CN118516580B - High-temperature antioxidant high-entropy alloy material and preparation method thereof - Google Patents
High-temperature antioxidant high-entropy alloy material and preparation method thereof Download PDFInfo
- Publication number
- CN118516580B CN118516580B CN202411002412.9A CN202411002412A CN118516580B CN 118516580 B CN118516580 B CN 118516580B CN 202411002412 A CN202411002412 A CN 202411002412A CN 118516580 B CN118516580 B CN 118516580B
- Authority
- CN
- China
- Prior art keywords
- entropy alloy
- smelting
- raw material
- alloy material
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 138
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 239000003963 antioxidant agent Substances 0.000 title claims abstract description 12
- 230000003078 antioxidant effect Effects 0.000 title claims abstract description 12
- 230000003647 oxidation Effects 0.000 claims abstract description 122
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 122
- 238000003723 Smelting Methods 0.000 claims abstract description 82
- 239000002994 raw material Substances 0.000 claims abstract description 77
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 62
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 28
- 238000000034 method Methods 0.000 claims abstract description 20
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims description 53
- 238000001816 cooling Methods 0.000 claims description 33
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 25
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 20
- 238000002844 melting Methods 0.000 claims description 17
- 230000008018 melting Effects 0.000 claims description 17
- 229910021364 Al-Si alloy Inorganic materials 0.000 claims description 11
- 229910052786 argon Inorganic materials 0.000 claims description 10
- 238000004321 preservation Methods 0.000 claims description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 7
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 7
- 244000137852 Petrea volubilis Species 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 239000010949 copper Substances 0.000 claims description 7
- 238000003756 stirring Methods 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract description 6
- 239000010703 silicon Substances 0.000 abstract description 6
- 239000007788 liquid Substances 0.000 abstract description 4
- 238000004806 packaging method and process Methods 0.000 abstract description 3
- 238000002203 pretreatment Methods 0.000 abstract description 3
- 238000004519 manufacturing process Methods 0.000 abstract description 2
- 230000008901 benefit Effects 0.000 abstract 2
- 230000000052 comparative effect Effects 0.000 description 26
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 238000001035 drying Methods 0.000 description 9
- 238000005498 polishing Methods 0.000 description 8
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 8
- 229910052721 tungsten Inorganic materials 0.000 description 8
- 239000010937 tungsten Substances 0.000 description 8
- 239000011856 silicon-based particle Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000007789 gas Substances 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 239000011651 chromium Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 4
- 238000004140 cleaning Methods 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000013461 design Methods 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000001291 vacuum drying Methods 0.000 description 4
- 238000005406 washing Methods 0.000 description 4
- 238000005303 weighing Methods 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000001590 oxidative effect Effects 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 230000004584 weight gain Effects 0.000 description 3
- 235000019786 weight gain Nutrition 0.000 description 3
- 229910003264 NiFe2O4 Inorganic materials 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000010952 cobalt-chrome Substances 0.000 description 2
- 229910052593 corundum Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- NQNBVCBUOCNRFZ-UHFFFAOYSA-N nickel ferrite Chemical compound [Ni]=O.O=[Fe]O[Fe]=O NQNBVCBUOCNRFZ-UHFFFAOYSA-N 0.000 description 2
- 238000005191 phase separation Methods 0.000 description 2
- 230000002040 relaxant effect Effects 0.000 description 2
- 238000004506 ultrasonic cleaning Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- NIPNSKYNPDTRPC-UHFFFAOYSA-N N-[2-oxo-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 NIPNSKYNPDTRPC-UHFFFAOYSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000010314 arc-melting process Methods 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 239000010431 corundum Substances 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 230000001052 transient effect Effects 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention discloses a high-temperature antioxidant high-entropy alloy material and a preparation method thereof, and belongs to the technical field of high-entropy alloy preparation. The invention reduces the oxidation rate of the alloy to 6.2 multiplied by 10 ‑9mg2/cm4/s by adding trace silicon elements into AlCrFeCoNi matrixes, so that the material reaches the full oxidation resistance level and shows excellent oxidation resistance. The preparation method of the high-entropy alloy material provides a novel smelting pretreatment method, namely an aluminum liquid packaging method, so that Si element, al and Fe element are better combined to form a new phase, and the high-temperature oxidation resistance of the high-entropy alloy is improved. And the raw materials are not easy to crack in the smelting process, and smelting is more uniform. The method has the advantages of simple operation, easy control and high cost benefit, and is suitable for industrial mass production.
Description
Technical Field
The invention belongs to the technical field of high-entropy alloy preparation, and particularly relates to a high-temperature oxidation-resistant high-entropy alloy material and a preparation method thereof.
Background
AlCrFeCoNi-series high-entropy alloy is an alloy system with wide application potential. At room temperature, the alloy exhibits high strength and good ductility. In addition, alCrFeCoNi-series high-entropy alloy exhibits excellent high-temperature oxidation resistance and hot corrosion resistance in the medium-high temperature range of 700 ℃ to 850 ℃. Such high entropy alloys contain higher levels of oxidation and corrosion resistant elements such as aluminum (Al) and chromium (Cr) than conventional nickel-based superalloys. Therefore, alCrFeCoNi-series high-entropy alloy is considered as a powerful competitor of a new generation of high-temperature metal structural materials, and is suitable for high-temperature environments such as aerospace, nuclear industry and the like.
