Interstitial atom reinforced high-entropy alloy and preparation method and application thereof

Abstract

The invention belongs to the technical field of metal materials, and particularly relates to an interstitial atom reinforced high-entropy alloy and a preparation method and application thereof. The chemical formula of the interstitial atom strengthened high-entropy alloy is recorded as (AlaFebNicNbdTieVfZrg) 100-x (OhSii) x according to the atomic number ratio, a is larger than or equal to 3 and smaller than or equal to 8, b is larger than or equal to 0 and smaller than or equal to 5, c is larger than or equal to 1 and smaller than or equal to 5, d is larger than or equal to 25 and smaller than or equal to 36, e is larger than or equal to 20 and smaller than or equal to 40, f is larger than or equal to 1 and smaller than or equal to 10, g is larger than or equal to 20 and smaller than or equal to 30, and a + b + c + d + e + f + g = 100. 20 < = h < = 80, 20 < = i < = 80, h + i = 100, and 0 < x < = 2. The density of the high-entropy alloy is 6.0-6.5 g / cm < 3 >, the tensile yield strength exceeds 1100 MPa, the strength at 800 DEG C is close to 400 MPa, the percentage elongation after fracture is 5%-10%, and the high-entropy alloy serves as a high-strength structural component to be used for building a high-voltage power transmission pipe network, so that the service safety of a building is enhanced.

Description

Technical Field

[0001] This invention belongs to the field of metallic materials technology, specifically relating to an interstitial atom-strengthened high-entropy alloy, its preparation method, and its application. Background Technology

[0002] High-entropy alloys, as a novel system that overturns traditional alloy design concepts, have shown great potential in achieving comprehensive properties such as high strength and high wear resistance. Among them, high-entropy alloys with refractory metal elements (such as Mo, Nb, Ta, Hf, W, Ti, Zr, V, etc.) as the main components and with a body-centered cubic (BCC) structure exhibit superior strength characteristics over a wide temperature range compared to traditional alloys, making them a key research focus for high-strength materials.

[0003] However, existing refractory metal element systems rely excessively on interactions between metallic elements, limiting the range of selectable elements to a limited number of high-density refractory metals. This results in alloys primarily using metallic bonds, making it difficult to introduce diverse chemical bonding interactions such as strong covalent bonds, thus fundamentally restricting the potential for further improvement in material properties. To achieve high strength, it is necessary to use large quantities of high-density elements such as tungsten and tantalum, leading to a significant increase in alloy density and making it difficult to meet the urgent need for lightweighting. Although some studies have attempted to introduce non-metallic elements to improve strength through interstitial strengthening or precipitation strengthening, there is a significant mutual constraint between the three key indicators of "low density," "ultra-high strength," and "good plasticity." Increasing strength often comes at the cost of sacrificing toughness and plasticity, while reducing density may weaken its strength-bearing capacity. Summary of the Invention

[0004] The purpose of this invention is to provide a high-entropy alloy with interstitial atom reinforcement, its preparation method, and its application, thereby overcoming the shortcomings of the prior art, breaking through the limitations of traditional metal element combinations, exploring the alloying effect of non-metallic elements, and ultimately achieving a synergistic improvement in high strength, low density, and good deformability. This is of vital significance for promoting the practical application of high-entropy alloys in the field of advanced manufacturing.

[0005] To achieve the above objectives, the technical solution of the present invention is as follows: In a first aspect, the present invention provides an interstitial atom-strengthened high-entropy alloy, the chemical formula of which is denoted by the atomic ratio as (Al a Fe b Ni c Nb d Ti e V f Zr g ) 100-x (O h Si i)x, where 3≤a≤8, 0≤b≤5, 1≤c≤5, 25≤d≤36, 20≤e≤40, 1≤f≤10, 20≤g≤30, a+b+c+d+e+f+g=100; 20≤h≤80, 20≤i≤80, h+i=100, and 0<x≤2.

