0043] A chromium diboride-based cermet material resistant to molten aluminum corrosion and its preparation method include the following steps;

[0044] (1) First sample preparation step: Weigh Fe powder, Cr powder, Ni powder, Al powder, and Ti powder with mass percentages of 23.135%, 21.54%, 24.315%, 11.18%, and 19.83% respectively. Their particle sizes are all 1-3 μm, and their purities are all ≥99.9%.

[0045] (2) Mechanical alloying step: Put a total of 40 grams of powder, including 9.254 grams of Fe powder, 8.616 grams of Cr powder, 9.726 grams of Ni powder, 4.472 grams of Al powder, and 7.932 grams of Ti powder, into a ball mill for mechanical alloying. The ball milling method is wet ball milling, the process control agent is anhydrous ethanol, the ball milling tank is a cemented carbide tank, the grinding balls are cemented carbide balls, the ball milling time is 60h, the ball-to-powder ratio is 10:1, the ball milling speed is 300r / min, and it stops for 15 minutes every 2 hours of rotation.

[0046] (3) First vacuum drying step: Put the FeCrNiAlTi high-entropy alloy powder into a vacuum drying oven for vacuum drying. The drying temperature is 80 °C, the vacuum degree is -0.1 MPa, and the drying time is 12 h. Finally, the FeCrNiAlTi high-entropy alloy powder with a duplex BCC structure is obtained. Figure 1 It is the XRD pattern of the FeCrNiAlTi high-entropy alloy powder. It can be seen from the figure that a duplex BCC structure has been formed.

[0047] (4) Second sample preparation step: Weigh 5 g of FeCrNiAlTi high-entropy alloy powder and 45 g of CrB2 powder and put them into a sample bag.

[0048] (5) Ball milling and powder mixing step: Put the CrB2 powder with a mass ratio of 90% and the FeCrNiAlTi high-entropy alloy powder with a mass ratio of 10% into a ball mill for ball milling and powder mixing. The ball milling method is wet ball milling, the process control agent is anhydrous ethanol, the ball milling tank is a cemented carbide tank, the grinding balls are cemented carbide balls, the ball milling time is 3 h, the ball-to-powder ratio is 3:1, the ball milling speed is 250 r / min, and it stops for 15 minutes every 2 hours of rotation.

[0049] (6) Second vacuum drying step: Put the mixed powder into a vacuum drying oven for vacuum drying. The drying temperature is 80 °C, the vacuum degree is -0.1 MPa, and the drying time is 12 h.

[0050] (7) Spark plasma sintering step: Put the dried mixed powder into a cylindrical graphite mold, and then put it into a sintering device for sintering. The sintering process is as follows: Heat up from room temperature to 1400 °C at a heating rate of 100 °C / min and hold for 5 minutes at 1400 °C. The pressure applied during sintering is 50 MPa. After sintering, it is cooled with the furnace and demolded to obtain the chromium boride-based metal ceramic material.

[0051] Example 2

[0052] Compared with the method of Example 1, the method of Example 2 is the same in other aspects except for the different second sample preparation step in step (4). The second sample preparation step in Example 2: Weigh 7.5 g of FeCrNiAlTi high-entropy alloy powder and 42.5 g of CrB2 powder and put them into a sample bag. The particle sizes of the Fe powder, Cr powder, Ni powder, Al powder, Ti powder and CrB2 powder are all 1 - 3 μm, and the purities are all ≥99.9%.

[0053] Example 3

[0054] The method of Example 3 is the same as that of Example 1 except for the second sample preparation step in step (4), and the rest are the same, so they will not be elaborated here. The second sample preparation step in step (4) of Example 3: Weigh 10 grams of FeCrNiAlTi high-entropy alloy powder and 40 grams of CrB2 powder and put them into a sample bag. The particle sizes of Fe powder, Cr powder, Ni powder, Al powder, Ti powder and CrB2 powder are all 1-3 μm, and the purities are all ≥99.9%.

[0055] The properties of the chromium boride-based cermet materials prepared in Examples 1-3 were tested respectively:

[0056] (1) Refractory aluminum corrosion test

[0057] The refractory aluminum corrosion resistance of the chromium boride-based cermet materials prepared in Examples 1-3 can be reflected by the thickness of the corrosion layer formed in the aluminum liquid, the thickness loss of the matrix in the aluminum liquid and the average corrosion rate. The present invention uses the depth method to calculate the average corrosion rate v, and its calculation formula is:

[0058] v = (a - b) / 2t

[0059] Where a is the thickness of the specimen before corrosion, b is the thickness of the specimen after corrosion, a - b is the thickness loss of the matrix, and t is the corrosion time.

