CN115976391B - High-temperature-resistant multi-principal-element intermetallic compound and preparation method thereof - Google Patents
High-temperature-resistant multi-principal-element intermetallic compound and preparation method thereof Download PDFInfo
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Abstract
The invention relates to a novel metal material and the preparation field thereof, in particular to a high-temperature-resistant multi-principal-element intermetallic compound and the preparation method thereof. The invention aims to meet urgent requirements of the rapid development of industries such as modern aerospace and the like on advanced light high-temperature structural materials, and provides a light multi-principal-element intermetallic compound with excellent room-temperature and high-temperature mechanical properties and a preparation method thereof. The invention relates to a high temperature resistant multi-principal element intermetallic compound which consists of Ni, co, cr, ti, al, ta and B elements. The density of the high temperature resistant multi-principal element intermetallic compound is lower than that of the traditional high temperature alloy, the working temperature can reach 700-900 ℃, and the high temperature resistant multi-principal element intermetallic compound can be prepared by adopting methods of casting, hot working, powder metallurgy, additive manufacturing and the like, and is suitable for the production of hot end parts in the industrial fields of aviation, aerospace, civil use and the like.
Description
Technical Field
The invention belongs to the field of metal materials and preparation thereof, and particularly relates to a high-temperature-resistant multi-principal-element intermetallic compound and a preparation method thereof.
Background
The development of advanced aerospace vehicles is a constantly pursuing development goal. With the rise of flying speed, higher requirements are put on the specific gravity and the room temperature high temperature performance of the engine and some hot end part materials.
As the earliest developed high temperature structural materials, nickel-based superalloys have been widely used in advanced aerospace engines and some hot-end components thereof by virtue of their excellent high temperature strength, structural stability and corrosion resistance. However, the addition of high-density refractory elements in large amounts, while improving the temperature bearing capacity of nickel-based superalloys to some extent, inevitably increases the alloy density, which tends to increase the weight of the aerospace vehicle and thereby reduce the speed of the vehicle. Intermetallic compounds have lower density, higher high temperature specific strength and excellent oxidation resistance than nickel-based superalloys. Therefore, intermetallic compounds become candidates for advanced lightweight high temperature metallic structural materials. However, the poor room temperature plasticity problem severely limits the application of intermetallic structural materials. At present, multi-principal alloy is attracting attention. In particular, the multi-principal element alloy with the face-centered cubic structure is expected to be applied as a new generation of structural material because the perfect combination of strength and plasticity is realized in a wide temperature range (liquid nitrogen temperature to room temperature). However, such multi-principal alloy materials are not strong at high temperatures, thereby limiting their use in high temperature environments. It is thus seen that in order to accommodate the continued advancement of the aerospace industry, it is necessary to find a lightweight high temperature resistant structural material that has both good plasticity at room temperature and high temperature strength.
Disclosure of Invention
The invention aims to solve the technical problems that the light high-temperature structural material of the existing aerospace craft cannot meet the requirements of good room-temperature plasticity and high-temperature strength. And provides a high temperature resistant multi-principal element intermetallic compound and a preparation method thereof.
The invention relates to a high-temperature-resistant multi-principal-element intermetallic compound, which comprises the following components in percentage by atom: 8 to 16 percent, 6 to 12 percent of Ti, 6 to 12 percent of Al, 2 to 6 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein the atomic percentage of Ni and Co elements is 1:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta.
Further, the atomic percentage of the Ni and Co elements is 1:1.5-3:1, and the total atomic content of the Ni and Co is 2-3 times of the total atomic content of the Al, ti and Ta.
Further, the multi-principal element intermetallic compound is prepared from Cr:8 to 16 percent, 8 to 10 percent of Ti, 8 to 10 percent of Al, 3 to 5 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein the atomic percentage of Ni and Co elements is 1:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta.
Further, the multi-principal element intermetallic compound is prepared from Cr:8 to 16 percent, 10 to 12 percent of Ti, 10 to 12 percent of Al, 5 to 6 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein the atomic percentage of Ni and Co elements is 1:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta.
Further, the preparation method is casting, deformation processing, powder metallurgy or additive manufacturing.
Further, the casting method is vacuum non-consumable electrode arc melting, vacuum consumable electrode arc melting or vacuum induction melting.