[0006] This invention optimizes the selection of seven specific metallic elements—Al, Fe, Ni, Nb, Ti, V, and Zr—as the alloy matrix. The addition of lightweight elements (Al and Ti) reduces density, while multiple strengthening mechanisms provide ultra-high strength. The synergistic effect of refractory elements and interstitial atoms allows it to maintain high strength and high creep resistance even at high temperatures. Nb, Zr, V, and Ti are strengthened through nanoclusters rather than coarse, brittle phases, maintaining necessary ductility even at ultra-high strength. Oxygen atoms, with their small radius, tend to occupy interstitial positions in the crystal lattice. They induce strong asymmetric lattice distortion, producing a more significant strengthening effect than substitutional atoms, especially at high temperatures, effectively pinning dislocations and improving creep resistance. Si can act as a solute atom or form stable silicides (such as Nb5Si3) with certain metals (Nb and Zr). These silicides typically have high melting points and high hardness, providing additional precipitation strengthening. More importantly, the addition of Si can regulate the activity and distribution of oxygen, preventing excessive oxygen segregation at grain boundaries that could lead to embrittlement and resulting in a more uniform strengthening effect. O and Si may co-segregate to form complex (Nb, Zr, Ti)-O-Si clusters. These composite clusters exhibit higher stability and a more durable strengthening effect, especially at high temperatures where they are less prone to coarsening. Through complex chemical interactions between elements, the advantages of multiple strengthening mechanisms are complemented and synergistically enhanced, resolving the traditional contradiction between high strength, low density, and good plasticity.

[0007] Specifically, the chemical formula of interstitial atom-strengthened high-entropy alloys is denoted by the atomic ratio as (Al... a Fe b Ni c Nb d Ti e V f Zr g ) 100-x (O h Si iLet x be a, where a is one of the following: 3≤a≤5, 3≤a≤6, 5≤a≤7, or 5≤a≤8; b is one of the following: 0≤b≤2, 1≤b≤3, 2≤b≤4, or 2≤b≤5; c is one of the following: 1≤c≤2, 1≤c≤3, or 1≤c≤4; d is one of the following: 25≤d≤30, 25≤d≤35, or 28≤d≤30; e is one of the following: 20≤e≤33, 25≤e≤35, or 30≤e≤35; f is one of the following: 1≤f≤3, 2≤f≤5, 3≤f≤6, or 3≤f≤10; g is one of the following: 20≤g≤26, 25≤g≤26, or 25≤g≤30; a+b+c+d+e+f+g=100. h takes the value of 20, 30, 40, 50, 60, 70 or 80, i takes the value of 20, 30, 40, 50, 60, 70 or 80, h+i=100; x takes the value of 0.1, 0.25, 0.5, 0.75, 1, 1.5 or 2.

[0008] In some other embodiments, the chemical formula is denoted by atomic ratio as (Al). a Fe b Ni c Nb d Ti e V f Zr g ) 100-x (O h Si i )x, where 3≤a≤5, 1≤b≤2, 1≤c≤3, 25≤d≤30, 30≤e≤35, 2≤f≤5, 25≤g≤30, a+b+c+d+e+f+g=100; 20≤h≤80, 20≤i≤80, h+i=100, and 0<x≤1.

[0009] In some other embodiments, the interstitial atom-strengthened high-entropy alloy is chemically denoted by atomic ratio as (Al5Fe2Ni1Nb). 30 Ti 33 V3Zr 26 ) 99.75 (O 80 Si 20 ) 0.25 or (Al5Fe2Ni1Nb) 30 Ti 33 V3Zr 26 ) 99.75 (O 80 Si 20 ) 0.25 .

[0010] In some other embodiments, the high-entropy alloy has a BCC phase structure with a density of 6.0-6.5 g / cm³. 3 The room temperature tensile yield strength is 960 MPa-1072 MPa, and the tensile elongation is 5%-10%. The maximum tensile yield strength at 800℃ is 400 MPa. Interstitial atoms pin the grain boundaries, inhibiting grain coarsening and softening at high temperatures. The stable interface phase formed by Si and O enhances creep resistance, allowing the alloy to maintain high strength at high temperatures.