[0060] Refractory aluminum corrosion test: Before the refractory aluminum corrosion test, use a vernier caliper with digital display to measure the thickness of the chromium boride-based cermet specimens in Examples 1-3. The measurement method is to measure 5 times at different positions of the specimen and then take the average value. Then put the samples with measured thickness into an ultrasonic cleaning machine to clean the oil and other impurities on the surface of the samples. Finally, place each specimen in a preheated graphite crucible containing molten aluminum liquid, and then put these graphite crucibles into a pit furnace for heating. By setting the program, the temperature in the pit furnace is kept constant at 700 °C. Finally, take out the samples after 3 days, 6 days, 9 days, 12 days, and 15 days of corrosion respectively. Subsequently, use a wire cutting machine to cut the corroded samples along the cross-section, and then observe the cross-section of the corroded samples under a scanning electron microscope (SEM), and measure the thickness of the matrix and the thickness of the corrosion layer. The measurement method is to measure 5 times at different positions and then take the average value.

[0061] The scanning electron microscope images of the cross-sections of the cermet specimens in Example 3 after 3 days, 6 days, 9 days, 12 days, and 15 days of corrosion in molten aluminum liquid at 700 °C are shown in Figure 2 (a)-(e) respectively. It can be seen from the figure that no new corrosion products appear in the corrosion layer as the corrosion time prolongs, only the thickness of the corrosion layer increases.

[0062] The relationship between the matrix thickness loss of the cermet specimen in Example 3 after being corroded in molten aluminum at 700°C for 3 days, 6 days, 9 days, 12 days, and 15 days and the corrosion time is as follows Figure 3 shown. It can be seen from Figure 3 that the thickness loss of the matrix shows an approximately linear relationship with the corrosion time, indicating that its interfacial reaction is controlled by the dissolution of the corrosion products.

[0063] The relationship between the average corrosion rate of the cermet specimen in Example 3 after being corroded in molten aluminum at 700°C for 3 days, 6 days, 9 days, 12 days, and 15 days and the corrosion time is as follows Figure 4 shown. It can be seen from Figure 4 that the average corrosion rate of the cermet specimen in Example 3 shows a negative correlation with the corrosion time, indicating that the rate of matrix thickness loss cannot keep up with the increase in corrosion time, thus indicating that the prepared cermet specimen has good resistance to molten aluminum corrosion.

[0064] The relationship between the corrosion layer thickness of the cermet specimen in Example 3 after being corroded in molten aluminum at 700°C for 3 days, 6 days, 9 days, 12 days, and 15 days and the corrosion time is as follows Figure 5 shown. It can be seen from Figure 5 that the corrosion layer thickness of the cermet specimen in Example 3 shows a positive correlation with the corrosion time, indicating that the thickness of the corrosion layer continuously increases with the extension of the corrosion time, but the increase amplitude is not large and there is no spalling of the corrosion layer, indicating that the prepared cermet specimen has good resistance to molten aluminum corrosion.

[0065] Vickers hardness test

[0066] The Vickers hardness of the cermet materials prepared in Examples 1 - 3 was tested using a Vickers hardness tester. The applied force was 98 N and the loading time was 15 s. Five different positions were selected for measurement on each specimen. The relationship between the Vickers hardness of the cermet materials prepared in Examples 1 - 3 and the change in the binder phase content is as follows Figure 6 shown. It can be seen from Figure 6 that the Vickers hardness of the prepared cermet materials decreases with the increase in the binder phase content.

[0067] Fracture toughness test

[0068] After testing the Vickers hardness of the cermet specimen, indentations and cracks will appear on the specimen surface. Therefore, we can use the indentation method to calculate the fracture toughness of the cermet specimen. The calculation formula is as follows:

[0069] K IC =0.203×[(a1 + a2) / 2] 1 / 2×[(c1 + c2) / (a1 + a2)] -3 / 2 ×HV

[0070] Wherein, KIC is the fracture toughness, a1 and a2 are respectively half of the indentation diagonal length, c1 and c2 are respectively half of the indentation crack length, and HV is the Vickers hardness of the specimen.

[0071] The variation relationship of the Vickers hardness of the cermet materials prepared in Examples 1 - 3 with the change of the binder phase content is as Figure 7 shown. It can be seen from the figure that in the range where the binder phase content is 10% - 20%, the fracture toughness of the cermet materials prepared with the increase of the binder phase content is improved. The fracture toughness of the chromium boride - based cermet specimen prepared in Example 3 can reach 10.5 MPa·m 1 / 2 , making up for the deficiency of the large brittleness of pure chromium boride ceramic materials and being able to be applied to industrial production.

[0072] Comparative Example 1

[0073] Other conditions are the same as those in Example 3, only the sintering temperature is different. The sintering temperature used in Comparative Example 1 is 1600 °C. The sample of Comparative Example 1 was not sintered into shape because the sintering temperature was too high, resulting in too much liquid phase formed and part of the liquid phase flowing out. The remaining samples were broken after sintering and covered with cracks on the surface, and subsequent tests could not be carried out.