At high temperatures, high entropy alloys react primarily through selective oxidation of elements. For example, aluminum in AlCrFeCoNi-series high-entropy alloy is preferentially oxidized under a high-temperature environment to generate an Al 2O3 film with high oxidation resistance, so that a metal matrix is protected. Studies have shown that the oxidation behaviour of an alloy depends largely on its chemical composition, in particular the aluminium content. For example, butler et Al's study indicated that Al x CoCrFeNi high-entropy alloys first undergo a transient oxidation stage during oxidation, and then exhibit varying degrees of parabolic growth regularity. As the aluminum content increases, the oxidation resistance of the alloy increases significantly. However, even if the aluminum content reaches 20at.%, the oxidation resistance of the AlCoCrFeNi high entropy alloy still does not reach the ideal state. Further research shows that the silicon (Si) element can change the growth mechanism of the oxide film, and the oxidation resistance and the hot corrosion resistance of the oxide film are obviously improved. Therefore, si plays an important role in improving the high-temperature oxidation performance of AlCoCrFeNi high-entropy alloy. The addition of Si not only can improve the compactness and stability of the oxide film, but also can obviously enhance the overall performance of the alloy in a high-temperature environment. In conclusion, the AlCrFeCoNi-based high-entropy alloy containing trace silicon can remarkably improve the oxidation resistance of the alloy under the high-temperature condition by optimizing chemical components, particularly the content of Al and Si, and provides more reliable material selection for high-temperature application.
Disclosure of Invention
Aiming at the prior art, the invention provides a high-temperature oxidation-resistant high-entropy alloy material and a preparation method thereof, which solve the problem of insufficient oxidation resistance and hot corrosion resistance.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows: the preparation method of the high-temperature oxidation-resistant high-entropy alloy material comprises the following steps:
s1: pretreating the raw materials to remove an oxide layer;
s2: smelting an Al raw material into an aluminum melt at 670-700 ℃, preserving heat for 15-20 min, adding an Si raw material in the heat preservation process, uniformly stirring, and cooling the aluminum melt mixed with the Si raw material to room temperature after heat preservation is finished to obtain an Al-Si alloy block;
S3: placing Al-Si alloy blocks, cr raw materials, fe raw materials, co raw materials and Ni raw materials into a water-cooled copper mold of a vacuum arc melting furnace according to the sequence of the melting point of the alloy raw materials from low to high, placing an indicating element in the center of the mold, vacuumizing, and then filling high-purity argon into the mold until the state is in a micro-positive pressure state;
s4: pre-smelting by using a vacuum arc smelting furnace, and formally smelting the raw materials when the indicator element has no obvious color change; smelting raw materials to a molten state, repeatedly smelting for 5 times until the raw materials are uniform, and stopping the furnace and cooling for 10-15 min to obtain a high-temperature antioxidant high-entropy alloy material;
The addition amounts of the Al raw material, the Cr raw material, the Fe raw material, the Co raw material, the Ni raw material and the Si raw material are based on the atomic ratio of each element of the obtained high-temperature oxidation-resistant high-entropy alloy material, namely 19.5% -20% of Al, 19.5% -20% of Cr, 19.5% -20% of Fe, 19.5% -20% of Co, 19.5% -20% of Ni and 0.8% -2.4% of Si.
The beneficial effects of the invention are as follows: the invention uses a novel smelting pretreatment method, namely an aluminum liquid packaging method, namely, before the re-smelting operation, si particles are packaged by molten Al liquid, and conventional smelting operation is performed after Al-Si alloy is formed, so that raw material explosion phenomenon in the smelting process is avoided, raw material loss in the smelting operation process is reduced, the components of the smelted high-entropy alloy material are more uniform, the components are more in accordance with the component design proportion, and Si element, al and Fe element are better combined to form a new phase, thereby improving the high-temperature oxidation resistance of the high-entropy alloy.
On the basis of the technical scheme, the invention can be improved as follows.
Further, the Al raw material, the Cr raw material, the Fe raw material, the Co raw material, the Ni raw material and the Si raw material are particles with the purity of more than 99.9% and the particle size of 1-3 mm.
The beneficial effects of adopting further technical scheme are: the smelting effect is closely related to the size of raw material particles, and the uniformity of a smelting sample can be influenced by excessively large or excessively small particles. Too large particles may result in insufficient material contact, reducing the uniformity of the alloy; while too small particles may increase the loss of raw materials, resulting in deviations of the smelted sample composition from the design.
Further, the pretreatment for removing the oxide layer is to polish the surface of the raw material by sand paper or a grinder, then sequentially put the raw material into absolute ethyl alcohol, and then carry out ultrasonic cleaning on the raw material by 300 s, and finally dry the raw material at the temperature of 80 ℃.
Further, the high-temperature oxidation-resistant high-entropy alloy material comprises the following elements in mole ratio: al: cr: fe: co: ni=1:1:1:1.
Further, vacuum was applied to 5X 10 -3 Pa in S3.
Further, the indicator element is Ti, the vacuum arc premelting process is to control the arc to be 1-3 mm away from the surface of Ti, the control current is 60A, and 60 s is maintained.
Further, the vacuum arc melting process gradually increases the current from 60A to 120A, the speed is 5-8A/s, the melting time is 5min each time, and the raw materials are turned over after the alloy is cooled.