Further, the deformation processing method is a forging and rolling method at normal temperature or a forging, rolling and extruding method at 800-1300 ℃.
Further, the powder metallurgy is to prepare the high-temperature-resistant multi-principal-element intermetallic compound by mixing Ni, co, cr, ti, al, ta with B simple substance powder, or mechanically alloying the simple substance powder, or prealloying the simple substance powder and then sintering.
Further, the sintering process is pressureless sintering, pressure sintering, spark plasma sintering or energy field assisted sintering.
Further, the additive manufacturing is a laser/electron beam selective melting technique, a laser/electron beam/arc fuse deposition technique, or a laser powder deposition technique.
The scheme principle of the invention is as follows:
according to the invention, the Ni, co, cr, ti, al, ta and B elements with specific contents are combined, so that the atomic ratio of Ni and Co elements needs to be controlled, and the ratio of the sum of the atomic contents of Ni and Co to the sum of the atomic contents of Al, ti and Ta is controlled. The atomic ratio of Ni and Co elements is controlled to form a small amount of solid solution phase of non-intermetallic compound at the grain boundary, the grain boundary is toughened, so that the room temperature plasticity is obviously improved, the relation between the total of three element atoms of Ti+Al+Ta and the total of two element atoms of Ni+Co is controlled, so that the two elements reach the optimal ratio state, the effect that the volume fraction of the main phase of the multi-element intermetallic compound is obviously increased (Ni and Co atoms occupy the sub-lattice of one type of crystal structure of the intermetallic compound, and Al, ti and Ta atoms occupy the sub-lattice of the other type of crystal structure of the intermetallic compound, so that the sub-lattice is multi-main, the effect of uniformly bonding and strengthening the multi-atom solid solution is achieved, and the purposes of good room temperature plasticity and higher high-temperature strength of the light high-temperature resistant multi-element intermetallic compound are realized.
The main phase prepared by the invention is L1 2 Intermetallic compound of crystal structure, multi-principal-component of crystal structure sub-lattice of intermetallic compound (L1 2 The two types of sub-lattices of the crystal structure have multiple element occupation, and the content of the occupied elements is high, so that the aim of improving the mixed entropy of the sub-lattices is fulfilled, and the method is not only the multi-principal diversification of the sub-lattices. Through the multiple principal components of the sub-lattice, the intermetallic compound can not only obviously improve the strength (solid solution strengthening) due to the multiple principal components, but also obviously improve the room temperature brittleness due to the fact that the bonding approach of the intermetallic compound is regulated by the multiple principal components, thereby solving the room temperature brittleness problem of the traditional intermetallic compound material. Meanwhile, the multi-principal element intermetallic compound has higher density than that of high-temperature alloy due to the fact that the multi-principal element intermetallic compound contains high-density elements such as Al and Ti, and the like, so that the multi-principal element intermetallic compound has excellent room temperature and high temperature specific strength, and is a light high-temperature resistant metal structural material with important application value.
The invention discovers that the element combination has important influence on forming the high temperature resistant multi-principal element intermetallic compound through carefully adjusting the types and the contents of the elements. Mainly, ni element has excellent alloying ability, which provides necessary conditions for multi-principal component constitution and alloy property improvement. The addition of Co promotes the solid solution strengthening effect, thereby increasing the strength of the alloy and improving the intrinsic brittleness of the intermetallic compound. The addition of a large amount of Al element and Ti element ensures the generation of a main phase intermetallic compound phase on one hand and improves the high-temperature strength of the alloy; on the other hand, the density of the alloy can be effectively reduced, and the application range of the alloy is expanded. The Ta element not only increases the use temperature of the alloy, but also promotes the generation of intermetallic compound phases. The moderate temperature brittleness problem of the alloy can be effectively improved by adding a proper amount of Cr element. The addition of element B can reduce the problem of brittleness of grain boundary and lower density, so that the plasticity of the material at room temperature is further improved. Meanwhile, the combination of elements such as Ni, co, cr, ti, al, ta with higher content is controlled, and the ratio of Ni to Co and the ratio of the total content of Ni and Co to the total content of the atoms of the other elements are controlled, wherein the atomic percentage of the Ni and Co elements is 1:1-3:1, and the total content of Ni and Co is 2-5 times of the total content of Al, ti and Ta. The multi-principal element of the intermetallic compound crystal structure sub-lattice is realized, so that the intermetallic compound can not only obviously improve the strength (solid solution strengthening) due to the multi-principal element, but also obviously improve the room temperature brittleness due to the fact that the multi-principal element adjusts the bonding of the intermetallic compound, effectively solve the problems of high room temperature brittleness, unavailable strength and plasticity of the traditional intermetallic compound material, and the like, and be beneficial to the wide application of the high temperature resistant intermetallic compound structural material.