[0074] Comparative Example 2

[0075] Other conditions are the same as those in Example 3, only the particle size of the CrB2 powder is 20 μm. After the particle size of the CrB2 powder increased, compared with Example 3, the density of Comparative Example 2 decreased by about 10%, resulting in a great decrease in its molten aluminum corrosion resistance, and the average corrosion rate decreased by nearly an order of magnitude.

[0076] Comparative Example 3

[0077] Other conditions are the same as those in Example 3. Only when 40 g of powders including 9.254 g of Fe powder, 8.616 g of Cr powder, 9.726 g of Ni powder, 4.472 g of Al powder, and 7.932 g of Ti powder were put into a ball mill for mechanical alloying, the ball - to - powder ratio was 12:1. After increasing the ball - to - powder ratio, compared with Example 3, the time required for mechanical alloying in Comparative Example 4 was extended, the ball - milling time reached 90 - 120 h, and at the same time, the wear of the grinding balls was aggravated and some grinding balls were slightly deformed. And due to the introduction of trace impurities during long - time ball - milling, its performance decreased slightly. Although the small change in the ball - to - powder ratio has less impact on the final performance than the parameters changed in other comparative examples, it increases the time and economic cost required for preparing the samples and has a slight adverse effect on the final performance.

[0078] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the embodiments of the present invention rather than to limit them. Those of ordinary skill in the art should understand that without departing from the principle of the present invention, the modification and refinement of the technical solutions of the present invention should also be regarded as the protection scope of the present invention.

Claims

1. A preparation method of a chromium boride-based cermet material, characterized in that: The CrB2 powder and FeCrNiAlTi high-entropy alloy powder are ball-milled to obtain a mixed powder, and the mixed powder is sintered by spark plasma sintering to obtain a chromium boride-based cermet material. The temperature of the spark plasma sintering is 1300-1500 °C; The particle size of the CrB2 powder is 1-3 μm; The chromium boride-based cermet material uses chromium boride as the hard phase and FeCrNiAlTi high-entropy alloy as the binder phase. The mass percentage of the FeCrNiAlTi high-entropy alloy in the cermet material is 10%-20%.

2. The preparation method of a chromium boride-based cermet material according to claim 1, characterized in that: The ball-milling method is wet ball-milling. The rotation speed of the wet ball-milling is 240-260 r / min, the wet ball-milling time is 3-5 h, the ball-to-material ratio is 3-5:1, and the process control agent for the wet ball-milling is anhydrous ethanol.

3. The preparation method of a chromium boride-based cermet material according to claim 1, characterized in that: The mixed powder is dried at 80-100 °C for 12-15 h under the condition of a vacuum degree of -0.08~-0.1 MPa, and then spark plasma sintering is carried out; The heating rate of the spark plasma sintering is 50-100 °C / min, the heat preservation time is 5-15 min, and the pressure is 30-50 MPa.

4. The preparation method of a chromium boride-based cermet material according to claim 1, wherein: The process for obtaining the FeCrNiAlTi high-entropy alloy powder is as follows: Fe powder, Cr powder, Ni powder, Al powder, and Ti powder are proportioned according to the design ratio and subjected to wet ball-milling, and then dried to obtain it. The rotation speed of the wet ball-milling is 280-320 r / min, the wet ball-milling time is 60-80 h, the ball-to-material ratio is 8-10:1, and the process control agent for the wet ball-milling is anhydrous ethanol.

5. The preparation method of a chromium boride-based cermet material according to claim 4, characterized in that: The particle sizes of the Fe powder, Cr powder, Ni powder, Al powder, and Ti powder are all 1-3 μm; The drying is carried out under the condition of a vacuum degree of -0.08~-0.1 MPa, the drying temperature is 80-100 °C, and the drying time is 12-15 h.

6. The preparation method of a chromium boride-based cermet material according to claim 1, characterized in that: In the binder phase, by molar ratio: Fe:Cr:Ni:Al:Ti = 1:1:1:0.2-1:0.2-1.

7. The preparation method of a chromium boride-based cermet material according to claim 1, characterized in that: The average corrosion rate of the chromium diboride-based cermet material is 8.46×10 -4 -4.29×10 -4 mm / h, the Vickers hardness is 1453.32 - 1786.78 HV, and the fracture toughness is 5.92 - 10.5 MPa·m 1 / 2 .

8. Use of a chromium boride-based cermet material prepared by the preparation method according to any one of claims 1 to 3, characterized in that: The chromium boride-based cermet material is used as a refractory aluminum corrosion-resistant material.

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