Further, S4 cooling was performed by cooling with circulating water having a flow rate of 20 cm/S.
The beneficial effects of adopting further technical scheme are: the smelting quality and the production efficiency of the alloy can be effectively improved, and meanwhile, the physical and chemical properties of the final product are ensured to meet the application requirements of high standards.
The invention also discloses a high-temperature oxidation-resistant high-entropy alloy material prepared by the preparation method of the high-temperature oxidation-resistant high-entropy alloy material.
The beneficial effects of the invention are as follows: the alloy material of the invention has low cost and high performance, can be used at high temperature, remarkably improves the oxidation resistance, and has lattice distortion caused by the addition of Si, which is helpful for relaxing the lattice distortion energy, thereby promoting the formation of BCC phase. When the XRD patterns of the high-entropy alloy are analyzed, only a BCC diffraction peak is shown on XRD without adding Si alloy, which shows that a single-phase BCC crystal structure is mainly formed in the alloy, and in the alloy containing Si, a superlattice (100) B2 diffraction peak related to ordered BCC appears, which shows that phase separation exists in the alloy.
Drawings
FIG. 1 is an XRD pattern of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1 to 3 and comparative example 1;
FIG. 2 is a scanning electron microscope image of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1 to 3 and comparative example 1;
FIG. 3 is a graph showing the oxidation kinetics of the high temperature oxidation resistant high entropy alloy materials prepared in examples 1-3 and comparative example 1;
FIG. 4 is XRD patterns of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1, oxidized 96 h at 900 ℃;
FIG. 5 is a graph showing the oxidized surfaces of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1, wherein the surfaces are oxidized at 900 ℃ to 96 h;
FIG. 6 is an EDS diagram of an oxidation layer of a high-temperature oxidation-resistant high-entropy alloy material prepared in comparative example 1, which is oxidized at 900 ℃ to 96 h;
FIG. 7 is an EDS diagram of the cross section of an oxide layer of the high-temperature oxidation-resistant high-entropy alloy material prepared in example 1, which is oxidized at 900 ℃ and 96 h;
FIG. 8 is an EDS diagram of the cross section of an oxide layer of the high-temperature oxidation-resistant high-entropy alloy material prepared in example 2, which is oxidized at 900 ℃ and 96 h;
FIG. 9 is an EDS diagram of an oxidation layer of a high temperature oxidation resistant high entropy alloy material prepared in example 3 at 900 ℃ for oxidation 96 h.
Detailed Description
The following describes the present invention in detail with reference to examples.
Example 1
A high-temperature oxidation-resistant high-entropy alloy material comprises the following elements of Al, cr, fe, co, ni, si (according to an atomic ratio) =19.84% (19.84%) (0.8%) and the elements of Al, cr, fe, co, ni, si (according to a mass ratio) =10.6% (20.5% (22.1%) (23.3%) (23.1%) (0.4%) in terms of mass ratio).
The high-temperature oxidation-resistant high-entropy alloy material in the embodiment is prepared through the following steps:
s1: polishing the surface of the raw material by sand paper, and removing an oxide film on the surface of the raw material; weighing polished raw material particles Al 1.0642g, cr 2.0495g, fe 2.2072g, co 2.3253g, ni 2.3096g and Si 0.0441g according to the total smelting amount of 10 g g, sequentially placing the weighed different particles into absolute ethyl alcohol, cleaning with ultrasonic waves for 300 s, and then placing the particles into a vacuum drying oven to set the drying temperature to 80 ℃ for drying;
s2: smelting Al particles into an aluminum melt at 680 ℃, preserving heat 15 min, adding Si particles in the heat preservation process, uniformly stirring, and cooling the aluminum melt mixed with the Si particles to room temperature after heat preservation is finished to obtain an Al-Si alloy block;
S3: the Al-Si alloy blocks, cr particles, fe particles, co particles and Ni particles are put into a water-cooled copper mold of a vacuum arc melting furnace according to the sequence from low melting point to high melting point of the alloy raw materials, and Ti particles are put in the center of the mold. After a circulating water cooling system of the vacuum arc furnace is opened, firstly starting a mechanical pump to perform low vacuum, then starting a molecular pump to perform high vacuum, then introducing high-purity argon to enable the air pressure to be more than 0, repeating the air washing operation for one time, removing other impurity gases in the vacuum arc furnace, ensuring the smelting effect of a sample, and then introducing high-purity argon to enable the air pressure to be 0.03 pa;
S4: the arc was initiated by the tungsten tip and adjusted to be 2mm above the Ti particle surface. Controlling the current to be 60A when smelting for the first time, maintaining 60 s, and continuing smelting when Ti particles have no obvious color change state; the tungsten electrode head is moved to the position 2mm above the metal raw material to be smelted, the current is increased from 0A to 100A by the current of 6A/s for smelting, 3 min is smelted each time, the alloy is turned over after being cooled (circulating water flow rate is 20 cm/s for water cooling), the smelting operation is repeated, the front smelting operation and the back smelting operation are counted as one smelting operation, the smelting operation is repeated for 5 times, the furnace cooling (circulating water flow rate is 20 cm/s for water cooling) is stopped for 10 min, a bleed valve is opened, and when the air pressure in the arc smelting furnace is consistent with the normal pressure, the smelting furnace can be opened, so that the high-temperature antioxidant high-entropy alloy material AlCrFeCoNiSi 0.04 is obtained.