The high temperature resistant multi-principal element intermetallic compound can be prepared by adopting methods of casting, hot working, powder metallurgy, additive manufacturing and the like, has lower density than the existing high temperature alloy, can reach 700-900 ℃, and is suitable for the production of hot end parts in the industrial fields of aviation, aerospace, civil use and the like.
The beneficial effects of the invention are as follows:
1) The high temperature resistant multi-principal element intermetallic compound obtained by the invention has the advantages that although the principal phase is still the intermetallic compound, the long-range order structural characteristics of the intermetallic compound are maintained, meanwhile, as a plurality of elements with higher content are added together, the chemical composition characteristics of the multi-principal elements of the crystal structure of the intermetallic compound are formed, the purpose of improving the mixed entropy of the sub-lattice is achieved, and therefore, a high temperature resistant structural material with excellent mechanical property is formed, and compared with the traditional intermetallic compound and multi-principal element alloy, the high temperature resistant structural material is obviously different.
2) The high temperature resistant multi-principal element intermetallic compound obtained by the invention integrates the advantages of three structural materials of high temperature alloy, multi-principal element alloy and intermetallic compound, not only has the room temperature and high temperature plasticity and strength of the high temperature alloy, but also has the light weight and excellent high temperature resistance of the intermetallic compound, and the solid solution strengthening effect is further increased by increasing the mixed entropy of the alloy crystal structure sub-lattice through multi-principal element, thereby realizing the improvement of specific gravity reduction, room temperature and high temperature strength and plasticity, and reaching the excellent comprehensive performance which is not possessed by the prior main high temperature metal structural material.
3) The room temperature elongation of the high temperature resistant multi-principal element intermetallic compound obtained by the invention exceeds 6%, the room temperature brittleness problem of the traditional intermetallic compound is solved, and the wide application of the multi-principal element intermetallic compound structural material can be realized. The density of the high temperature resistant multi-principal element intermetallic compound obtained by the invention is only 6.5-7.5 g/cm 3 Is lower than the traditional nickel-based superalloy>8.2g/cm 3 ) The weight of the hot end parts of the advanced aerospace craft can be reduced. The high temperature yield strength of the high temperature resistant multi-principal element intermetallic compound obtained by the invention is higher than the room temperature yield strength, which is the characteristic that common high temperature alloy and multi-principal element alloy do not have, and is more suitable for the application of high temperature parts.
4) The high-temperature-resistant multi-principal-element intermetallic compound obtained by the invention can be prepared by adopting a traditional preparation method of a high-temperature metal structural material, does not need to add extra special equipment, and can also be used for large-scale industrial production of hot-end parts by adopting the existing high-temperature metal material production equipment, thereby having important commercial value.
5) The high-temperature-resistant multi-principal-element intermetallic compound and the preparation method thereof provided by the invention have wide application prospects in the fields of aerospace and the like, and have remarkable economic benefits.
Drawings
FIG. 1 is a diagram of an embodiment Ni 47.9 Co 26 Al 8 Ti 8 Ta 2 Cr 8 B 0.1 Multi-principal intermetallic compoundIs a microscopic structure diagram of (2);
FIG. 2 is a diagram of two Ni embodiments 47.9 Co 24 Al 9 Ti 9 Ta 2 Cr 8 B 0.1 Microstructural map of multi-principal intermetallic compound;
FIG. 3 is a diagram of three Ni of the embodiment 47.9 Co 22 Al 10 Ti 10 Ta 2 Cr 8 B 0.1 Microstructural map of multi-principal intermetallic compounds.