[0011] In a second aspect, the present invention provides a method for preparing the interstitial atom-strengthened high-entropy alloy described in the first aspect, comprising the following steps: (1) Add the clean metal raw materials into the electric arc furnace crucible in order of increasing melting point, with the low-melting-point metal raw materials at the bottom of the crucible, and place elemental Si and TiO at the very bottom of the metal materials; then evacuate the electric arc furnace and fill it with inert gas. (2) Under inert gas, the Ti ingot is first melted and cooled, and then the other raw materials in the crucible are melted to obtain an alloy ingot; the obtained alloy ingot is turned over and melted repeatedly until the alloy composition is uniform. (3) The obtained alloy ingot with uniform composition is hot rolled and heat treated to obtain a high entropy alloy with interstitial atom strengthening.

[0012] Traditional processes typically involve mixing all raw materials and melting them all at once, which can lead to premature volatilization of low-melting-point elements and incomplete melting of high-melting-point elements, resulting in compositional deviations and splattering. This invention employs a layered feeding method, adding materials in ascending order of melting point, with Si and TiO placed at the bottom. This design ensures that low-melting-point components are protected by the upper layers, reducing volatilization; simultaneously, high-melting-point components gradually melt within the formed molten pool, improving alloying efficiency and compositional uniformity. Melting the Ti ingot first provides a nucleation substrate for subsequent melting, inhibiting elemental segregation; multiple turnings during melting effectively eliminate microscopic segregation through forced convection, ensuring uniform distribution of key interstitial atoms such as Si and O, laying the structural foundation for subsequent strengthening. This design, by pre-placing TiO and Si, releases oxygen atoms in situ during melting, creating a synergistic strengthening effect with Si, improving strength while preventing embrittlement, achieving dual enhancement through "solid solution strengthening + interstitial strengthening."

[0013] In summary, this invention solves key problems such as difficulty in controlling the uniformity of high-entropy alloy composition, poor effect of introducing interstitial atoms, and prominent contradiction between strength and plasticity by optimizing the entire process of "ordered feeding, step-by-step melting, interstitial atom control, and thermomechanical treatment". It provides an efficient and controllable preparation path for developing high-performance interstitial atom-strengthened high-entropy alloys.

[0014] In some other embodiments, step (1) involves using elemental metals such as Al, Fe, Ni, Nb, Ti, V, and Zr with a purity greater than 99.9%.

[0015] In some other embodiments, step (2): the vacuum level inside the electric arc furnace is evacuated to 2.0 × 10⁻⁶. -3 Below Pa, the inert gas is high-purity argon.

[0016] In some other implementations, in step (2), the peak current of the melting process is greater than 300A, the melt is held for more than 1 minute during the melting process, and the melting is repeated 3-8 times.

[0017] In some other embodiments, in step (3), the hot rolling is to process the alloy ingot until the upper and lower surfaces are parallel, and the thickness of the sample after processing is 8 mm or more.

[0018] In some other embodiments, in step (3), the hot rolling temperature is 650 ℃-800 ℃ and the pressing amount is 75%-90% of the sample thickness.

[0019] In some other embodiments, in step (3), the heat treatment temperature is 700°C and the heat treatment time is 30 min.

[0020] Thirdly, the present invention provides the application of the interstitial atom-strengthened high-entropy alloy described in the first aspect in the structural materials of power transmission networks.

[0021] Fourthly, the present invention provides a structural material for a power transmission network, which adopts the high-entropy alloy with interstitial atom reinforcement as described in the first aspect.

[0022] The beneficial effects of this invention are: (1) The Al, Ti, V, Si, TiO and other elements selected in this invention are all low-density components, and an overall density of only 6.0-6.5 g / cm³ was successfully prepared. 3 This alloy series (determined by the Archimedes method) exhibits a density significantly lower than traditional high-strength steels and nickel-based superalloys, demonstrating enormous potential for lightweight applications in aerospace, transportation, and other fields with stringent weight reduction requirements.

[0023] (2) The high-entropy alloy prepared by this invention has a room temperature tensile yield strength of up to 960-1072 MPa, which is superior to most cast steels and nickel-based alloys, providing extremely high load-bearing capacity. The room temperature tensile elongation is stable at 5%-10%, indicating that the alloy retains a moderate plastic deformation capacity while possessing ultra-high strength, avoiding the brittleness risk that is usually present in high-strength materials. Under high temperature (800 ℃) conditions, based on the synergistic strengthening effect of interstitial oxygen atoms (O) and silicon atoms (Si), the alloy can still maintain a strength of close to 400 MPa, showing good resistance to high temperature softening and a wide applicable temperature range.