Example 2
A high-temperature oxidation-resistant high-entropy alloy material comprises the following elements of Al, cr, fe, co, ni, si (according to an atomic ratio) =19.68% (19.68%) (1.6%) (mass ratio), and Al, cr, fe, co, ni, si (according to a mass ratio) =10.6% (20.4%) (22.0%) (23.2%) (23.0%) (0.8%) (on a mass ratio basis).
The high-temperature oxidation-resistant high-entropy alloy material in the embodiment is prepared through the following steps:
S1: polishing the surface of the raw material by sand paper, and removing an oxide film on the surface of the raw material; weighing polished raw material particles Al 1.0595g, cr 2.0405g, fe 2.1975g, co 2.3152g, ni 2.2995g and Si 0.0878g according to the total smelting amount of 10 g g, sequentially placing the weighed different particles into absolute ethyl alcohol, cleaning with ultrasonic waves for 300 s, and then placing the particles into a vacuum drying oven to set the drying temperature to 80 ℃ for drying;
S2: smelting Al particles into an aluminum melt at 670 ℃, preserving heat for 20 min, adding Si particles in the heat preservation process, uniformly stirring, and cooling the aluminum melt mixed with the Si particles to room temperature after the heat preservation is finished to obtain an Al-Si alloy block;
S3: the Al-Si alloy blocks, cr particles, fe particles, co particles and Ni particles are put into a water-cooled copper mold of a vacuum arc melting furnace according to the sequence from low melting point to high melting point of the alloy raw materials, and Ti particles are put in the center of the mold. After a circulating water cooling system of the vacuum arc furnace is opened, firstly starting a mechanical pump to perform low vacuum, then starting a molecular pump to perform high vacuum, then introducing high-purity argon to enable the air pressure to be more than 0, repeating the air washing operation for one time, removing other impurity gases in the vacuum arc furnace, ensuring the smelting effect of a sample, and then introducing high-purity argon to enable the air pressure to be 0.01 pa;
s4: the arc was initiated by the tungsten tip and adjusted to be located 1mm above the Ti particle surface. Controlling the current to be 60A when smelting for the first time, maintaining 60 s, and continuing smelting when Ti particles have no obvious color change state; the tungsten electrode head is moved to the position 2mm above the metal raw material to be smelted, the current is increased from 0A to 90A for smelting at a current speed of 5A/s, each time of smelting is 4 min, after the alloy is cooled (circulating water flow rate is 20 cm/s for water cooling), the alloy is turned over, the smelting operation is repeated, the front smelting and the back smelting are counted as one smelting operation, the smelting operation is repeated for 5 times, the furnace cooling (circulating water flow rate is 20 cm/s for water cooling) is stopped for 15min, a gas release valve is opened, and when the gas pressure in the arc smelting furnace is consistent with the normal pressure, the smelting furnace is opened, so that the high-temperature antioxidant high-entropy alloy material AlCrFeCoNiSi 0.08 is obtained.
Example 3
A high-temperature oxidation-resistant high-entropy alloy material comprises the following elements of Al, cr, fe, co, ni, si (according to an atomic ratio) =19.52% (19.52%) (2.4%) and is converted into a mass ratio, wherein the mass ratio of Al, cr, fe, co, ni, si (according to the mass ratio) =10.5% (20.3% (21.9%) (23.1%) (23.0%) (1.2%).
The high-temperature oxidation-resistant high-entropy alloy material in the embodiment is prepared through the following steps:
S1: polishing the surface of the raw material by sand paper, and removing an oxide film on the surface of the raw material; weighing polished raw material particles Al 1.0549g, cr 2.0316g, fe 2.1875g, co 2.3050g, ni 2.2894g and Si 0.1313g according to the total smelting amount of 10g, sequentially placing the weighed different particles into absolute ethyl alcohol, cleaning with ultrasonic waves for 300 s, and then placing the particles into a vacuum drying oven to set the drying temperature to 80 ℃ for drying;
S2: smelting Al particles into an aluminum melt at 700 ℃, preserving heat 18 min, adding Si particles in the heat preservation process, uniformly stirring, and cooling the aluminum melt mixed with the Si particles to room temperature after the heat preservation is finished to obtain an Al-Si alloy block;
S3: the Al-Si alloy blocks, cr particles, fe particles, co particles and Ni particles are put into a water-cooled copper mold of a vacuum arc melting furnace according to the sequence from low melting point to high melting point of the alloy raw materials, and Ti particles are put in the center of the mold. After a circulating water cooling system of the vacuum arc furnace is opened, firstly starting a mechanical pump to perform low vacuum, then starting a molecular pump to perform high vacuum, then introducing high-purity argon to enable the air pressure to be more than 0, repeating the air washing operation for one time, removing other impurity gases in the vacuum arc furnace, ensuring the smelting effect of a sample, and then introducing high-purity argon to enable the air pressure to be 0.05 pa;
S4: the arc was initiated by the tungsten tip and adjusted to be 3mm above the Ti particle surface. Controlling the current to be 60A when smelting for the first time, maintaining 60 s, and continuing smelting when Ti particles have no obvious color change state; the tungsten electrode head is moved to a position 3mm above a metal raw material to be smelted, the current is increased from 0A to 120A by current acceleration of 5A/s, smelting is carried out, each time of smelting is carried out for 5min, after alloy cooling (circulating water flow rate is 20 cm/s water cooling), the smelting operation is repeated, the front smelting and the back smelting are counted as one smelting operation, smelting is repeated for 5 times, furnace cooling (circulating water flow rate is 20 cm/s water cooling) is carried out for 12 min, a bleed valve is opened, and when the air pressure in an electric arc smelting furnace is consistent with normal pressure, the smelting furnace can be opened, and the high-temperature antioxidant high-entropy alloy material AlCrFeCoNiSi 0.12 is obtained.