Detailed Description
It will be understood by those of ordinary skill in the art that the foregoing embodiments are specific examples of carrying out the invention and that various changes in form and details may be made therein without departing from the spirit and scope of the invention.
For the purposes of clarity, technical solutions and advantages of embodiments of the present invention, the following detailed description will clearly illustrate the spirit of the present disclosure, and any person skilled in the art, after having knowledge of the embodiments of the present disclosure, may make alterations and modifications to the technology taught by the present disclosure without departing from the spirit and scope of the present disclosure.
The exemplary embodiments of the present invention and the descriptions thereof are intended to illustrate the present invention, but not to limit the present invention.
Embodiment one:
the high temperature resistant multi-principal element intermetallic compound of the embodiment has the component ratio of Ni 50 Co 24.5 Cr 8 Ti 7.5 Al 7.5 Ta 2.4 B 0.1 (at.%) the atomic content ratio of Ni and Co elements in the chemical composition is 2.04:1, and the sum of the atomic contents of Ni and Co is 4.26 times the sum of the atomic contents of Al, ti and Ta. The preparation method comprises the following steps:
step one, the total mass of each alloy sample is 120g. According to the component proportion, the simple substance raw material of high purity Ni, co, cr, ti, al, ta, B powder or granule (the purity is more than 99.99 percent) is weighed, and the error is +/-0.001 g. Placing the weighed raw materials into a copper crucible in a vacuum non-consumable electrode arc furnace, adjusting a vacuum non-consumable electrode arc gun to enable the gun tip to be 1-2 mm away from the raw materials, and then closing a furnace door;
step two, opening the extraction valve to carry out vacuumizing, so that the vacuum degree in the furnace reaches 10 -4 The MPa is then filled with a protective gas, namely high-purity argon to 0.004MPa for scrubbing;
step three, observing the condition in the furnace chamber through an observation port on the side wall of the non-consumable vacuum arc furnace, simultaneously opening a circulating water cooling system, and observing whether the condenser pipe is completely immersed in circulating cooling water so as to dissipate heat;
and fourthly, switching on a power supply to electrify the arc gun for arc striking, slowly lifting the arc gun and increasing current after arc light appears, wherein the current in the smelting process is not more than 400A, and the distance between the arc gun and the raw materials is kept at 1-2 mm. When the raw materials are completely melted, an electromagnetic stirring switch is turned on, and an external magnetic field is applied to stir so as to ensure that the components are uniform, and each button ingot is smelted for about 3 minutes (including magnetic stirring for 10 s). Slowly reducing current and lifting an arc gun after smelting is finished, and waiting for the button ingot to be naturally cooled and solidified in the water-cooled copper crucible after a power supply is turned off;
turning over the cooled button ingot by using a mechanical arm, correcting the position of an arc gun, electrifying and reheating, and repeatedly smelting for 4 times to ensure that the alloy components are uniform;
step six, smelting for the last time in a mode of gradually reducing current to ensure that the arc light moves at a constant speed along the edge of the button ingot until the current is reduced to 0A, thus finishing Ni 50 Co 25 Cr 7.5 Ti 7.5 Al 7.5 Ta 2.4 B 0.1 Preparation of multi-principal intermetallic compounds. The main purpose is to adjust the shape of the button ingot to make the edge smooth and round, and facilitate the subsequent mechanical processing.
In connection with the description of the figure, ni 50 Co 25 Cr 7.5 Ti 7.5 Al 7.5 Ta 2.4 B 0.1 The alloy solidification structure presents dendrite morphology and consists of two phases, namely, the dark gray main phase is a multi-main-element intermetallic compound phase, and the volume fraction of the multi-main-element intermetallic compound main phase reaches more than 85 percent, which shows that the embodiment prepares the high-temperature-resistant multi-main-element goldAn intermetallic compound. Table I is Ni 47.9 Co 26 Al 8 Ti 8 Ta 2 Cr 8 B 0.1 As can be seen from the table, the elongation of the alloy at room temperature reaches 8.5%, the tensile strength at 800 ℃ reaches 615MPa, and the yield strength at 800 ℃ is 30MPa higher than the room temperature yield strength, which indicates that the alloy of the embodiment has excellent room temperature high temperature mechanical properties.