[0024] (3) The high-entropy alloy prepared by this invention has good room temperature deformation capability and can be used to prepare complex structural parts through conventional plastic processing technology, with good process adaptability. Its good matching of strength and plasticity provides sufficient safety margin for the components during service, effectively prevents brittle fracture, and improves the reliability of use.

[0025] In summary, this invention successfully resolves the traditional contradiction between high strength, low density, and good plasticity, resulting in a wide-temperature-range structural material with excellent comprehensive performance, which can play an important role as a key load-bearing component in high-end equipment manufacturing. Attached Figure Description

[0026] The accompanying drawings, which form part of this invention, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an improper limitation of the invention.

[0027] Figure 1 It is the (Al4Fe1Ni2Nb) prepared in Example 1 of this invention. 30 Ti 34 V3Zr 26 ) 99.75 (O 20 Si 80 ) 0.25 Room temperature stretching curve; Figure 2 It is the (Al4Fe1Ni2Nb) prepared in Example 1 of this invention. 30 Ti 34 V3Zr 26 ) 99.75 (O 20 Si 80 ) 0.25 Compression curve at 800℃; Figure 3 This is the (Al5Fe2Ni1Nb) prepared in Example 2 of the present invention. 30 Ti 33 V3Zr 26 ) 99.75 (O80 Si 20 ) 0.25 Room temperature stretching curve; Figure 4 The compression curve of the high-entropy alloy material prepared in Comparative Example 1 at room temperature is shown. Figure 5 The stress-strain curves of the high-entropy alloy material prepared in Comparative Example 2 under room temperature tensile testing are shown. Figure 6 The stress-strain curves of the high-entropy alloy material prepared in Comparative Example 3 under room temperature tensile testing are shown. Figure 7 The stress-strain curves of the high-entropy alloy material prepared in Comparative Example 4 are shown in the tensile engineering at room temperature. Detailed Implementation

[0028] Those skilled in the art will understand that the following embodiments are for illustrative purposes only and should not be construed as limiting the scope of the invention. Specific conditions not specified in the embodiments are performed under conventional conditions or conditions recommended by the manufacturer. Components whose manufacturers are not specified are all commercially available conventional products.

[0029] Example 1 This embodiment provides a high-entropy alloy with interstitial atom strengthening and its preparation method. (1) High-entropy alloy material, composed of nine elements: Al, Fe, Ni, Nb, Ti, V, Zr, O, and Si, with the chemical formula recorded in terms of atomic ratio as (Al4Fe1Ni2Nb) 30 Ti 34 V3Zr 26 ) 100-x (O 20 Si 80 ) x , where x=0.25.

[0030] (2) The preparation method of the high-entropy alloy material includes the following steps: Step 1, Grinding: Use different grades of SiC sandpaper to grind the surface of the elemental metal raw materials Al, Fe, Ni, Nb, Ti, V and Zr in sequence to remove oxide scale; TiO powder is not involved in the surface grinding process.

[0031] Step 2, Cleaning: Place the polished metal raw materials into beakers containing anhydrous ethanol and perform ultrasonic cleaning. Clean each type of raw material three times, 5 minutes each time. After cleaning, place them in a vacuum drying oven to dry, and then store them in sealed bags for later use.

[0032] Step 3, Batching: Convert the molar percentage of the interstitial atom-strengthened, low-density, high-strength, high-entropy alloy material to a mass percentage. Using a total alloy weight of 35g as a standard, weigh each element separately using an electronic balance. Step 4, Melting: First, place elemental Si and TiO powder at the bottom of the crucible. Then, add raw materials such as Al, Fe, Ni, Nb, Ti, V, and Zr into the electric arc furnace crucible in order of their melting points from lowest to highest. Close the furnace door and evacuate to a vacuum of 2.0 × 10⁻⁶. -3 Below Pa, high-purity argon gas is introduced in reverse to -0.05 MPa. First, the Ti ingot supplied to the electric arc furnace is melted twice, each melting time not less than 1 minute. After the Ti ingot solidifies, the metal material in the crucible is melted, with a peak current of 400 A each time, and the alloy is kept in a molten state for more than 1 minute each time. After each melting cycle, the alloy ingot is flipped, and each ingot is melted 6 times, ultimately obtaining a homogeneous, interstitial atom-strength, high-entropy alloy.

[0033] Step 5: Continue hot rolling and heat treatment of the smelted alloy ingot. During hot rolling, first process the alloy ingot until the upper and lower surfaces are parallel, and the thickness of the sample after processing is 8 mm or more. The hot rolling temperature is 750℃. The hot rolling reduction is 75% of the thickness. After hot rolling, the sample is heat-treated at 700℃ for 30 minutes.

[0034] Example 2 This embodiment provides a high-entropy alloy with interstitial atom reinforcement and its preparation method. (1) High-entropy alloy material, composed of nine elements: Al, Fe, Ni, Nb, Ti, V, Zr, O, and Si, with the chemical formula recorded in terms of atomic ratio as (Al5Fe2Ni1Nb). 30 Ti 33 V3Zr 26 ) 100-x (O 80 Si 20 )x, where x=0.25.

[0035] (2) The preparation method is the same as in Example 1.

[0036] Comparative Example 1 (1) Unlike Example 1, the high-strength, high-entropy alloy material has the chemical formula (Al4Fe1Ni2Nb) according to the atomic ratio. 16 Ti 34 V3Zr 40 ) 99.75 (Si 100 ) 0.25 .

[0037] (2) The smelting method is different from that in Example 1, step 5 is omitted, while the other preparation steps are the same as in Example 1.

[0038] Comparative Example 2 (1) The composition of the high-strength, high-entropy alloy material is the same as that in Example 1.

[0039] (2) The smelting method differs from that in Example 1, except that step 5 is as follows: The smelted alloy ingot is then subjected to hot rolling and heat treatment. During hot rolling, the alloy ingot is first machined until the upper and lower surfaces are parallel, and the thickness of the sample after machining is 8 mm or more. The hot rolling temperature is 500℃. The hot rolling reduction is 75% of the thickness. After hot rolling, the sample is heat-treated at 600℃ for 120 min. Other preparation steps are the same as in Example 1.

[0040] Comparative Example 3 (1) Unlike Example 1, the high-strength, high-entropy alloy material has the chemical formula (Al4Fe1Ni2Nb) according to the atomic ratio. 30 Ti 34 V3Zr 26 ) 100-x (O 100 ) x , where x=5.

[0041] (2) The preparation method of this high-entropy alloy material is different from that of Example 1 in that step 5 is omitted, while the other preparation steps are the same as those of Example 1.

[0042] Comparative Example 4 (1) The composition of the high-strength, high-entropy alloy material is the same as that in Example 1.

[0043] (2) In the preparation method of this high-entropy alloy material, the loading sequence is reversed from that in Example 1, that is, the low-melting-point Al is placed on the upper surface of the raw material, and step 5 is omitted.

[0044] Performance testing: The test results of the alloys prepared in the examples and comparative examples are shown in Table 1. Density was tested using Archimedes' displacement method. Room temperature tensile stress-strain, room temperature compressive stress-strain, elongation after fracture, and compressive strength at 800°C were tested using an electronic universal testing machine and a Gleeble thermal simulation testing machine. Specifically, the room temperature tensile test used a dog-bone shaped standard specimen with a gauge length of 10 mm, a width of 2 mm, and a thickness of 2 mm, at a tensile rate of 1.0 × 10⁻⁶. -3 S -1 Cylindrical specimens were used for room temperature and high temperature compression tests. The room temperature compression specimens had a diameter of 4 mm and a height of 9 mm. The high temperature compression specimens had a diameter of 6 mm and a height of 9 mm. To ensure the accuracy of the specimen temperature during high temperature compression, the specimens were held at that temperature for 10 minutes before compression began.

[0045] Figure 1 and 2 The (Al4Fe1Ni2Nb) prepared in Example 1 are respectively 30 Ti 34 V3Zr 26 ) 99.75 (O 20 Si 80 ) 0.25 Room temperature tensile stress-strain curves and 800℃ high-temperature compression curves of high-strength, high-entropy alloys. Figure 1 As can be seen, the yield strength of Example 1 at room temperature is close to 1100 MPa, and the elongation after fracture is about 10%, exhibiting excellent comprehensive mechanical properties. Furthermore, thanks to the high-temperature strengthening effect of Si atoms, the compressive strength of this alloy at 800℃ is close to 400 MPa. Figure 2 Its strength is higher than that of titanium alloys and some iron-based high-temperature alloys at the same temperature, showing good potential for high-temperature applications.

[0046] Figure 3 (Al5Fe2Ni1Nb) prepared in Example 2 30 Ti 33 V3Zr 26 ) 99.75 (O 80 Si 20 ) 0.25 Room temperature tensile stress-strain curves of high-strength, high-entropy alloys. Figure 3 It can be seen that the strength of Example 2 exceeds 1000 MPa and the elongation after tensile fracture exceeds 5%, demonstrating good comprehensive mechanical properties.

[0047] Figure 4 The room temperature compression curve is for Comparative Example 1. From... Figure 4 As can be seen, the room temperature compressive plasticity of this alloy is only about 5%, and there is almost no tensile plasticity.

[0048] Figure 5 The stress-strain curves for a room-temperature tensile engineering project are shown in Comparative Example 2. From... Figure 5 As can be seen, the alloy fractures before tensile yielding, exhibiting poor room temperature deformation capability.

[0049] Figure 6 The stress-strain curves for room temperature tensile engineering are shown in Comparative Example 3. From... Figure 6 As can be seen, the alloy fractures before tensile yielding, exhibiting poor room temperature mechanical properties.

[0050] Figure 7 For Comparative Example 4, the stress-strain curves for room temperature tensile engineering are shown. From... Figure 7As can be seen, the alloy fractures before tensile yielding, exhibiting poor room temperature mechanical properties.

[0051] Table 1 shows the properties of the alloys prepared in the examples and comparative examples.

[0052] As shown in Table 1, compared with the comparative examples, the alloys prepared in Examples 1 and 2 simultaneously achieved a synergistic improvement in high strength, low density, and good deformability. However, compared with Example 1, Comparative Example 1 showed a significant decrease in elongation at room temperature. This is because increasing the Nb content and decreasing the Zr content significantly increases the volume fraction of the brittle phase while correspondingly reducing the volume fraction of the matrix. In the non-metallic example, O was omitted, and a high Si content was used. However, Si, as a strong precipitation strengthening element, rapidly reacts with the high content of Nb, Ti, and other elements in the low solid solubility BCC matrix, generating a large amount of coarse, brittle silicides and / or stable Laves phases. When subjected to external forces, this significantly increased brittle phase promotes crack initiation in the brittle phase or at the brittle phase / matrix interface, and rapidly propagates along the brittle phase network, causing the material to fracture under very small plastic deformation.

[0053] Compared to Example 1, Comparative Example 2 fractured before yielding because the unsuitable heat treatment temperature (600°C) promoted the formation of brittle phases during the holding process. When tensile testing is performed, these brittle phases are inherently difficult to deform, leading to strain incompatibility with the relatively soft matrix in the early stages of deformation. This incompatibility results in numerous microcracks at the brittle phase / matrix interface or within the brittle phase itself. As strain increases, these microcracks rapidly increase, grow, and interconnect, ultimately causing the specimen to fracture and fail.

[0054] Compared to Example 1, Comparative Example 3 omitted Si in the non-metallic alloy and used a high O content, which not only led to casting defects inside the alloy but also promoted the formation of brittle phases. During deformation, these brittle phases and casting defects became crack initiation points, and the propagation and aggregation of microcracks in the early strain stage caused the sample to fracture prematurely.

[0055] Compared to Example 1, Comparative Example 4 involved directly mixing all raw materials and melting them in one go. This resulted in premature volatilization of low-melting-point elements and incomplete melting of high-melting-point elements, causing compositional deviations and melting spatter. These compositional deviations led to different microstructures and phase structures compared to Example 1, which in turn worsened the mechanical properties of the alloy.

[0056] It is evident that even with the same alloy components, differences in component content significantly affect the mechanical properties of the alloy. Furthermore, even with identical alloy compositions, differences in preparation and processing methods can lead to significant variations in mechanical properties. Therefore, the selected alloy composition and processing parameters can be determined.

[0057] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A gap-atom-strengthened high-entropy alloy, characterized in that, Chemical formula is recorded as (Al a Fe b Ni c Nb d Ti e V f Zr g ) 100-x (O h Si i )x, wherein, 3≤a≤8, 0≤b≤5, 1≤c≤5, 25≤d≤36, 20≤e≤40, 1≤f≤10, 20≤g≤30, a+b+c+d+e+f+g=100; 20≤h≤80, 20≤i≤80, h+i=100, and 0 2. The interstitial atom-strengthened high-entropy alloy of claim 1, wherein, Chemical formula is recorded as (Al a Fe b Ni c Nb d Ti e V f Zr g ) 100-x (O h Si i )x, wherein, 3≤a≤5, 1≤b≤2, 1≤c≤3, 25≤d≤30, 30≤e≤35, 2≤f≤5, 25≤g≤30, a+b+c+d+e+f+g=100; 20≤h≤80, 20≤i≤80, h+i=100, and 0 3. The interstitial atom-strengthened high-entropy alloy of claim 2, wherein, The chemical formula of the interstitial atom strengthened high-entropy alloy is (Al5Fe2Ni1Nb 30 Ti 33 V3Zr 26 ) 99.75 (O 80 Si 20 ) 0.25 or (Al5Fe2Ni1Nb 30 Ti 33 V3Zr 26 ) 99.75 (O 80 Si 20 ) 0.25 .

4. The interstitial atom-strengthened high-entropy alloy of claim 1, wherein, The high-entropy alloy has a BCC phase structure, a density of 6.0-6.5 g / cm 3 , a tensile yield strength at room temperature of 960 MPa - 1072 MPa, a tensile elongation of 5% -10%, and a maximum tensile yield strength at 800°C of 400 MPa.

5. A method of producing the interstitial atom-strengthened high-entropy alloy according to any one of claims 1 to 4, characterized by, The method comprises the following steps: (1) adding clean metal raw materials into an arc furnace crucible in order of melting point from low to high, with the metal raw material of low melting point at the bottom of the crucible, and placing Si and TiO at the bottom of the metal materials; then vacuumizing the arc furnace and filling with inert gas; (2) under the inert gas, first melting the Ti ingot, and then melting other raw materials in the crucible after the Ti ingot is cooled, to obtain an alloy ingot; the obtained alloy ingot is turned over and repeatedly melted for multiple times until the alloy composition is uniform; (3) hot-rolling and heat-treating the obtained alloy ingot with uniform composition to obtain the interstitial atom strengthened high-entropy alloy.

6. The method of claim 5, wherein the gap-atom-strengthened high-entropy alloy is prepared by a process comprising: In step (1), the metal raw materials are Al, Fe, Ni, Nb, Ti, V and Zr metal elements, with a purity of >99.9%.

7. The method of claim 5, wherein the gap atom-strengthened high-entropy alloy is prepared by a process comprising: In step (2), the vacuum degree in the electric arc furnace is drawn to 2.0 x 10 -3 Pa or below, and the inert gas is high-purity argon.

8. The method of claim 5, wherein the gap-atom-strengthened high-entropy alloy is prepared by a process comprising: In step (2), the peak current of the melting is greater than 300 A, the molten bath is maintained for more than 1 min during the melting process, and the melting is repeated for 3-8 times.

9. The method of claim 5, wherein the gap-atom-strengthened high-entropy alloy is prepared by a process comprising: In step (3), the hot-rolling is to process the alloy ingot to have parallel upper and lower surfaces, and the thickness of the sample after processing is 8 mm or more.

10. The method of claim 5, wherein the gap-atom-strengthened high-entropy alloy is prepared by a process comprising: In step (3), the hot-rolling temperature is 650-800 ℃, and the pressing amount is 75-90% of the thickness of the sample.

11. The method of claim 10, wherein the gap-atom-strengthened high-entropy alloy is prepared by a process comprising: In step (3), the heat treatment temperature is 700 ℃, and the heat treatment time is 30 min.

12. Application of the interstitial atom strengthened high-entropy alloy of any one of claims 1-4 to a structural material of a power transmission pipeline.

13. A structural material for a power transmission pipe network, characterized by The interstitial atom strengthened high-entropy alloy of any one of claims 1-4 is used.

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