Comparative example 1
A high-temperature oxidation-resistant high-entropy alloy material comprises the following elements of Al, cr, fe, co, ni (according to an atomic ratio) =20% (20%), and the elements are converted into mass ratio, wherein the mass ratio of Al, cr, fe, co, ni (according to the mass ratio) =10.7% (20.6%) (22.2%) (23.3%) (23.2%) (and Si is not added).
The high-temperature oxidation-resistant high-entropy alloy material in the comparative example is prepared through the following steps:
S1: polishing the surface of the raw material by sand paper, and removing an oxide film on the surface of the raw material; weighing polished raw material particles Al 1.0689g, cr 2.0589g, fe 2.2169g, co 2.3357g and Ni 2.3198g according to the total smelting amount of 10g, sequentially placing the weighed different particles into absolute ethyl alcohol, cleaning with ultrasonic waves for 300 s, and then placing the particles into a vacuum drying box to set the drying temperature to 80 ℃ for drying;
S2: al particles, cr particles, fe particles, co particles and Ni particles are put into a water-cooled copper mould of a vacuum arc melting furnace according to the sequence from low melting point to high melting point of alloy raw materials, and Ti particles are put in the center of the mould. After a circulating water cooling system of the vacuum arc furnace is opened, firstly starting a mechanical pump to perform low vacuum, then starting a molecular pump to perform high vacuum, then introducing high-purity argon to enable the air pressure to be more than 0, repeating the air washing operation for one time, removing other impurity gases in the vacuum arc furnace, ensuring the smelting effect of a sample, and then introducing high-purity argon to enable the air pressure to be in a micro-positive pressure state with the air pressure to be more than 0;
S3: the arc was initiated by the tungsten tip and adjusted to be 2mm above the Ti particle surface. Controlling the current to be 60A when smelting for the first time, maintaining 60 s, and continuing smelting when Ti particles have no obvious color change state; the tungsten electrode head is moved to the position 2mm above the metal raw material to be smelted, the current is increased from 0A to 100A by the current of 6A/s for smelting, 3 min is smelted each time, the alloy is turned over after being cooled (circulating water flow rate is 20 cm/s for water cooling), the smelting operation is repeated, the front smelting and the back smelting are counted as one smelting operation, the smelting operation is repeated for 5 times, the furnace is stopped for cooling (circulating water flow rate is 20 cm/s for water cooling) for 10 min, a release valve is opened, and when the air pressure in the arc smelting furnace is consistent with the normal pressure, the smelting furnace can be opened, so that the high-temperature antioxidant high-entropy alloy material AlCrFeCoNi is obtained.
Comparative example 2
The preparation conditions are different from those of the embodiment 1 in that an aluminum liquid packaging pretreatment method is not used, the alloy material part is cracked in a smelting process, the smelted high-entropy alloy sample does not accord with design components, and the sample is unevenly smelted.
Comparative example 3
The difference from the preparation conditions of example 1 is that the circulating water flow rate of the circulating water cooling system of the vacuum arc furnace is adjusted to 40 cm/s, and the result shows that the obtained alloy sample has cracks in the process of rapid cooling, which indicates that the cooling speed is too high, and the internal stress of the material is possibly increased, so that the cracks are caused. In addition, the non-uniformity of the alloy composition also suggests that rapid cooling may affect the flow and uniform solidification of the alloy melt in the mold, further demonstrating the importance of proper cooling rates for maintaining alloy structure and performance.
Comparative example 4
The difference from the preparation conditions of example 1 is that the current increase rate during smelting is set at 15A/s to 150A, which results in the alloy raw material being partially splashed out of the water-cooled copper mould during smelting, resulting in material loss. This loss not only reduces the yield of the final product, but also results in a substantial atomic ratio that differs from the designed composition, affecting the desired properties and quality of the alloy.
Experimental example 1
High temperature antioxidant test: cutting the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative examples into cuboid block-shaped samples of 3 mm multiplied by 6 mm multiplied by 10 mm by a wire cutting machine, polishing six surfaces of the cuboid block-shaped samples by using 400-mesh, 800-mesh, 1200-mesh and 2000-mesh SiC sand paper respectively, polishing the six surfaces by using diamond polishing paste with the particle size of 1.5 mm, polishing the six surfaces of the samples until no obvious scratches are observed under a metallographic microscope at 50 times, then placing the polished samples into absolute ethyl alcohol for ultrasonic cleaning, and drying the samples by a blower, thereby obtaining the high-temperature oxidation-resistant test.