TABLE 1
Embodiment two:
the high temperature resistant multi-principal element intermetallic compound of the embodiment has the component ratio of Ni 47.5 Co 22.5 Cr 9 Ti 9 Al 9 Ta 2.95 B 0.05 (at.%) the atomic content ratio of Ni and Co elements in the chemical composition is 2.11:1, and the sum of the atomic contents of Ni and Co is 3.34 times the sum of the atomic contents of Al, ti and Ta. The preparation method comprises the following steps:
step one, the total mass of each alloy sample is 120g. According to the component proportion, the simple substance raw material of high purity Ni, co, cr, ti, al, ta, B powder or granule (the purity is more than 99.99 percent) is weighed, and the error is +/-0.001 g. Placing the weighed raw materials into a copper crucible in a vacuum non-consumable electrode arc furnace, adjusting a vacuum non-consumable electrode arc gun to enable the gun tip to be 1-2 mm away from the raw materials, and then closing a furnace door;
step two, opening the extraction valve to carry out vacuum pumping, so that the vacuum degree in the furnace reaches 5 multiplied by 10 -4 Charging protective gas high-purity argon to 0.003MPa for scrubbing;
step three, observing the condition in the furnace chamber through an observation port on the side wall of the non-consumable vacuum arc furnace, simultaneously opening a circulating water cooling system, and observing whether the condenser pipe is completely immersed in circulating cooling water so as to dissipate heat;
and fourthly, switching on a power supply to electrify the arc gun for arc striking, slowly lifting the arc gun and increasing current after arc light appears, wherein the current in the smelting process is not more than 400A, and the distance between the arc gun and the raw materials is kept at 1-2 mm. When the raw materials are completely melted, an electromagnetic stirring switch is turned on, and an external magnetic field is applied to stir so as to ensure that the components are uniform, and each button ingot is smelted for about 3 minutes (including magnetic stirring for 10 s). Slowly reducing current and lifting an arc gun after smelting is finished, and waiting for the button ingot to be naturally cooled and solidified in the water-cooled copper crucible after a power supply is turned off;
turning over the cooled button ingot by using a mechanical arm, correcting the position of an arc gun, electrifying and reheating, and repeatedly smelting for 6 times to ensure that the alloy components are uniform;
step six, smelting for the last time in a mode of gradually reducing current to ensure that the arc light moves at a constant speed along the edge of the button ingot until the current is reduced to 0A, thus finishing Ni 47.5 Co 22.5 Cr 9 Ti 9 Al 9 Ta 2.95 B 0.05 Preparation of multi-principal intermetallic compounds. The main purpose is to adjust the shape of the button ingot to make the edge smooth and round, and facilitate the subsequent mechanical processing.
In connection with the description of the figure II, ni 47.5 Co 22.5 Cr 9 Ti 9 Al 9 Ta 2.95 B 0.05 The alloy solidification structure presents dendrite morphology, the main phase is a multi-main-element intermetallic compound phase, the number of secondary phases distributed among crystals is small, and the volume fraction of the multi-main-element intermetallic compound main phase reaches more than 90%, which indicates that the high-temperature-resistant multi-main-element intermetallic compound is prepared in the embodiment. Table II is Ni 47.5 Co 22.5 Cr 9 Ti 9 Al 9 Ta 2.95 B 0.05 As can be seen from the table, the elongation of the alloy at room temperature reaches 8%, the tensile strength at 800 ℃ reaches 712MPa, and the yield strength at 800 ℃ is 26MPa higher than the room temperature yield strength, indicating that the alloy of the embodiment has excellent room temperature heightThermal mechanical properties.
TABLE 2
Embodiment III:
the high temperature resistant multi-principal element intermetallic compound of the embodiment has the component ratio of Ni 45 Co 23 Cr 9.5 Ti 9.5 Al 9.5 Ta 3.45 B 0.05 (at.%) the atomic content ratio of Ni and Co elements in the chemical composition is 1.957:1, and the sum of the atomic contents of Ni and Co is 3.03 times the sum of the atomic contents of Al, ti and Ta. The preparation method comprises the following steps:
step one, the total mass of each alloy sample is 120g. According to the component proportion, the simple substance raw material of high purity Ni, co, cr, ti, al, ta, B powder or granule (the purity is more than 99.99 percent) is weighed, and the error is +/-0.001 g. Placing the weighed raw materials into a copper crucible in a vacuum non-consumable electrode arc furnace, adjusting a vacuum non-consumable electrode arc gun to enable the gun tip to be 1-2 mm away from the raw materials, and then closing a furnace door;
step two, opening the extraction valve to carry out vacuum pumping to ensure that the vacuum degree in the furnace reaches 2 multiplied by 10 -4 The MPa is then filled with a protective gas, namely high-purity argon to 0.004MPa for scrubbing;
step three, observing the condition in the furnace chamber through an observation port on the side wall of the non-consumable vacuum arc furnace, simultaneously opening a circulating water cooling system, and observing whether the condenser pipe is completely immersed in circulating cooling water so as to dissipate heat;
and fourthly, switching on a power supply to electrify the arc gun for arc striking, slowly lifting the arc gun and increasing current after arc light appears, wherein the current in the smelting process is not more than 400A, and the distance between the arc gun and the raw materials is kept at 1-2 mm. When the raw materials are completely melted, an electromagnetic stirring switch is turned on, and an external magnetic field is applied to stir so as to ensure that the components are uniform, and each button ingot is smelted for about 3 minutes (including magnetic stirring for 10 s). Slowly reducing current and lifting an arc gun after smelting is finished, and waiting for the button ingot to be naturally cooled and solidified in the water-cooled copper crucible after a power supply is turned off;
turning over the cooled button ingot by using a mechanical arm, correcting the position of an arc gun, electrifying and reheating, and repeatedly smelting for 5 times to ensure that the alloy components are uniform;
step six, smelting for the last time in a mode of gradually reducing current to ensure that the arc light moves at a constant speed along the edge of the button ingot until the current is reduced to 0A, thus finishing Ni 47.5 Co 22.5 Cr 9 Ti 9 Al 9 Ta 2.95 B 0.05 Preparation of multi-principal intermetallic compounds. The main purpose is to adjust the shape of the button ingot to make the edge smooth and round, and facilitate the subsequent mechanical processing.
In combination with the description of the third figure, ni 45 Co 23 Cr 9.5 Ti 9.5 Al 9.5 Ta 3.45 B 0.05 The alloy solidification structure presents dendrite morphology, the main phase is a multi-main-element intermetallic compound phase, the number of secondary phases distributed among crystals is small, and the volume fraction of the multi-main-element intermetallic compound main phase reaches more than 90%, which indicates that the high-temperature-resistant multi-main-element intermetallic compound is prepared in the embodiment. Table III is Ni 45 Co 23 Cr 9. 5 Ti 9.5 Al 9.5 Ta 3.45 B 0.05 As can be seen from the table, the tensile strength of the multi-principal-element intermetallic compound exceeds 1GPa, the elongation reaches 7%, the tensile strength at 800 ℃ reaches 890MPa, and the yield strength at 800 ℃ is 18MPa higher than the room temperature yield strength, which indicates that the alloy of the embodiment has excellent room temperature high temperature mechanical properties.
TABLE 3 Table 3
Embodiment four:
this example is a comparative example.
The first difference between this embodiment and the first embodiment is that: the components with atomic percentages of Ni and Co below 1:1 and above 3:1 are proportioned, and the components with atomic percentages of Ni and Co below 2 and above 5 are proportioned. Which is the same as in the first embodiment.
The preparation method of example one was used, and the composition and the results of the room temperature mechanical properties are shown in Table 4. As can be seen from Table 4, the mechanical properties at room temperature are far lower than those of the above examples, indicating that the high temperature resistant multi-principal element intermetallic compound with excellent mechanical properties can be formed only by the composition range and the compounding ratio of the present invention.
TABLE 4 Table 4
In addition to the specific examples described above, all modifications or variations in the components obtained in accordance with the component ranges of the present invention, the preparation methods, and the improvements or modifications made on the basis of the present invention are included in the scope of the present patent.
Claims (3)
1. The high temperature resistant multi-principal element intermetallic compound is characterized in that the multi-principal element intermetallic compound comprises the following components in percentage by atom: 8 to 16 percent, 6 to 12 percent of Ti, 6 to 12 percent of Al, 2 to 6 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein, the atomic percentage of Ni and Co elements is 2.04:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta;
the preparation method of the high-temperature-resistant multi-principal-element intermetallic compound comprises the following steps:
weighing Ni, co, cr, ti, al, ta, B powder or granular simple substance raw materials with the purity of more than 99.99 percent according to the component proportion, placing the weighed raw materials into a copper crucible in a vacuum non-consumable electrode arc furnace, adjusting the vacuum non-consumable electrode arc gun to enable the gun tip to be 1-2 mm away from the raw materials, and then closing the furnace door;
step two, opening the extraction valve to carry out vacuumizing, so that the vacuum degree in the furnace reaches 10 -4 The MPa is then filled with a protective gas, namely high-purity argon to 0.004MPa for scrubbing;
step three, observing the condition in the furnace chamber through an observation port on the side wall of the non-consumable vacuum arc furnace, simultaneously opening a circulating water cooling system, and observing whether the condenser pipe is completely immersed in circulating cooling water so as to dissipate heat;
step four, switching on a power supply to start an arc for the arc gun, slowly raising the arc gun and increasing current after arc light appears, keeping the current not more than 400A in the smelting process, keeping the distance between the arc gun and raw materials at 1-2 mm, switching on an electromagnetic stirring switch after the raw materials are completely melted, stirring by an external magnetic field to ensure that the components are uniform, wherein each button ingot is smelted for 3min, including magnetic stirring for 10s, reducing the current and raising the arc gun after smelting is finished, and waiting for the button ingot to be naturally cooled and solidified in a water-cooled copper crucible after the power supply is closed;
turning over the cooled button ingot by using a mechanical arm, correcting the position of an arc gun, electrifying and reheating, and repeatedly smelting for 4 times to ensure that the alloy components are uniform;
and step six, smelting for the last time adopts a mode of gradually reducing current, so that arc light moves at a constant speed along the edge of the button ingot until the current is reduced to 0A, and the preparation of the multi-principal-element intermetallic compound is completed.
2. The high temperature resistant multi-principal element intermetallic compound according to claim 1, wherein the multi-principal element intermetallic compound is composed of, in atomic percent, cr:8 to 16 percent, 8 to 10 percent of Ti, 8 to 10 percent of Al, 3 to 5 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein the atomic percentage of Ni and Co elements is 2.04:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta.
3. The high temperature resistant multi-principal element intermetallic compound according to claim 2, wherein the multi-principal element intermetallic compound is composed of, in atomic percent, cr:8 to 16 percent, 10 to 12 percent of Ti, 10 to 12 percent of Al, 5 to 6 percent of Ta, 0.001 to 1 percent of B and the balance of Ni and Co; wherein the atomic percentage of Ni and Co elements is 2.04:1-3:1, and the total atomic content of Ni and Co is 2-5 times of the total atomic content of Al, ti and Ta.
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| CN111500917A (en) * | 2020-05-11 | 2020-08-07 | 北京科技大学 | High-strength and high-toughness medium-entropy high-temperature alloy and preparation method thereof |
| CN114703472A (en) * | 2022-03-15 | 2022-07-05 | 湘潭大学 | Method for repairing nickel-based superalloy based on isothermal solidification principle |
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| JP2015074795A (en) * | 2013-10-07 | 2015-04-20 | 三菱重工業株式会社 | Method of repairing member and method of manufacturing powder for repair |
| CN107475596A (en) * | 2017-08-10 | 2017-12-15 | 哈尔滨工业大学 | A kind of high entropy intermetallic compound |
| CN107824796A (en) * | 2017-11-15 | 2018-03-23 | 安徽工业大学 | The preparation method of multi-principal elements alloy powder body material containing ordered nano deposit in a kind of structure |
| CN108842076A (en) * | 2018-08-17 | 2018-11-20 | 北京科技大学 | A kind of high entropy eutectic alloy of Ni-Co-Cr-Ti-Ta system and preparation method thereof |
| CN111500917A (en) * | 2020-05-11 | 2020-08-07 | 北京科技大学 | High-strength and high-toughness medium-entropy high-temperature alloy and preparation method thereof |
| CN114703472A (en) * | 2022-03-15 | 2022-07-05 | 湘潭大学 | Method for repairing nickel-based superalloy based on isothermal solidification principle |
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