The high temperature oxidation test is carried out by using a high temperature box type furnace, a clean sample is placed into a clean corundum crucible, the high temperature box type furnace is set to be heated to 900 ℃, the crucible filled with the alloy sample is placed into the box type furnace, the sample is taken out respectively at the 0 h, 2h, 4 h, 6 h, 12h, 24 h, 36 h, 48 h, 60 h, 72 h, 84 h and 96 h, the mass of the sample is weighed after the sample is cooled to room temperature, and the mass change of the sample is recorded.
XRD patterns of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 are shown in figure 1, the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 both have disordered BCC (A2) phase and ordered BCC (B2) phase structures, but the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 have lattice distortion due to the addition of Si, which is helpful for relaxing lattice distortion energy, so that the formation of BCC phase is promoted, and the high-temperature oxidation-resistant high-entropy alloy material prepared in comparative example 1 only shows BCC diffraction peaks, which indicate that single-phase BCC crystal structures are mainly formed in the alloy. In the high temperature oxidation resistant high entropy alloy materials prepared in examples 1-3, a superlattice (100) B2 diffraction peak associated with ordered BCC appeared, which indicates that there was phase separation in the alloy.
Scanning electron microscopes are used for scanning the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1, and as shown in fig. 2, the scanning electron microscope observes that 4 samples have no obvious dendrite segregation phenomenon, which indicates that the smelting is very uniform.
The sample unit area mass gain data of 96 h of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 are counted, and as shown in the result of fig. 3, the oxidation gain of AlCrFeCoNiSi 0.04 and h of the high-temperature oxidation-resistant high-entropy alloy material prepared in example 1 is only 0.008873mg cm -2, by data fitting, the oxidation rate of the high-entropy alloy is only 7.76x10 -4mg·cm-2·h-1 (namely 8.51x10 -9(mg2/cm4/s), and the high-entropy alloy belongs to the complete oxidation resistance grade and has excellent oxidation resistance according to the oxidation resistance grade rating standard of the steel and the alloy provided by GB/T13303-1991 shown in table 1. Example 2 the high temperature oxidation resistant high entropy alloy material AlCrFeCoNiSi 0.08, 96, h produced had an oxidation weight gain of 0.01420mg cm -2, an oxidation rate of 1.33 x 10 -3mg·cm-2·h-1 (i.e., 1.51 x 10 -8(mg2/cm4/s)), The high-temperature oxidation resistance is better than that of the example 1, and the AlCrFeCoNiSi 0.08 high-entropy alloy material also belongs to the complete oxidation resistance grade and has excellent oxidation resistance according to the oxidation resistance grade rating standard of the steel and the alloy provided by GB/T13303-1991 shown in the table 1. Example 3 the high temperature oxidation resistant high entropy alloy material AlCrFeCoNiSi 0.12 96 h has an oxidation weight gain of 0.007199 mg.cm -2, an oxidation rate of 6.05X10 -4mg·cm-2·h-1（6.20×10-9(mg2/cm4/s), The high-temperature oxidation resistance is better than that of the example 1, and the AlCrFeCoNiSi 0.12 high-entropy alloy material also belongs to the complete oxidation resistance grade and has excellent oxidation resistance according to the oxidation resistance grade rating standard of the steel and the alloy provided by GB/T13303-1991 shown in the table 1. Comparative example 1 the high temperature oxidation resistant high entropy alloy material AlCrFeCoNi, which had a h oxidation weight gain of 0.01136mg cm -2, an oxidation rate of 1.96 x 10 -3mg·cm-2·h-1（6.86×10-8(mg2/cm4/s), had a lower oxidation resistance at high temperature than other Si-added examples, according to the oxidation resistance rating criteria for steels and alloys provided by GB/T13303-1991 shown in table 1, AlCrFeCoNi the high-entropy alloy material belongs to oxidation resistance grade and has excellent oxidation resistance, but the oxidation resistance of the AlCrFeCoNi high-entropy alloy material is improved by one order of magnitude by adding trace Si, which shows that the addition of Si effectively improves the high-temperature oxidation resistance of the alloy, and achieves the effects of reducing oxidation rate and prolonging service life.
Table 1 antioxidant rating criteria for steels and alloys (from GB/T13303-1991)
The oxidation kinetics curve of the high-temperature oxidation-resistant high-entropy alloy material prepared in examples 1-3 and comparative example 1 in oxidation for 96 hours at 900 ℃ in high-temperature environment meets the power law equationFitting the oxidation mass gain data, wherein the obtained oxidation kinetics curve for 96 hours approximately meets the parabolic law oxidation, and the fitted n value and K value are shown in table 2.
Table 2 n and K values of the oxidized integral high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1 to 3 and comparative example 1 at 900 DEG C
The high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 are oxidized at 900 ℃ to 96 h and then detected by an X-ray diffractometer, and the result is shown in fig. 4, the oxidized layer of the high-temperature oxidation-resistant high-entropy alloy material prepared in example 1-3 after being oxidized at 900 ℃ consists of Al2O3,SiO2,Fe2O3,CoCr2O4,NiFe2O4 oxides, a compact oxide film is formed on the surface of a substrate by the oxides, so that the high-temperature oxidation-resistant high-entropy alloy material has excellent oxidation resistance, and the oxidized layer of the high-temperature oxidation-resistant high-entropy alloy material prepared in comparative example 1 after being oxidized at 900 ℃ consists of four oxides, namely Al 2O3,Fe2O3,CoCr2O4,NiFe2O4.
The surfaces of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 after being oxidized at 900 ℃ and 96 h are observed by an electron microscope, and the results are shown in fig. 5, the oxidized surfaces of the high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 are smooth, and the oxidized surfaces of the high-temperature oxidation-resistant high-entropy alloy materials prepared in comparative example 1 are loose.
The high-temperature oxidation-resistant high-entropy alloy materials prepared in examples 1-3 and comparative example 1 are subjected to element analysis by using an energy spectrum diffractometer after being oxidized at 900 ℃ for 96 h, and the result is shown in fig. 6-9, and according to the analysis of an EDS (electron beam ionization) chart of an oxide layer section, the oxide layer thickness formed by oxidizing the high-temperature oxidation-resistant high-entropy alloy material AlCrFeCoNiSi 0.04 prepared in example 1 is compact, so that the direct contact between oxygen and a matrix is effectively isolated, and the high oxidation resistance is achieved; compared with the embodiment 1, the oxide layer formed by oxidizing the high-temperature oxidation-resistant high-entropy alloy material AlCrFeCoNiSi 0.08 prepared in the embodiment 2 is thicker and is continuous and compact, so that the direct contact between oxygen and a matrix is effectively isolated, and the oxide layer has excellent oxidation resistance; the oxidation layer formed by oxidizing the high-temperature oxidation-resistant high-entropy alloy material AlCrFeCoNiSi 0.12 prepared in the embodiment 2 is thicker and is continuous and compact as compared with the embodiment 2, so that the direct contact between oxygen and a matrix is effectively isolated, and compared with the embodiment 1 and the embodiment 2, the high-temperature oxidation-resistant high-entropy alloy material AlCrFeCoNiSi 0.12 has the most excellent oxidation resistance; whereas the oxide layer formed by the high temperature oxidation resistant high entropy alloy material AlCrFeCoNi prepared in comparative example 1 was dispersed and discontinuous as seen in the oxide layer cross-sectional EDS diagram of 96 and h.
In conclusion, by adding trace silicon into AlCrFeCoNi-base alloy and optimizing alloy components, the oxidation resistance of the material is obviously improved by adding the trace silicon, and the complete oxidation resistance level is achieved. This performance enhancement allows the alloy to exhibit excellent stability and durability under extreme high temperature conditions, further demonstrating the critical role of silicon in enhancing high temperature oxidation resistance. Through the innovative alloy design and preparation method, the invention not only realizes excellent adaptability to high-temperature environment, but also provides an efficient and economical material solution for high-temperature application fields such as aviation, energy sources and the like.
While specific embodiments of the invention have been described in detail in connection with the examples, it should not be construed as limiting the scope of protection of the patent. Various modifications and variations which may be made by those skilled in the art without the creative effort are within the scope of the patent described in the claims.
Claims (5)
1. The preparation method of the high-temperature oxidation-resistant high-entropy alloy material is characterized by comprising the following steps of:
s1: pretreating the raw materials to remove an oxide layer;
s2: smelting an Al raw material into an aluminum melt at 670-700 ℃, preserving heat for 15-20 min, adding an Si raw material in the heat preservation process, uniformly stirring, and cooling the aluminum melt mixed with the Si raw material to room temperature after heat preservation is finished to obtain an Al-Si alloy block;
S3: placing Al-Si alloy blocks, cr raw materials, fe raw materials, co raw materials and Ni raw materials into a water-cooled copper mold of a vacuum arc melting furnace according to the sequence of the melting point of the alloy raw materials from low to high, placing an indicating element in the center of the mold, vacuumizing, and then filling high-purity argon to a state of 0.01-0.05 Pa;
s4: pre-smelting by using a vacuum arc smelting furnace, and formally smelting the raw materials when the indicator element has no obvious color change; smelting raw materials to a molten state, repeatedly smelting for 5 times until the raw materials are uniform, and stopping the furnace and cooling for 10-15 min to obtain a high-temperature antioxidant high-entropy alloy material;
The indication element is Ti, the vacuum arc premelting process is to control the arc to be 1-3 mm away from the surface of Ti, control the current to be 60A and maintain 60 s;
The vacuum arc formal smelting process is that the current gradually increases from 0A to 90-120A, the speed is 5-8A/s, the smelting time is 3-5 min each time, and the raw materials are turned over after the alloy is cooled; the cooling is to use circulating water with the flow rate of 20cm/s for water cooling;
the Al raw material, the Cr raw material, the Fe raw material, the Co raw material, the Ni raw material and the Si raw material are particles with the purity of more than 99.9 percent and the particle size of 1-3 mm, and the raw material addition amount is based on the atomic ratio of each element of the obtained high-temperature oxidation-resistant high-entropy alloy material, wherein the atomic ratio is 19.5-20 percent of Al, 19.5-20 percent of Cr, 19.5-20 percent of Fe, 19.5-20 percent of Co, 19.5-20 percent of Ni and 0.8-2.4 percent of Si.
2. The method for preparing the high-temperature oxidation-resistant high-entropy alloy material according to claim 1, which is characterized in that: the pretreatment for removing the oxide layer is to polish the surface of the raw material by sand paper or a grinder, then sequentially put the raw material into absolute ethyl alcohol, and then washed by ultrasonic waves for 300 s, and finally dried at 80 ℃.
3. The method for preparing the high-temperature oxidation-resistant high-entropy alloy material according to claim 1, which is characterized in that: the high-temperature antioxidant high-entropy alloy material comprises the following elements in mole ratio: al: cr: fe: co: ni=1:1:1:1.
4. The method for preparing the high-temperature oxidation-resistant high-entropy alloy material according to claim 1, which is characterized in that: and S3, vacuumizing to 5X 10 -3 Pa.
5. A high-temperature oxidation-resistant high-entropy alloy material is characterized in that: the method for preparing the high-temperature oxidation-resistant high-entropy alloy material according to any one of claims 1-4.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202411002412.9A CN118516580B (en) | 2024-07-25 | 2024-07-25 | High-temperature antioxidant high-entropy alloy material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202411002412.9A CN118516580B (en) | 2024-07-25 | 2024-07-25 | High-temperature antioxidant high-entropy alloy material and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN118516580A CN118516580A (en) | 2024-08-20 |
| CN118516580B true CN118516580B (en) | 2024-10-01 |
Family
ID=92274572
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202411002412.9A Active CN118516580B (en) | 2024-07-25 | 2024-07-25 | High-temperature antioxidant high-entropy alloy material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN118516580B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103898463A (en) * | 2014-03-07 | 2014-07-02 | 浙江大学 | Multi-element high-entropy alloy film and preparation method thereof |
| CN109750209A (en) * | 2019-03-27 | 2019-05-14 | 广东工业大学 | A kind of Ultra-fine Grained eutectic high-entropy alloy and preparation method thereof |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101927611B1 (en) * | 2016-05-02 | 2018-12-10 | 한국과학기술원 | High- strength and heat-resisting high entropy alloy matrix composites and method of manufacturing the same |
| KR102584270B1 (en) * | 2021-09-08 | 2023-10-04 | 세종대학교산학협력단 | High ductility Co-Cu-Fe-Ni-M high entropy alloy with improved strength |
| US20230323516A1 (en) * | 2022-04-11 | 2023-10-12 | General Electric Company | High entropy alloy-based compositions and bond coats formed therefrom |
-
2024
- 2024-07-25 CN CN202411002412.9A patent/CN118516580B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103898463A (en) * | 2014-03-07 | 2014-07-02 | 浙江大学 | Multi-element high-entropy alloy film and preparation method thereof |
| CN109750209A (en) * | 2019-03-27 | 2019-05-14 | 广东工业大学 | A kind of Ultra-fine Grained eutectic high-entropy alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN118516580A (en) | 2024-08-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN113789464B (en) | Ceramic phase reinforced refractory high-entropy alloy and preparation method thereof | |
| CN113881886B (en) | High-specific-strength Ti-Al-Nb-Zr-Ta refractory high-entropy alloy | |
| CN113652593A (en) | MoxNbTayTiV high-entropy alloy and preparation method thereof | |
| CN113667875A (en) | MoNbTaTiVSix high-entropy alloy and preparation method thereof | |
| CN111254298B (en) | High-entropy alloy resistant to molten aluminum corrosion and preparation method thereof | |
| CN114774752B (en) | High-strength high-toughness TiZrNbMoV refractory high-entropy alloy and preparation method thereof | |
| CN109536883B (en) | Method for improving high-temperature oxidation resistance of Ti-45Al-8.5Nb alloy | |
| CN111663070B (en) | AlCoCrFeNiSiY high-entropy alloy resistant to high-temperature oxidation and preparation method thereof | |
| CN118516580B (en) | High-temperature antioxidant high-entropy alloy material and preparation method thereof | |
| CN114134355A (en) | Strengthening and toughening control method for refractory high-entropy alloy | |
| CN112553488B (en) | CrAlNbTiVZr high-entropy alloy material and preparation method thereof | |
| CN114941098B (en) | Refractory high-entropy alloy and preparation method and application thereof | |
| CN114686741B (en) | Refractory high-entropy alloy with coating and preparation method thereof | |
| JP2021502476A (en) | Alloy turbine parts containing MAX phase | |
| CN115466867A (en) | TiAl alloy capable of improving uniform deformation capacity and preparation method thereof | |
| CN114892063A (en) | Dispersion strengthening high-strength high-temperature high-entropy alloy and preparation method thereof | |
| CN113528923A (en) | Doped multi-principal-element hydrogen storage alloy and preparation method thereof | |
| CN111254316A (en) | (MoNbZrTi) high-entropy alloy reinforced Ni-based alloy and preparation method thereof | |
| CN113088901A (en) | Nickel-chromium alloy sputtering target material and hot isostatic pressing preparation method thereof | |
| CN118773460B (en) | Re doped refractory high-entropy alloy material and preparation method thereof | |
| CN114836669B (en) | Co-Fe-Ni-V-Zr eutectic high-entropy alloy and preparation method thereof | |
| CN115747604B (en) | Mo-based high-entropy alloy and application thereof | |
| CN115216677B (en) | High-entropy alloy material with second phases uniformly distributed and reinforced and preparation method thereof | |
| CN113481418B (en) | Nickel-aluminum-molybdenum-chromium-vanadium-iron eutectic high-entropy alloy and preparation method thereof | |
| CN114058925A (en) | Mo-alloyed high-strength high-toughness high-entropy alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |