Material for electromagnetic rail gun guide rail and preparation method and application thereof

Abstract

The invention discloses a material for an electromagnetic rail gun guide rail and a preparation method and application thereof, and belongs to the technical field of copper-based composite materials. The invention relates to a material for a guide rail of an electromagnetic rail gun. The material comprises a 5-20nm nano precipitated phase dispersed and distributed in a copper matrix; the MXene lamellas are continuously distributed on the grain boundary, and the nanometer MAX phase is distributed in the grain; and the nano precipitated phase, the MXene sheet layer and the nano MAX phase form a continuous reinforced network. The Cu-Ti-Be-Co alloy serves as a matrix, and unification of high strength and high conductivity is achieved through the synergistic effect of nanometer precipitated phase strengthening and MAX and MXene strengthening. The yield strength of the composite material reaches more than 700MPa and the conductivity is greater than or equal to 80% IACS (International Annealed Copper Standard) by regulating and controlling the interface combination of MAX and MXene with a matrix and the size and distribution of a nano precipitated phase, and the composite material is suitable for the fields of high-load electromagnetic guide rails, electromagnetic rail guns and the like.

Description

Technical Field

[0001] This invention relates to a material for electromagnetic railgun guides, its preparation method, and its applications, particularly to a copper-titanium-beryllium-cobalt-MXene-MAX composite material with both ultra-high strength and high conductivity, and its preparation method. This material achieves synergistic reinforcement between nano-precipitated phases and two-dimensional ceramic reinforcing phases through unique compositional design and multi-scale microstructure control. It is primarily targeted at fields such as electromagnetic railgun guides where the comprehensive performance of materials under strong electromagnetic pulses is extremely demanding. This invention belongs to the field of copper-based composite materials technology. Background Technology

[0002] Copper and its alloys play an irreplaceable role in fields such as power, electronics, rail transportation, and defense due to their excellent electrical and thermal conductivity. However, pure copper has relatively low strength (yield strength is typically below 100 MPa), making it difficult to meet the stringent requirements of modern high-tech equipment for integrated structural and functional materials. Traditional strengthening methods, such as solid solution strengthening (e.g., Cu-Cr-Zr series) and cold working strengthening, while significantly improving strength, often come at the cost of reduced conductivity. For example, solid solution atoms can severely scatter electrons, leading to a sharp decrease in conductivity. This contradictory relationship between strength and conductivity has become the core bottleneck restricting the development of high-strength, high-conductivity copper alloys.

[0003] To overcome this bottleneck, researchers are exploring two main directions: developing precipitation-strengthened copper alloys and preparing ceramic particle-reinforced copper-based composite materials.

[0004] Regarding precipitation-strengthened copper alloys, CN 117286353 A discloses a copper-chromium-niobium-zirconium alloy for electromagnetic railgun guides. This alloy achieves a certain degree of strength and toughness by forming fine precipitates in the copper matrix using elements such as Cr, Nb, and Zr. However, the controllability of the type and size distribution of precipitates in this type of alloy is limited, and it is difficult to further improve the strength beyond 550-580 MPa. Furthermore, to ensure conductivity, the total content of alloying elements is strictly limited, thus hitting a ceiling in the strengthening effect.

[0005] In composite materials, introducing high-modulus, high-strength ceramic reinforcing phases is an effective way to improve strength. CN120505536 B discloses a copper-based powder metallurgy friction material containing a pretreated MAX phase (Ti2AlN). This material improves the interfacial bonding between the MAX phase and the copper matrix through ball milling and pre-sintering treatment. Primarily used for brake pads, it prioritizes stable friction coefficients and wear resistance, rather than high electrical conductivity. This patent does not involve strengthening using nano-precipitations within the matrix alloy itself; its strength level mainly depends on the physical bonding between the ceramic particles and the matrix.

[0006] In recent years, novel two-dimensional materials MXene (such as Ti3C2T) have emerged.x Due to its unique layered structure, high electrical conductivity, and abundant surface functional groups, MXene is considered an ideal reinforcement. CN 120519732 A discloses an MXene-reinforced copper-based composite material, the innovation of which lies in the use of Cu... 2+ Self-reducing deposition on the MXene surface achieves strong interfacial bonding. However, the substrate of this patent is pure copper or ordinary copper alloy, and its strengthening source comes entirely from MXene, without combining with the precipitation strengthening effect of the substrate itself. When the amount of MXene added is high, although it can improve strength, it will cause significant damage to conductivity, and a single strengthening mechanism is unlikely to achieve a leap in strength.

[0007] In summary, the existing technology has the following shortcomings: Copper alloys can dissolve most atoms in solid solution, making it difficult to improve their strength using precipitation strengthening. Traditional methods, which rely on precipitation phases formed by the alloying elements themselves, have limited strengthening effects. Furthermore, traditional single strengthening mechanisms cannot simultaneously achieve ultra-high strength (>700 MPa) and high conductivity (>80% IACS).

[0008] For composite materials, the interface between the reinforcement and the matrix is ​​the key to the stability of performance and conductivity, and existing technologies still lack fine control over the interface.

[0009] There is a lack of material systems that combine nanoscale precipitates with micro / nanoscale two-dimensional reinforcing phases in a multi-scale, synergistic design.

[0010] Therefore, there is an urgent need in this field for a new material design and preparation method that can organically combine multiple strengthening mechanisms to achieve synergistic effects at the microscale, thereby breaking the bottleneck problem that it is difficult to simultaneously achieve both strength and conductivity in copper-based materials. Summary of the Invention

[0011] The primary objective of this invention is to overcome the shortcomings of existing technologies and provide a method for preparing materials for electromagnetic railgun guides. This method, through a specially designed compositional system and a multi-step coupled process, simultaneously introduces nanoscale intermetallic compound precipitates, MXene ceramic reinforcing phases, and MAX ceramic reinforcing phases into a copper matrix, constructing a multi-scale, multi-mechanism synergistic strengthening structure.

[0012] Another object of the present invention is to provide a composite material (i.e., a material for electromagnetic railgun guides) prepared by the above method. This material has a unique reinforcing structure at the microscopic level, thereby achieving excellent comprehensive performance at the macroscopic level with a yield strength of not less than 700 MPa and an electrical conductivity of not less than 80% IACS.

[0013] Another object of the present invention is to provide an application of a material for an electromagnetic railgun guide rail.

[0014] To solve the above-mentioned technical problems, the technical solution adopted by the present invention is as follows: To achieve the above objectives, the core of the technical solution provided by this invention lies in: using Cu-Ti-Be-Co alloy as the matrix, by introducing trace amounts of Ti, Be, and Co elements, high-density, nanoscale coherent / semi-coherent precipitates are formed during aging treatment; at the same time, pretreated MAX phase and MXene are selectively introduced as reinforcing phases, utilizing their structure and excellent intrinsic properties, and generating a synergistic effect with the matrix precipitates.

[0015] Its specific preparation method includes the following steps: Step 1: Pretreatment and structural control of the MAX / MXene-enhanced phase: This step is crucial for resolving the interface problem between the reinforcement and the matrix.

[0016] For MXene, a "mild etching-deep stratification" strategy is adopted. Taking the precursor Ti3AlC2 as an example, it is mixed with lithium fluoride (LiF) and hydrochloric acid (HCl), where the molar ratio must satisfy LiF : Ti3AlC2 ≈ (7.5~8) : 1. For example, 1g of Ti3AlC2, 1g of LiF, and 20mL of 9M or 12M HCl are used. The mixture is stirred at 350~400rpm for 36~48 hours in a water bath at 35-45℃. This mild etching condition helps to obtain MXene with a complete structure and fewer defects. After etching, the MXene is centrifuged and washed until neutral, followed by a stepwise ultrasonic treatment: first, preliminary exfoliation is performed by ultrasonication for 20-40 minutes at 80-200W in an ice-water bath, and then deep stratification is performed by ultrasonication for 30-60 minutes at 200-300W in 55-65℃. The sonicated solution was centrifuged at 2000-3000 rpm for 20-30 minutes, and the supernatant rich in few-layer MXene was collected. The supernatant was vacuum filtered and vacuum dried at 50-60℃ for 12-24 hours to obtain few-layer MXene powder for later use. This method can obtain few-layer MXene solutions with a lateral size of 1-5 μm and a thickness of 1-5 nm (i.e., 1-5 atomic layers). Transmission electron microscopy (TEM) showed that the MXene sheets prepared in this way had few wrinkles and a uniform distribution of surface functional groups (-O, -OH), providing highly active and uniform sites for its subsequent reaction with copper ions.

[0017] For MAX phases (such as Ti₂AlN), a "high-energy ball milling-morphology control" strategy is employed. MAX phase powder is ball-milled in a planetary ball mill at 300-400 rpm under high-purity argon protection for 10-20 hours. By controlling the milling time and ball-to-powder ratio (e.g., 8-10:1), the MAX phase can be broken down and exfoliated from its original tens of micrometer-sized particles into submicrometer-sized plate-like particles with a thickness between 50-200 nm and a lateral size between 0.5-2 μm. This plate-like morphology retains the layered characteristics of the MAX phase while significantly increasing the specific surface area and improving its distribution in the matrix.

[0018] Step Two: Melting and Powdering of Cu-Ti-Be-Co Matrix Alloys: The composition of the matrix alloy is the basis for achieving nano-precipitation strengthening in this invention. Its composition by mass percentage is as follows: Ti: 1.0 ~ 3.0%. Titanium is a key element in the formation of the main precipitates. Below 1.0%, the number of precipitates is insufficient; above 3.0%, coarse primary phases will form, impairing toughness and conductivity. Copper and titanium can form high-hardness Cu4Ti precipitates, improving the alloy's strength.

[0019] Be: 0.5 ~ 1.5%. Beryllium can form high-hardness intermetallic compounds such as Be₂Ti (B₂ structure) with titanium, which are the core of precipitation strengthening. Its content needs to be matched with that of titanium to ensure that the atomic ratio is close to 2:1.

[0020] Co: 0.2 ~ 1.0%. The addition of cobalt has multiple benefits: first, it can refine the grain size; second, it may participate in the formation of more complex (Cu,Co)2Ti or Co2Ti type precipitates, improving the thermal stability of the precipitates; finally, cobalt can inhibit the excessive solid solution of titanium and beryllium in copper, promoting their more complete precipitation during the aging process.

[0021] Cu: Balance.

[0022] Melting is carried out in a vacuum induction furnace at a temperature of 1450-1550℃, supplemented by electromagnetic stirring to ensure homogeneous composition. The homogeneous alloy liquid is further superheated to approximately 100℃ above the liquidus (e.g., if the alloy liquidus is approximately 1450℃, superheat to approximately 1550℃), and then guided out through a Φ4 mm diameter guide tube. At the nozzle, it is ablated into fine droplets by high-pressure (3-5 MPa) argon gas preheated to 40-50℃. By controlling this superheat and atomization pressure, the surface tension and solidification rate of the droplets can be precisely controlled, thereby obtaining powder with a target particle size range (15-53 μm) and good sphericity. This powder morphology is beneficial for subsequent uniform mixing with the two-dimensional reinforcing phase.

[0023] Step 3: Construction and Interface Engineering of Composite Powders This step aims to achieve uniform and stable dispersion of the reinforcing phase in the matrix powder and to pre-build a strong bonding interface.

[0024] Two methods are preferred: mechanical ball milling composite and solution self-assembly composite.

[0025] Method A (Mechanical Ball Milling): The Cu-Ti-Be-Co alloy powder obtained in step two and the MXene powder treated in step one (added at 0.5~5.0 wt% of the total mass of Cu-Ti-Be-Co alloy powder) are placed together in a ball mill jar. Anhydrous ethanol is used as the process control agent (the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol is 1:2). High-energy ball milling is carried out under argon protection, with a ball-to-powder ratio of 8-10:1. The ball milling parameters are crucial: a medium-low speed (250-350 rpm) and a medium time (6-10 h) are used. The purpose of this parameter design is to utilize the collision and shear force of the grinding balls to "weld" or "pin" the two-dimensional lamellar reinforcing phase onto the relatively soft copper alloy powder surface, achieving physical and mechanical interlocking, while avoiding excessive cold welding and excessive damage to the two-dimensional structure of the reinforcing phase. Scanning electron microscopy (SEM) observations showed that this method allows MXene to adhere firmly to the surface of alloy powder in a lamellar morphology, forming a "core-shell" structured composite powder, thus obtaining core-shell structure one. Core-shell structure one was then blended with MAX phase powder, with the MAX powder addition amount being 0.5-5.0 wt% of the total Cu-Ti-Be-Co alloy powder. The same ball milling process as described above was employed (specifically: using anhydrous ethanol as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 8-10:1, high-energy ball milling was performed under argon protection, using a medium-low speed of 250-350 rpm and a medium time of 6-10 h), to obtain core-shell structure two.

[0026] Method B (Solution Self-Assembly Recombination - For MXene): This method is an optimization and alternative to Method A, and is particularly suitable for MXene. Pretreatment: Place 50-100 g of Cu-Ti-Be-Co alloy powder obtained in step two into a tube furnace and heat-treat it for 20-30 minutes at 200-300°C with flowing air (flow rate 80-100 sccm) to form an extremely thin oxide layer (approximately 5-10 nm) on its surface to enhance surface polarity, obtaining a slightly oxidized alloy powder. Mix the few-layer MXene solution obtained in step one with the above-mentioned slightly oxidized alloy powder and stir under ultrasonic assistance. Specifically, disperse the above-mentioned slightly oxidized alloy powder (approximately 50-100 g) in 500 mL of a few-layer MXene aqueous solution with a concentration of 1-10 mg / mL prepared in step one (i.e., containing 0.5-5 g MXene). Subsequently, an ultrasonic-assisted self-assembly process was initiated: the mixture was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 10-30 minutes at a power range of 100-300 W and a temperature of 20-40°C. This step aims to completely dissociate MXene aggregates using ultrasonic energy and force the alloy powder and MXene sheets into full and uniform contact in the liquid, laying the foundation for subsequent electrostatic adsorption. After ultrasonic pretreatment, the mixture was transferred to a mechanical stirrer and continuously stirred at a speed of 200-300 rpm for at least 12 hours to complete the self-assembly process. Utilizing the electrostatic attraction between the negatively charged functional groups on the MXene surface and the slightly oxidized alloy powder surface, MXene sheets self-assemble, coating the alloy powder surface in single or multiple layers. This method can maximize the preservation of the intact structure and high conductivity of MXene, achieving a finer and more uniform dispersion. After drying, a core-shell structure with good interfacial contact is obtained. Then, the core-shell structure is blended with MAX phase powder and ball milled using the same process as in Method A (specifically, the amount of MAX powder added is 0.5-5.0 wt% of the total Cu-Ti-Be-Co alloy powder, anhydrous ethanol is used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol is 1:2, the ball-to-material ratio is 8-10:1, high-energy ball milling is carried out under argon protection, and medium-low speed (250-350 rpm) and medium time (6-10 h) are used to obtain a second core-shell structure.

[0027] Step 4: Densification sintering and grain structure control: Densification is achieved using spark plasma sintering (SPS) or hot isostatic pressing (HIP). SPS features rapid heating, low sintering temperature, and short holding time, effectively suppressing coarsening of the reinforcing phase and excessive growth of matrix grains. The sintering parameters are: temperature 600-900℃ (preferably 700-850℃), pressure 20-50 MPa (preferably 30-50 MPa), vacuum level below 5 Pa, heating rate 100-200℃ / min, and holding time 5-15 minutes. During this process, the combined action of strong pulsed current and axial pressure rapidly generates discharge plasma between composite powder particles, cleaning and activating the particle surface, thus achieving rapid densification. The resulting sintered green body achieves a density of over 98.5%. Metallographic analysis shows that the matrix grains are fine equiaxed crystals, with an average grain size controlled at 5-15 μm. The MAX phase and MXene-enhanced phase are confined at grain boundaries or exist within the grain, playing a role in pinning grain boundaries and hindering dislocation movement.

[0028] A similar densification effect can be achieved by hot isostatic pressing (HIP). The specific process includes: loading the composite powder into a low-carbon steel sheath, evacuating and sealing it. The sheath is then placed in a hot isostatic pressing furnace and held at 800-900℃ and 100-200 MPa argon pressure for 90-180 minutes.

[0029] Step 5: Precise Control of Aging Treatment and Nanoprecipitated Phase This is the core step in achieving matrix self-precipitation strengthening. During the service of the electromagnetic railgun, the copper rails are subjected to extremely strong currents of megahertz (MA) for a very short time, with current densities reaching up to 10. 9 A / m 2 Therefore, copper alloys are required to possess ultra-high strength (>700MPa) and high conductivity (>80% IACS). Furthermore, the strengthening phase must not degrade under strong electromagnetic pulses and must maintain morphological stability. Thus, the core technology lies in subjecting the sintered billet to multi-stage aging treatment in a protective atmosphere (such as argon or nitrogen), and accurately controlling the aging time, temperature, and intervals between each stage.

[0030] First, the sintered copper alloy undergoes solution treatment by heating it to the single-phase region (usually the α-Cu solid solution region) to dissolve all Ti atoms into the copper matrix, forming a homogeneous supersaturated solid solution, which prepares for subsequent aging precipitation. The solution treatment temperature is 800~900℃, and the time is 0.5~2 hours. Within 1 minute after solution treatment, the alloy is water-quenched to room temperature to "freeze" the supersaturated Ti atoms at room temperature, preventing the precipitation of equilibrium phases (such as coarse Cu3Ti) during cooling.

[0031] Secondly, the temperature is maintained at 450-500℃ for 1-2 hours. This stage is the nucleation and growth stage of the precipitated phases. Ti, Be, and Co atoms precipitate from the supersaturated solid solution, forming high-density spherical or cubic precipitates with a size of 5-15 nm. The precipitates in this aging step are mainly nanoscale Cu4Ti precipitates, coherent Be2Ti phases, and semi-coherent Co2Ti phases. They maintain specific crystal orientation relationships with the copper matrix, exerting an extremely strong hindrance effect on dislocation movement (the Orowan bypass mechanism and the shearing mechanism work together), and are one of the main sources of strength contribution.

[0032] Subsequently, a second stage of aging is performed: holding at 380-420℃ for 2-4 hours. The purpose of this stage is stabilization. It can make the size distribution of the precipitated nanophase more uniform, and some metastable phases transform into more stable phases, while avoiding coarsening of the precipitated phases due to excessive aging. Finally, a highly dispersed precipitate population with a size range of 5-20 nm is obtained in the matrix.

[0033] This invention discloses a material for an electromagnetic railgun guide rail, comprising a Cu-Ti-Be-Co alloy core, with Cu-Ti-Be-Co alloy powder coated with MXene phase powder to obtain a core-shell structure one, and the core-shell structure one coated with MAX phase powder to obtain a core-shell structure two. After post-processing, the core-shell structure two has 5-20 nm nano-precipitates dispersed in a copper matrix. MXene sheets are continuously distributed at the grain boundaries, and the nano-MAX phase is distributed within the grains; the nano-precipitates, MXene sheets, and nano-MAX phase form a continuous reinforcing network.

[0034] The present invention discloses a material for an electromagnetic railgun guide rail, wherein the Cu-Ti-Be-Co alloy contains 5-20 nm nano-precipitates, including nano-sized Cu4Ti precipitates, coherent Be2Ti phase and semi-coherent Co2Ti phase.

[0035] This invention relates to the application of a material for electromagnetic railgun guideways in high-load electromagnetic railguns. The high load is defined as an impact of at least 3000N within 2.5 milliseconds.

[0036] The present invention provides a material for an electromagnetic railgun guide that can withstand an impact of at least 3000N within 2.5 milliseconds on the electromagnetic railgun guide material.

[0037] An electromagnetic railgun is prepared from a rail material of an electromagnetic railgun according to the present invention.

[0038] (III) The innovativeness and beneficial effects of this invention Compared with the closest existing technology, the outstanding innovation of this invention and the beneficial effects therefrom are reflected in the following aspects: 1. Innovation and synergistic effect of material composition system design This invention innovatively selects the Cu-Ti-Be-Co quaternary alloy system as the composite matrix. This system differs from the common Cu-Cr-Zr or Cu-Ni-Si systems. The combination of Ti and Be can form a nanoscale Cu4Ti reinforcing phase and a thermodynamically stable and extremely hard Be2Ti nanoscale precipitate, with a reinforcing efficiency far exceeding that of a single Cr or Ni2Si precipitate. The introduction of Co not only provides additional precipitation reinforcement by forming Co2Ti and other phases, but more importantly, it optimizes the precipitation kinetics and morphology of Ti and Be, improving the overall thermal stability and uniformity of the precipitate group. This "Ti-Be-Co" ternary synergistic precipitation system, combined with the MAX phase and MXene reinforcing phase, constitutes the unique synergistic reinforcement structure of this invention: "nanoscale precipitate (5-20 nm) + micro / nano MXene reinforcing phase (submicron / nano thickness) + MAX reinforcing phase (submicron / nano thickness)".

[0039] 2. Morphology, distribution, and contribution of multi-scale precipitated phases to performance. By employing a precisely controlled two-stage aging process, this invention successfully constructs a high-density, ultrafine nano-precipitate network within a matrix. These precipitates are not randomly distributed but are uniformly dispersed within the grains and near the grain boundaries.

[0040] Contribution to Strength: These nanoprecipitates act as major obstacles to dislocation movement. When a dislocation encounters an impenetrable precipitate, it bypasses it via the Orowan mechanism, leaving a dislocation loop behind it. This process requires a significant amount of energy and significantly increases the rheological stress of the material. Some even finer coherent precipitates can be cut through by dislocations, similarly resulting in strengthening. This combined "bypass" and "cut" mechanism provides a remarkably substantial increase in strength.

[0041] Contribution to conductivity: Because these precipitated phases are coherent or semi-coherent with the matrix, the lattice distortion at the interface is small, and the scattering effect on electrons is much lower than that of the solid-solution atoms. More importantly, the aging treatment causes the Ti, Be, and Co atoms dissolved in the copper matrix to fully precipitate, greatly purifying the matrix lattice. This allows the electron transport channels of copper to almost return to the level of pure copper, thus achieving high strength while maintaining extremely high conductivity.

[0042] 3. Morphology, distribution, and synergistic effect of MAX and MXene-enhanced phases This invention allows for precise control of the morphology and interface of the MAX and MXene enhancement phases.

[0043] Morphology control: Through specific pretreatment, the present invention obtains not blocky MAX phases or re-stacked MXene aggregates, but sheet-like or layered two-dimensional structures. This morphology results in a larger specific surface area and maximizes the contact area with the matrix.

[0044] Distribution control: Through optimized powder composite processes (especially self-assembly), two-dimensional sheets can be continuously and in a network distributed at the grain boundaries of the matrix, forming a "grain boundary engineering" structure. Like a fence, they effectively hinder grain boundary slip and dislocation movement across grain boundaries, providing another powerful strengthening mechanism (geometrically necessary dislocation strengthening and load transfer strengthening).

[0045] Synergistic effect: This is the core of this invention. The nanoprecipitates are mainly responsible for strengthening the interior of the grains, while MAX and MXene sheets are mainly responsible for strengthening the grain boundaries. They complement each other spatially and synergize functionally, jointly constructing a comprehensive strengthening network from the nano to the micro scale. When a dislocation struggles to bypass the nanoprecipitates within the grain, it is blocked at the grain boundary by the hard MAX and MXene sheets. This multi-layered defense system enables the material's strength to achieve "1+1>2", easily exceeding the 700 MPa barrier. Simultaneously, because MXene itself has good metallic conductivity and good bonding with the matrix interface (electrons can be transported across the interface with low scattering), its negative impact on the overall conductivity is minimized.

[0046] 4. A significant leap in overall performance Through the aforementioned material design and process control, the composite material prepared by this invention achieves a breakthrough in performance. Its typical properties are: yield strength (Rp0.2) ≥ 700 MPa, tensile strength (Rm) ≥ 750 MPa, elongation (A) ≥ 8%, electrical conductivity (20℃) ≥ 80% IACS, and Vickers hardness (HV) ≥ 220. This combination of properties, especially the match between strength and electrical conductivity, significantly outperforms all existing patented materials mentioned in the background art, meeting the urgent needs of next-generation high-tech equipment for key materials.

[0047] This invention discloses a method for preparing a copper-titanium-beryllium-cobalt-MAX / MXene material for electromagnetic railgun guideways, belonging to the field of copper-based composite material technology. This material uses a Cu-Ti-Be-Co alloy as the matrix, achieving a balance between high strength and high conductivity through the synergistic effect of nano-precipitated phase reinforcement and MAX and MXene reinforcing phases. The preparation method includes: MAX and MXene pretreatment, alloy melting, powder composite, sintering, and aging treatment. By controlling the interfacial bonding between MAX and MXene and the matrix, as well as the size and distribution of the nano-precipitated phases, this invention enables the composite material to achieve a yield strength of over 700 MPa and a conductivity ≥80% IACS, making it suitable for high-load electromagnetic railguns and other applications. Attached Figure Description

[0048] Figure 1 The metallographic structure of the composite material of this invention after aging treatment; Figure 2 These are SEM images of the area near the fracture surface of the composite material of this invention, showing that the fracture mechanism is ductile fracture. Figure 3 These are the mechanical property data of the composite materials of this invention; Figure 4 This is the precipitated phase in the composite material of the present invention, which shows a nano-precipitated phase dispersed within the crystal. Detailed Implementation

[0049] The present invention will now be described in further detail with reference to the accompanying drawings and specific embodiments. The following embodiments are for illustrative purposes only and are not intended to limit the scope of the invention. Example 1

[0050] A method for preparing a material for an electromagnetic railgun guide rail includes the following steps: Step 1: Preparation of few-layer MXene ("mild etching-deep layering" method) Etching: Accurately weigh 1.0 g of Ti3AlC2MXene phase powder (precursor) with a particle size of 18-25 μm and place it in a 100 mL polytetrafluoroethylene beaker. Add 1.5 g of lithium fluoride (LiF) and 20 mL of 9 mol / L hydrochloric acid (HCl) sequentially. Place the beaker in a 40°C water bath and react continuously at 400 rpm for 36 hours. This mild condition aims to maximize etching efficiency while minimizing damage to the intrinsic structure of the MXene sheets.

[0051] Washing: After the reaction is complete, transfer the mixture to a 50 mL centrifuge tube and centrifuge at 8000 rpm for 5 minutes. Discard the supernatant (rich in Li). + Al 3+ (Impurities such as impurities). Then add 40 mL of deionized water, manually shake to redisperse the precipitate, and centrifuge again at 8000 rpm for 5 minutes. Repeat this washing process at least 8 times until the pH of the supernatant stabilizes between 6.5 and 7.0, ensuring complete removal of acidic impurities and salts.

[0052] Stratification: The precipitate obtained from the last centrifugation was dispersed in 100 mL of deionized water and subjected to stepwise ultrasonic stripping.

[0053] Phase 1: Using an ultrasonic cell disruptor (400W power), sonicate for 30 minutes at 40% amplitude (160W) under ice-water bath conditions (to prevent overheating). The purpose of this phase is to initially remove the multilayer MXene.

[0054] The second stage involves transferring the initially exfoliated solution to an ultrasonic cleaner (300W power, 40kHz frequency) and sonicating it in a 60℃ water bath for 60 minutes. This stage utilizes heat and continuous low-energy ultrasound to further dissolve the van der Waals forces between the layers, achieving deep delamination.

[0055] Collection: The sonicated solution was centrifuged at 3000 rpm for 30 minutes, and the supernatant rich in few-layer MXene was collected. The precipitate consisted of incompletely peeled thick sheets, which could be recycled. The few-layer MXene powder was obtained by vacuum filtration and vacuum drying at 60°C for 12 hours. Atomic force microscopy (AFM) analysis showed that the thickness of the obtained MXene sheets was mainly 1-3 atomic layers (approximately 1-3 nm), and the lateral dimension was 1-3 μm.

[0056] Step 2: Preparation of flake-like MAX phase (Ti2AlN) powder Commercially available Ti₂AlN bulk powder (average particle size 45 μm) was placed in a planetary ball mill jar along with stainless steel grinding balls (ball-to-powder ratio 10:1). An appropriate amount of anhydrous ethanol was added as a process control agent, with a mass-to-volume ratio of Ti₂AlN bulk powder to anhydrous ethanol of 1:2. The mixture was ball-milled at 350 rpm for 15 hours under argon protection. SEM images of the powder after ball milling showed that it transformed from irregular lumps to flakes or flattened shapes, with an average thickness of approximately 150 nm and a lateral dimension of 0.8–1.5 μm.

[0057] Step 3: Preparation of Cu-2.0Ti-1.0Be-0.5Co alloy powder ("vacuum melting-high pressure atomization" method) Batching and Smelting: Weigh out high-purity (≥99.95%) metal raw materials according to the mass percentage (Cu: 96.5%, Ti: 2.0%, Be: 1.0%, Co: 0.5%). Place copper blocks and cobalt sheets in an alumina crucible, and titanium ingots and beryllium beads in the charging bin. Evacuate the smelting chamber to 5.0 × 10⁻⁶. -3 The pressure was increased to -0.05 MPa, and then high-purity argon gas was introduced to bring the pressure to -0.05 MPa. The medium-frequency induction power supply was started, and the temperature was slowly increased to 1500℃. After the copper and cobalt were completely melted, the mixture was electromagnetically stirred for 5 minutes. Then, titanium and beryllium were added through a feeding mechanism, and electromagnetic stirring continued at 1500℃ for 20 minutes to ensure uniform alloy composition.

[0058] Atomization powder production: The uniform molten alloy is superheated to 1550℃ and then guided to flow out through a guide tube with a diameter of Φ4 mm. At the nozzle, it is broken into fine droplets by high-pressure (4.0 MPa) argon gas preheated to 50℃. The droplets are cooled as they fly through a sealed atomization tower, forming spherical powder.

[0059] Sieving: The atomized powder was collected and graded using standard sieves. Powder with a particle size range of 15-53 μm was selected for subsequent experiments. Laser particle size analysis showed that the D50 of this grade of powder was 35 μm. Scanning electron microscopy (SEM) observation showed that the powder was regularly spherical with a smooth surface, which is beneficial for uniform compounding with MXene.

[0060] Step 4: Construction of composite powder (solution self-assembly method) Pretreatment: Place 50g of alloy powder obtained in step 3 into a tube furnace and heat treat it at 300°C in flowing air (flow rate 100 sccm) for 30 minutes to form an extremely thin (about 10 nm) oxide layer on its surface to enhance surface polarity.

[0061] Self-assembly composite: The slightly oxidized alloy powder was dispersed in 500 mL of a few-layer MXene aqueous solution (containing 1 g MXene) prepared in step one, with a concentration of 2 mg / mL. The mixture was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 30 minutes at 180 W and 25 °C to fully dissociate the MXene sheets. Subsequently, it was transferred to a mechanical stirrer and stirred continuously at 250 rpm for 12 hours. During this period, the negatively charged MXene sheets spontaneously and directionally adsorbed onto the surface of the positively charged alloy powder through electrostatic forces.

[0062] Drying and sieving: After the reaction, the composite powder was collected by vacuum filtration using a Buchner funnel and washed three times with anhydrous ethanol to remove physically adsorbed MXene. It was then dried in a vacuum drying oven at 60°C for 24 hours. Finally, it was sieved through a 100-mesh standard sieve to obtain a free-flowing composite powder (core-shell structure 1). SEM characterization confirmed that the MXene sheets were uniformly and completely coated on the surface of the alloy powder, forming an ideal "core-shell" structure. The theoretical mass fraction of MXene in the composite material was 2.0 wt%.

[0063] The MAX phase powder obtained in step two was then blended with core-shell structure one, and core-shell structure two was obtained using the following ball milling process. The amount of MAX powder added was 2.0 wt% of the total Cu-Ti-Be-Co alloy powder. The ball milling process was as follows: anhydrous ethanol was used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 8:1, and high-energy ball milling was carried out under argon protection, using a medium-low speed of 300 rpm and a medium time of 8 hours to obtain core-shell structure two.

[0064] Step 5: Spark Plasma Sintering (SPS) Loading: Load approximately 60 grams of composite powder into a graphite mold with an inner diameter of Φ30 mm, and place a layer of graphite paper on both the top and bottom of the powder to facilitate demolding.

[0065] Sintering: Place the mold inside the SPS furnace chamber. Evacuate to below 5 Pa and begin the sintering process: The temperature was increased to 780℃ at a rate of 150℃ / min.

[0066] Axial pressure was applied at 780°C and gradually increased to 40 MPa within 2 minutes.

[0067] Hold at 780℃ and 40 MPa for 8 minutes.

[0068] After the heat preservation is completed, heating is stopped, pressure is released, and the furnace is cooled to below 200°C. Argon gas is then introduced to break the air vent, and the sintered billet is removed.

[0069] Post-processing: The relative density of the sintered green body was measured to be 99.2%. The graphite paper contamination layer on the surface was removed by lathe to obtain a composite material ingot with a diameter of 30mm × 10mm.

[0070] Step Six: Solution Treatment + Multi-stage Aging Treatment The SPS sintered samples were placed in a box-type resistance furnace and subjected to solution heat treatment at 800℃+1h under the protection of flowing high-purity argon gas (99.999% purity), followed by rapid water quenching. The alloy was then water quenched to room temperature within 1 minute after solution treatment. Subsequently, multi-stage aging treatment was performed. First-level aging: The sample is placed in a box-type resistance furnace and heated to 480℃ at a rate of 10℃ / min under the protection of flowing high-purity argon gas, and held for 90 minutes.

[0071] Secondary aging: Subsequently, the furnace temperature is lowered to 400℃ and held at this temperature for 180 minutes.

[0072] Cooling: After aging, the sample is quickly removed and quenched in water to fix the morphology of the precipitated phase and prevent over-aging.

[0073] This embodiment describes the application of a material for an electromagnetic railgun guide rail in high-load electromagnetic rails and electromagnetic railguns. The high load refers to an impact of up to 3000N within 2.5 milliseconds.

[0074] An electromagnetic railgun is prepared from a rail material of an electromagnetic railgun according to this embodiment.

[0075] Performance testing and microstructure analysis Mechanical properties: Tensile tests were conducted at room temperature on a universal testing machine according to GB / T 228.1 standard. The results were: yield strength (Rp0.2) 752 MPa, tensile strength (Rm) 820 MPa, and elongation after fracture (A) 9.5%. Fracture morphology (e.g.) Figure 2 The fracture described above is a typical dimple fracture, indicating that the composite material has good plasticity and toughness.

[0076] Physical properties: Conductivity was measured using a dual-bridge microohmmeter and converted to the International Standard for Annealed Copper (IACS), yielding a result of 83% IACS. Vickers hardness (HV) was 235.

[0077] Microstructure: Fine MXene sheets are mainly distributed at the grain boundaries, forming a continuous network structure. Nanoscale MXene phases (~50 nm) are distributed within the grains. Meanwhile, Cu₄Ti, Be₂Ti, and Co₂Ti precipitates of 5-15 nm are dispersed in the matrix. These reinforcing phases together constitute a highly effective reinforcing network.

[0078] SEM: such as Figure 1 As shown, due to the nanoscale size of MXene and MAX, the grain distribution of copper alloy can be clearly seen in BSE mode. After SPS process and solution aging treatment, the copper alloy structure is dense and there are no obvious defects such as pores and inclusions.

[0079] TEM: such as Figure 4 As shown, a large number of spherical precipitates with a size of approximately 8-12 nm were observed in the copper matrix, exhibiting a highly dispersed distribution. High-resolution images showed that they were coherent with the matrix, and FFT diffraction analysis confirmed them to be Cu4Ti and Be2Ti phases. A small amount of slightly larger (approximately 15 nm) blocky Co2Ti phases were also visible.

[0080] Example 2

[0081] A method for preparing a material for an electromagnetic railgun guide rail includes the following steps: Step 1: Preparation of few-layer MXene ("mild etching-deep layering" method) Etching: Accurately weigh 1.0 g of Ti3AlC2MXene phase powder (precursor) with a particle size of 18-25 μm and place it in a 100 mL polytetrafluoroethylene beaker. Add lithium fluoride (LiF) and 30 mL of 12 mol / L hydrochloric acid (HCl) sequentially, ensuring a molar ratio of LiF:Ti3AlC2 = 7.5:1. Place the beaker in a 35°C constant temperature water bath and react continuously at a mechanical stirring speed of 350 rpm for 48 hours.

[0082] Washing: After the reaction is complete, transfer the mixture to a 50 mL centrifuge tube and centrifuge at 10,000 rpm for 3 minutes. Discard the supernatant (rich in Li). + Al 3+ (Impurities such as impurities ions). Then add 40 mL of deionized water, manually shake to redisperse the precipitate, and centrifuge again at 10,000 rpm for 3 minutes. Repeat this washing process at least 8 times until the pH of the supernatant stabilizes between 6.5 and 7.0, ensuring complete removal of acidic impurities and salts.

[0083] Stratification: The precipitate obtained from the last centrifugation was dispersed in 100 mL of deionized water and subjected to stepwise ultrasonic stripping.

[0084] Phase 1: Using an ultrasonic cell disruptor (400W), ultrasonic treatment was performed for 20 minutes at 20% amplitude (80W) under ice-water bath conditions (to prevent overheating). The purpose of this phase was to initially remove the multilayer MXene.

[0085] The second stage involves transferring the initially exfoliated solution to an ultrasonic cleaner (200W power, 40kHz frequency) and sonicating it in a 55℃ water bath for 30 minutes. This stage utilizes heat and continuous low-energy ultrasound to further dissolve the van der Waals forces between the layers, achieving deep delamination.

[0086] Collection: The sonicated solution was centrifuged at 2000 rpm for 20 minutes, and the supernatant rich in few-layer MXene was collected. The precipitate consisted of incompletely peeled thick sheets, which could be recycled. The few-layer MXene powder was obtained by vacuum filtration and vacuum drying at 50°C for 24 hours. Atomic force microscopy (AFM) analysis showed that the thickness of the obtained MXene sheets was mainly 1-5 atomic layers (approximately 1-5 nm), and the lateral dimension was 1-5 μm.

[0087] Step 2: Preparation of flake-like MAX phase (Ti2AlN) powder Commercially available Ti₂AlN bulk powder (average particle size 60 μm) and stainless steel grinding balls (ball-to-powder ratio 8:1) were placed together in a planetary ball mill jar. An appropriate amount of anhydrous ethanol was added as a process control agent, with a mass-to-volume ratio of Ti₂AlN bulk powder to anhydrous ethanol of 1:2. The mixture was ball-milled at 300 rpm for 20 hours under argon protection. After ball milling, the powder morphology changed from irregular lumps to flakes or flattened shapes, with an average thickness of approximately 50 nm and a lateral dimension of 0.5–0.8 μm.

[0088] Step 3: Preparation of Cu-1.0Ti-0.5Be-0.2Co alloy powder ("vacuum melting-high pressure atomization" method) Batching and Smelting: Weigh out high-purity (≥99.95%) metal raw materials according to the mass percentage (Cu: 98.3%, Ti: 1.0%, Be: 0.5%, Co: 0.2%). Place copper blocks and cobalt sheets in an alumina crucible, and titanium ingots and beryllium beads in the charging bin. Evacuate the smelting chamber to 1.0 × 10⁻⁶. -3 The pressure was increased to -0.08 MPa, and then high-purity argon gas was introduced to bring the pressure to -0.08 MPa. The medium-frequency induction power supply was started, and the temperature was slowly increased to 1450℃. After the copper and cobalt were completely melted, the mixture was electromagnetically stirred for 5 minutes. Then, titanium and beryllium were added through a feeding mechanism, and electromagnetic stirring continued at 1450℃ for 20 minutes to ensure uniform alloy composition.

[0089] Atomization powder production: The uniform molten alloy is superheated to 1550℃ and then guided to flow out through a guide tube with a diameter of Φ4 mm. At the nozzle, it is broken into fine droplets by high-pressure (3.0 MPa) argon gas preheated to 40℃. The droplets are cooled as they fly through a sealed atomization tower, forming spherical powder.

[0090] Sieving: The atomized powder was collected and graded using standard sieves. Powder with a particle size range of 15-53 μm was selected for subsequent experiments. Laser particle size analysis showed that the D50 of this grade of powder was 34 μm. Scanning electron microscopy (SEM) observation showed that the powder was regularly spherical with a smooth surface, which is beneficial for uniform compounding with MXene.

[0091] Step 4: Construction of composite powder (solution self-assembly method) Pretreatment: Place 100g of alloy powder obtained in step 3 into a tube furnace and heat treat it at 200°C in flowing air (flow rate 80 sccm) for 20 minutes to form an extremely thin (about 5nm) oxide layer on its surface to enhance surface polarity.

[0092] Self-assembly composite: The slightly oxidized alloy powder was dispersed in 500 mL of a few-layer MXene aqueous solution (containing 0.5 g MXene) prepared in step one, with a concentration of 1 mg / mL. The mixture was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 10 minutes at 100 W and 20 °C to fully dissociate the MXene sheets. Subsequently, it was transferred to a mechanical stirrer and stirred continuously at 200 rpm for 12 hours. During this period, the negatively charged MXene sheets spontaneously and directionally adsorbed onto the surface of the positively charged alloy powder through electrostatic forces.

[0093] Drying and sieving: After the reaction, the composite powder was collected by vacuum filtration using a Buchner funnel and washed three times with anhydrous ethanol to remove physically adsorbed MXene. It was then dried in a vacuum drying oven at 50°C for 24 hours. Finally, it was sieved through a 100-mesh standard sieve to obtain a composite powder with good flowability (core-shell structure 1). SEM characterization confirmed that the MXene sheets were uniformly and completely coated on the surface of the alloy powder, forming an ideal "core-shell" structure. The theoretical mass fraction of MXene in the composite material was 0.5 wt%.

[0094] The MAX phase powder obtained in step two was then blended with core-shell structure one, and core-shell structure two was obtained using the following ball milling process. The amount of MAX powder added was 0.5 wt% of the total Cu-Ti-Be-Co alloy powder. The ball milling process was as follows: anhydrous ethanol was used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 10:1, and high-energy ball milling was carried out under argon protection, using a medium-low speed of 250 rpm and a medium time of 6 h to obtain core-shell structure two.

[0095] Step 5: Spark Plasma Sintering (SPS) Loading: Load approximately 60 grams of composite powder into a graphite mold with an inner diameter of Φ30 mm, and place a layer of graphite paper on both the top and bottom of the powder to facilitate demolding.

[0096] Sintering: Place the mold inside the SPS furnace chamber. Evacuate to below 5 Pa and begin the sintering process: The temperature was increased to 850℃ at a rate of 100℃ / min.

[0097] Axial pressure was applied at 850°C and gradually increased to 30 MPa within 2 minutes.

[0098] Hold at 850℃ and 30 MPa for 5 minutes.

[0099] After the heat preservation is completed, heating is stopped, pressure is released, and the furnace is cooled to below 200°C. Argon gas is then introduced to break the air vent, and the sintered billet is removed.

[0100] Post-processing: The relative density of the sintered green body was measured to be 98.5%. The graphite paper contamination layer on the surface was removed by lathe to obtain a composite material ingot with a diameter of 30mm and a diameter of 10mm.

[0101] Step Six: Solution Treatment + Multi-stage Aging Treatment The SPS sintered samples were placed in a box-type resistance furnace and subjected to solution heat treatment at 900℃ for 0.5 h under the protection of flowing high-purity argon gas (99.999% purity), followed by rapid water quenching. The alloy was then water quenched to room temperature within 1 min after solution treatment. Subsequently, multi-stage aging treatment was performed. First-level aging: The sample is placed in a box-type resistance furnace and heated to 450℃ at a rate of 10℃ / min under the protection of flowing high-purity argon gas, and held for 60 minutes.

[0102] Secondary aging: Subsequently, the furnace temperature is lowered to 380℃ and held at this temperature for 120 minutes.

[0103] Cooling: After aging, the sample is quickly removed and quenched in water to fix the morphology of the precipitated phase and prevent over-aging.

[0104] This embodiment describes the application of a material for an electromagnetic railgun guide rail in high-load electromagnetic rails and electromagnetic railguns. The high load refers to an impact of up to 3000N within 2.5 milliseconds.

[0105] An electromagnetic railgun is prepared from a rail material of an electromagnetic railgun according to this embodiment.

[0106] Performance testing and microstructure analysis Mechanical properties: Tensile testing was conducted at room temperature on a universal testing machine according to GB / T 228.1 standard. The results showed a yield strength (Rp0.2) of 700 MPa. Figure 3 As shown), the tensile strength (Rm) is 750 MPa and the elongation after fracture (A) is 8%.

[0107] Physical properties: Conductivity was measured using a dual-bridge microohmmeter and converted to the International Standard for Annealed Copper (IACS), yielding a result of 80% IACS. Vickers hardness (HV) was 220.

[0108] Example 3

[0109] A method for preparing a material for an electromagnetic railgun guide rail includes the following steps: Step 1: Preparation of few-layer MXene ("mild etching-deep layering" method) Etching: Accurately weigh 1.0 g of Ti3AlC2MXene phase powder (precursor) with a particle size of 18-25 μm and place it in a 100 mL polytetrafluoroethylene beaker. Add lithium fluoride (LiF) and 30 mL of 12 mol / L hydrochloric acid (HCl) sequentially, ensuring a molar ratio of LiF:Ti3AlC2 = 8:1. Place the beaker in a 45℃ constant temperature water bath and react continuously for 40 hours with mechanical stirring at 400 rpm.

[0110] Washing: After the reaction is complete, transfer the mixture to a 50 mL centrifuge tube and centrifuge at 8000 rpm for 3 minutes. Discard the supernatant (rich in Li). + Al 3+ (Impurities such as impurities). Then add 40 mL of deionized water, manually shake to redisperse the precipitate, and centrifuge again at 8000 rpm for 5 minutes. Repeat this washing process at least 8 times until the pH of the supernatant stabilizes between 6.5 and 7.0, ensuring complete removal of acidic impurities and salts.

[0111] Stratification: The precipitate obtained from the last centrifugation was dispersed in 100 mL of deionized water and subjected to stepwise ultrasonic stripping.

[0112] Phase 1: Using an ultrasonic cell disruptor (400W power), ultrasonic treatment was performed for 40 minutes at 50% amplitude (200W) under ice-water bath conditions (to prevent overheating). The purpose of this phase was to initially remove the multilayer MXene.

[0113] The second stage involves transferring the initially exfoliated solution to an ultrasonic cleaner (300W power, 40kHz frequency) and sonicating it in a 65℃ water bath for 45 minutes. This stage utilizes heat and continuous low-energy ultrasound to further dissolve the van der Waals forces between the layers, achieving deep delamination.

[0114] Collection: The sonicated solution was centrifuged at 3000 rpm for 30 minutes, and the supernatant rich in few-layer MXene was collected. The precipitate consisted of incompletely peeled thick sheets, which could be recycled. The few-layer MXene powder was obtained by vacuum filtration and vacuum drying at 60°C for 12 hours. Atomic force microscopy (AFM) analysis showed that the thickness of the obtained MXene sheets was mainly 1-4 atomic layers (approximately 1-4 nm), and the lateral dimension was 1-4 μm.

[0115] Step 2: Preparation of flake-like MAX phase (Ti2AlN) powder Commercially available Ti₂AlN bulk powder (average particle size 50 μm) was placed in a planetary ball mill jar along with stainless steel grinding balls (ball-to-powder ratio 9:1). An appropriate amount of anhydrous ethanol was added as a process control agent, with a mass-to-volume ratio of Ti₂AlN bulk powder to anhydrous ethanol of 1:2. The mixture was ball-milled at 400 rpm for 10 hours under argon protection. SEM morphology of the powder after ball milling showed that it transformed from irregular lumps to flakes or flattened shapes, with an average thickness of approximately 200 nm and a lateral dimension of 1.2–2 μm.

[0116] Step 3: Preparation of Cu-3.0Ti-1.5Be-1.0Co alloy powder ("vacuum melting-high pressure atomization" method) Batching and Smelting: Weigh out high-purity (≥99.95%) metal raw materials according to the mass percentage (Cu: 94.5%, Ti: 3.0%, Be: 1.5%, Co: 1.0%). Place copper blocks and cobalt sheets in an alumina crucible, and titanium ingots and beryllium beads in the charging bin. Evacuate the smelting chamber to 5.0 × 10⁻⁶. -3 The pressure was increased to -0.05 MPa, and then high-purity argon gas was introduced to bring the pressure to -0.05 MPa. The medium-frequency induction power supply was started, and the temperature was slowly increased to 1550℃. After the copper and cobalt were completely melted, the mixture was electromagnetically stirred for 5 minutes. Then, titanium and beryllium were added through a feeding mechanism, and electromagnetic stirring continued at 1550℃ for 20 minutes to ensure uniform alloy composition.

[0117] Atomization powder production: The uniform molten alloy is superheated to 1550℃ and then guided to flow out through a guide tube with a diameter of Φ4 mm. At the nozzle, it is broken into fine droplets by high-pressure (5.0 MPa) argon gas preheated to 45℃. The droplets are cooled as they fly through a sealed atomization tower, forming spherical powder.

[0118] Sieving: The atomized powder was collected and graded using standard sieves. Powder with a particle size range of 15-53 μm was selected for subsequent experiments. Laser particle size analysis showed that the D50 of this grade of powder was 38 μm. Scanning electron microscopy (SEM) observation showed that the powder was regularly spherical with a smooth surface, which is beneficial for uniform compounding with MXene.

[0119] Step 4: Construction of composite powder (solution self-assembly method) Pretreatment: Place 100g of alloy powder obtained in step 3 into a tube furnace and heat treat it at 300°C in flowing air (flow rate 100 sccm) for 30 minutes to form an extremely thin (about 10 nm) oxide layer on its surface to enhance surface polarity.

[0120] Self-assembly composite: The slightly oxidized alloy powder was dispersed in 500 mL of a 10 mg / mL few-layer MXene aqueous solution prepared in step one (i.e., containing 5 g of MXene). The mixture was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 20 minutes at 300 W and 40 °C to fully dissociate the MXene sheets. Subsequently, it was transferred to a mechanical stirrer and stirred continuously at 300 rpm for 18 hours. During this period, the negatively charged MXene sheets spontaneously and directionally adsorbed onto the surface of the positively charged alloy powder through electrostatic forces.

[0121] Drying and sieving: After the reaction, the composite powder was collected by vacuum filtration using a Buchner funnel and washed three times with anhydrous ethanol to remove physically adsorbed MXene. It was then dried in a vacuum drying oven at 50°C for 24 hours. Finally, it was sieved through a 100-mesh standard sieve to obtain a composite powder with good flowability (core-shell structure 1). SEM characterization confirmed that the MXene sheets were uniformly and completely coated on the surface of the alloy powder, forming an ideal "core-shell" structure. The theoretical mass fraction of MXene in the composite material was 5 wt%.

[0122] The MAX phase powder obtained in step two was then blended with core-shell structure one, and core-shell structure two was obtained using the following ball milling process. The amount of MAX powder added was 5 wt% of the total Cu-Ti-Be-Co alloy powder. The ball milling process was as follows: anhydrous ethanol was used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 9:1, and high-energy ball milling was carried out under argon protection, using a medium-low speed of 350 rpm and a medium time of 10 h to obtain core-shell structure two.

[0123] Step 5: Spark Plasma Sintering (SPS) Loading: Load approximately 60 grams of composite powder into a graphite mold with an inner diameter of Φ30 mm, and place a layer of graphite paper on both the top and bottom of the powder to facilitate demolding.

[0124] Sintering: Place the mold inside the SPS furnace chamber. Evacuate to below 5 Pa and begin the sintering process: The temperature was increased to 700℃ at a rate of 200℃ / min.

[0125] Axial pressure was applied at 700°C and gradually increased to 50 MPa within 2 minutes.

[0126] Hold at 700℃ and 50 MPa for 15 minutes.

[0127] After the heat preservation is completed, heating is stopped, pressure is released, and the furnace is cooled to below 200°C. Argon gas is then introduced to break the air vent, and the sintered billet is removed.

[0128] Post-processing: The relative density of the sintered green body was measured to be 98.9%. The graphite paper contamination layer on the surface was removed by lathe to obtain a composite material ingot with a diameter of 30mm and a diameter of 10mm.

[0129] Step Six: Solution Treatment + Multi-stage Aging Treatment The SPS sintered samples were placed in a box furnace and subjected to solution heat treatment at 850℃ for 2 hours under the protection of flowing high-purity argon gas (99.999% purity), followed by rapid water quenching. The alloy was then water quenched to room temperature within 1 minute after solution treatment. Subsequently, multi-stage aging treatment was performed. First-level aging: The sample is placed in a box-type resistance furnace and heated to 500℃ at a rate of 10℃ / min under the protection of flowing high-purity argon gas, and held for 120 minutes.

[0130] Secondary aging: Subsequently, the furnace temperature is lowered to 420℃ and held at this temperature for 240 minutes.

[0131] Cooling: After aging, the sample is quickly removed and quenched in water to fix the morphology of the precipitated phase and prevent over-aging.

[0132] This embodiment describes the application of a material for an electromagnetic railgun guide rail in high-load electromagnetic rails and electromagnetic railguns. The high load refers to an impact of up to 3500N within 2.5 milliseconds.

[0133] An electromagnetic railgun is prepared from a rail material of an electromagnetic railgun according to this embodiment.

[0134] Performance testing and microstructure analysis Mechanical properties: Tensile tests were conducted at room temperature on a universal testing machine according to GB / T 228.1 standard. The results were: yield strength (Rp0.2) 718 MPa, tensile strength (Rm) 770 MPa, and elongation after fracture (A) 8.2%.

[0135] Physical properties: Conductivity was measured using a double-bridge microohmmeter and converted to the International Standard for Annealed Copper (IACS), yielding a result of 81% IACS. Vickers hardness (HV) was 224.

[0136] Example 4

[0137] The only difference between this embodiment and Embodiment 1 is that: In step five, the temperature is increased to 600℃ at a rate of 120℃ / min. At 600℃, axial pressure is applied and gradually increased to 20 MPa within 2 minutes. The temperature is then maintained at 600℃ and 20 MPa for 8 minutes.

[0138] Example 5

[0139] The only difference between this embodiment and Embodiment 1 is that: In step five, the temperature is increased to 900℃ at a rate of 180℃ / min. At 900℃, axial pressure is applied and gradually increased to 35 MPa within 2 minutes. The temperature is then maintained at 900℃ and 35 MPa for 12 minutes.

[0140] Example 6

[0141] The only difference between this embodiment and Embodiment 1 is that: The construction of the composite powder in step four ("solution self-assembly" method) was replaced by mechanical ball milling composite method. Specifically, the Cu-Ti-Be-Co alloy powder obtained in step three and the MXene powder treated in step one (added at 0.5 wt% of the total mass of Cu-Ti-Be-Co alloy powder) were placed together in a ball mill jar with a ball-to-powder ratio of 8:1. Anhydrous ethanol was used as the process control agent (the added volume of anhydrous ethanol was twice the mass of Cu-Ti-Be-Co alloy powder, in mL:g). High-energy ball milling was carried out under argon protection: a medium-low speed of 250 rpm and a medium time of 6 h were used to obtain the core-shell structure. The core-shell structure was then blended with MAX phase powder. The amount of MAX powder added was 0.5 wt% of the total Cu-Ti-Be-Co alloy powder. The process was ball milling: anhydrous ethanol was used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 8:1, and high-energy ball milling was carried out under argon protection. The process was carried out at a medium-low speed of 250 rpm and a medium time of 6 h to obtain the second core-shell structure.

[0142] Example 7

[0143] The only difference between this embodiment and Embodiment 1 is that: The construction of the composite powder in step four ("solution self-assembly" method) was replaced by mechanical ball milling composite method. Specifically, the Cu-Ti-Be-Co alloy powder obtained in step three and the MXene powder treated in step one (added at 5 wt% of the total mass of Cu-Ti-Be-Co alloy powder) were placed together in a ball mill jar with a ball-to-powder ratio of 10:1. Anhydrous ethanol was used as the process control agent (the added volume of anhydrous ethanol was twice the mass of Cu-Ti-Be-Co alloy powder, in mL:g). High-energy ball milling was carried out under argon protection: a medium-low speed of 350 rpm and a medium time of 10 h were used to obtain the core-shell structure. The core-shell structure was then blended with MAX phase powder. The amount of MAX powder added was 5 wt% of the total Cu-Ti-Be-Co alloy powder. The process was ball milling: anhydrous ethanol was used as the process control agent, the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol was 1:2, the ball-to-material ratio was 10:1, and high-energy ball milling was carried out under argon protection. The process was carried out at a medium-low speed of 350 rpm and a medium time of 10 h to obtain the second core-shell structure.

[0144] Example 8

[0145] The only difference between this embodiment and Embodiment 1 is that: Hot isostatic pressing (HIP) was used to replace spark plasma sintering (SPS) in step five. Specifically, the HIP process was as follows: the composite powder was packed into a low-carbon steel sheath, which was then evacuated and sealed. The sheath was placed in a hot isostatic pressing furnace and held at 800°C and 100 MPa argon pressure for 90 minutes.

[0146] Example 9

[0147] The only difference between this embodiment and Embodiment 1 is that: Hot isostatic pressing (HIP) was used to replace spark plasma sintering (SPS) in step five. Specifically, the HIP process was as follows: the composite powder was packed into a low-carbon steel sheath, which was then evacuated and sealed. The sheath was placed in a hot isostatic pressing furnace and held at 900°C and 200 MPa argon pressure for 180 minutes.

[0148] Comparative Example 1: MXene-reinforced phase + Cu-Ti-Be-Co alloy MXene-reinforced Cu-Ti-Be-Co composites (Objective: Optimal balance between strength and conductivity) Step 1: Preparation of few-layer MXene ("mild etching-deep layering" method) Etching: Accurately weigh 1.0 g of Ti3AlC2MXene phase powder (precursor) with a particle size of 18-25 μm and place it in a 100 mL polytetrafluoroethylene beaker. Add 1.5 g of lithium fluoride (LiF) and 20 mL of 9 mol / L hydrochloric acid (HCl) sequentially. Place the beaker in a 40°C water bath and react continuously at 400 rpm for 36 hours. This mild condition aims to maximize etching efficiency while minimizing damage to the intrinsic structure of the MXene sheets.

[0149] Washing: After the reaction is complete, transfer the mixture to a 50 mL centrifuge tube and centrifuge at 8000 rpm for 5 minutes. Discard the supernatant (rich in Li). + Al 3+ (Impurities such as impurities). Then add 40 mL of deionized water, manually shake to redisperse the precipitate, and centrifuge again at 8000 rpm for 5 minutes. Repeat this washing process at least 8 times until the pH of the supernatant stabilizes between 6.5 and 7.0, ensuring complete removal of acidic impurities and salts.

[0150] Stratification: The precipitate obtained from the last centrifugation was dispersed in 100 mL of deionized water and subjected to stepwise ultrasonic stripping.

[0151] Phase 1: Using an ultrasonic cell disruptor (400W power), sonicate for 30 minutes at 40% amplitude (160W) under ice-water bath conditions (to prevent overheating). The purpose of this phase is to initially remove the multilayer MXene.

[0152] The second stage involves transferring the initially exfoliated solution to an ultrasonic cleaner (300W power, 40kHz frequency) and sonicating it in a 60℃ water bath for 60 minutes. This stage utilizes heat and continuous low-energy ultrasound to further dissolve the van der Waals forces between the layers, achieving deep delamination.

[0153] Collection: The sonicated solution was centrifuged at 3000 rpm for 30 minutes, and the supernatant rich in few-layer MXene was collected. The precipitate consisted of incompletely peeled thick sheets, which could be recycled. The few-layer MXene powder was obtained by vacuum filtration and vacuum drying at 60°C for 12 hours. Atomic force microscopy (AFM) analysis showed that the thickness of the obtained MXene sheets was mainly 1-3 atomic layers (approximately 1-3 nm), and the lateral dimension was 1-3 μm.

[0154] Step 2: Preparation of Cu-2.0Ti-1.0Be-0.5Co alloy powder ("vacuum melting-high pressure atomization" method) Batching and Smelting: Weigh out high-purity (≥99.95%) metal raw materials according to the mass percentage (Cu: 96.5%, Ti: 2.0%, Be: 1.0%, Co: 0.5%). Place copper blocks and cobalt sheets in an alumina crucible, and titanium ingots and beryllium beads in the charging bin. Evacuate the smelting chamber to 5.0 × 10⁻⁶. -3 The pressure was increased to -0.05 MPa, and then high-purity argon gas was introduced to bring the pressure to -0.05 MPa. The medium-frequency induction power supply was started, and the temperature was slowly increased to 1500℃. After the copper and cobalt were completely melted, the mixture was electromagnetically stirred for 5 minutes. Then, titanium and beryllium were added through a feeding mechanism, and electromagnetic stirring continued at 1500℃ for 20 minutes to ensure uniform alloy composition.

[0155] Atomization powder production: The uniform molten alloy is superheated to 1550℃ and then guided to flow out through a guide tube with a diameter of Φ4 mm. At the nozzle, it is broken into fine droplets by high-pressure (4.0 MPa) argon gas preheated to 50℃. The droplets are cooled as they fly through a sealed atomization tower, forming spherical powder.

[0156] Sieving: The atomized powder was collected and graded using standard sieves. Powder with a particle size range of 15-53 μm was selected for subsequent experiments. Laser particle size analysis showed that the D50 of this grade of powder was 35 μm. Scanning electron microscopy (SEM) observation showed that the powder was regularly spherical with a smooth surface, which is beneficial for uniform compounding with MXene.

[0157] Step 3: Construction of composite powder (solution self-assembly method) Pretreatment: Place 50g of alloy powder obtained in step 2 into a tube furnace and heat treat it at 300℃ in flowing air (flow rate 100 sccm) for 30 minutes to form an extremely thin oxide layer (about 5-10 nm) on its surface to enhance surface polarity.

[0158] Self-assembly composite: The slightly oxidized alloy powder was dispersed in 500 mL of a few-layer MXene aqueous solution (containing 1 g MXene) prepared in step one, with a concentration of 2 mg / mL. The mixture was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 30 minutes at 180 W and 25 °C to fully dissociate the MXene sheets. Subsequently, it was transferred to a mechanical stirrer and stirred continuously at 250 rpm for 12 hours. During this period, the negatively charged MXene sheets spontaneously and directionally adsorbed onto the surface of the positively charged alloy powder through electrostatic forces.

[0159] Drying and sieving: After the reaction, the composite powder was collected by vacuum filtration using a Buchner funnel and washed three times with anhydrous ethanol to remove physically adsorbed MXene. It was then dried in a vacuum drying oven at 60°C for 24 hours. Finally, it was sieved through a 100-mesh standard sieve to obtain a final composite powder with good flowability. SEM characterization confirmed that the MXene sheets were uniformly and completely coated on the surface of the alloy powder, forming an ideal "core-shell" structure. The theoretical mass fraction of MXene in the composite material was 2.0 wt%.

[0160] Step 4: Spark Plasma Sintering (SPS) Loading: Load approximately 60 grams of composite powder into a graphite mold with an inner diameter of Φ30 mm, and place a layer of graphite paper on both the top and bottom of the powder to facilitate demolding.

[0161] Sintering: Place the mold inside the SPS furnace chamber. Evacuate to below 5 Pa and begin the sintering process: The temperature was increased to 780℃ at a rate of 150℃ / min.

[0162] Axial pressure was applied at 780°C and gradually increased to 40 MPa within 2 minutes.

[0163] Hold at 780℃ and 40 MPa for 8 minutes.

[0164] After the heat preservation is completed, heating is stopped, pressure is released, and the furnace is cooled to below 200°C. Argon gas is then introduced to break the air vent, and the sintered billet is removed.

[0165] Post-processing: The relative density of the sintered green body was measured to be 98.0%. The graphite paper contamination layer on the surface was removed by lathe to obtain a composite material ingot with a diameter of 30mm and a diameter of 10mm.

[0166] Step 5: Solution treatment + multi-stage aging treatment The SPS sintered samples were placed in a box-type resistance furnace and subjected to solution heat treatment at 800℃+1h under the protection of flowing high-purity argon gas (99.999% purity), followed by rapid water quenching. The alloy was then water quenched to room temperature within 1 minute after solution treatment. Subsequently, multi-stage aging treatment was performed. First-level aging: The sample is placed in a box-type resistance furnace and heated to 480℃ at a rate of 10℃ / min under the protection of flowing high-purity argon gas, and held for 90 minutes.

[0167] Secondary aging: Subsequently, the furnace temperature is lowered to 400℃ and held at this temperature for 180 minutes.

[0168] Cooling: After aging, the sample is quickly removed and quenched in water to fix the morphology of the precipitated phase and prevent over-aging.

[0169] Performance testing and microstructure analysis Mechanical properties: Tensile tests were conducted at room temperature on a universal testing machine according to GB / T 228.1 standard. The results were: yield strength (Rp0.2) 628 MPa, tensile strength (Rm) 685 MPa, and elongation after fracture (A) 9.5%.

[0170] Physical properties: Conductivity was measured using a dual-bridge microohmmeter and converted to the International Standard for Annealed Copper (IACS), yielding a result of 65% IACS. Vickers hardness (HV) was 186.

[0171] This comparative example uses MXene as a single reinforcing phase, which has a limited effect on improving the mechanical properties of the alloy material.

[0172] Comparative Example 2: MAX-reinforced phase + Cu-Ti-Be-Co alloy MAX phase reinforced Cu-Ti-Be-Co composite material (Target: high wear resistance and high temperature stability) Step 1: Preparation of flaky MAX phase (Ti2AlN) powder Commercially available Ti₂AlN bulk powder (average particle size 45 μm) was placed in a planetary ball mill jar along with stainless steel grinding balls (ball-to-powder ratio 10:1), and an appropriate amount of anhydrous ethanol was added as a process control agent. The mixture was ball-milled at 350 rpm for 15 hours under argon protection. SEM images of the powder after milling showed that it transformed from an irregular blocky shape to a flake or flattened shape, with an average thickness of approximately 150 nm and a lateral dimension of 0.8–1.5 μm.

[0173] Step 2: Preparation of Cu-1.5Ti-0.8Be-0.3Co alloy powder The method is the same as step two of Example 1, except that the composition is adjusted to: Ti: 1.5%, Be: 0.8%, Co: 0.3%, with the balance being Cu. After atomization, sieve 15-53 μm powder for later use.

[0174] Step 3: Construction of composite powder ("mechanical ball milling composite" method) 50 g of alloy powder and 3.0 wt% (1.55 g) of flaky MAX phase powder were weighed and placed together in a ball mill jar. 100 mL of anhydrous ethanol was added, resulting in a ball-to-powder ratio of 8:1. The mixture was ball-milled at 300 rpm for 8 hours under argon protection. SEM analysis of the milled powder showed that the MAX phase flakes were firmly embedded or pressed onto the surface of the alloy powder, which had undergone significant plastic deformation.

[0175] Step 4: Hot Isostatic Pressing (HIP) Sintering The composite powder was packed into a low-carbon steel sheath, which was then evacuated and sealed. The sheath was placed in a hot isostatic pressing furnace and held at 820°C and 150 MPa argon pressure for 120 minutes. This high-temperature and high-pressure condition is beneficial for achieving complete densification and promoting interfacial bonding.

[0176] Step 5: Solution treatment + multi-stage aging treatment The HIP-sintered samples were placed in a box-type resistance furnace and subjected to solution heat treatment at 800℃+1h under the protection of flowing high-purity argon gas (99.999% purity), followed by rapid water quenching. The alloy was then water quenched to room temperature within 1 minute after solution treatment. Subsequently, multi-stage aging treatment was performed. First-level aging: The sample is placed in a box-type resistance furnace and heated to 480℃ at a rate of 10℃ / min under the protection of flowing high-purity argon gas, and held for 90 minutes.

[0177] Secondary aging: Subsequently, the furnace temperature is lowered to 400℃ and held at this temperature for 180 minutes.

[0178] Cooling: After aging, the sample is quickly removed and quenched in water to fix the morphology of the precipitated phase and prevent over-aging.

[0179] Performance and Structure Properties: Yield strength 619 MPa, electrical conductivity 43% IACS, hardness (HV) 172. Its abrasion resistance (through pin-disc wear test) is approximately 15% higher than that of Comparative Example 1.

[0180] Structure: Metallographic analysis shows a uniform distribution of the MAX phase. TEM analysis reveals that the precipitated phase is slightly larger, approximately 30-40 nm, but still maintains high density. No obvious cracks or pores were observed at the interface between the MAX phase and the matrix, indicating good bonding.

[0181] Comparative Example 3: MXene and MAX hybrid enhancement of Cu-Ti-Be-Co, rather than core-shell structure II MXene and MAX hybrid reinforced Cu-Ti-Be-Co composite materials

[0182] The processes in steps one and two are the same as in comparative example 1.

[0183] In step three, 50 g of alloy powder was mechanically ball-milled with 1.0 wt% MXene + 1.5 wt% nano-MAX powder (particle size 50 nm) (parameters same as in step three of Comparative Example 2).

[0184] The SPS parameters for step four are adjusted to: 800℃, 45 MPa, 10 min.

[0185] The aging process in step five is the same as in comparative example 1.

[0186] Performance and Structure Performance: Yield strength reaches a peak of 625 MPa, conductivity is 57% IACS, and elongation is 7.8%.

[0187] Comparative Example 4: Cu-2.0Ti-1.0Be-0.5Co alloy To demonstrate the superiority of the synergistic effect of this invention, Comparative Example 4 was set up: using only Cu-2.0Ti-1.0Be-0.5Co alloy (without any dispersed strengthening phase), after sintering, solution treatment, and aging using the same process as Comparative Example 1, its yield strength was 520 MPa and its conductivity was 88% IACS. This shows that it is difficult to exceed 550 MPa with strength achieved solely through matrix precipitation strengthening.

[0188] Comparative Example 5: The only difference between this comparative example and Example 1 is that the solution treatment is omitted in step six.

[0189] Properties: Yield strength 608MPa, conductivity 71% IACS, hardness (HV) 165.

[0190] Comparative Example 6: The only difference between this comparative example and Example 1 is that in step six, a single-stage aging treatment of 450℃ for 240 minutes is used, followed by air cooling instead of multi-stage aging treatment.

[0191] Properties: Yield strength 637MPa, conductivity 75% IACS, hardness (HV) 194.

[0192] Comparative Example 7: The only difference between this comparative example and Example 1 is that: Step one involved a single-stage ultrasonic exfoliation: using an ultrasonic cell disruptor (400W power), under ice-water bath conditions (to prevent overheating), the cells were sonicated at 40% amplitude (160W) for 90 minutes. The sonicated solution was centrifuged at 3000 rpm for 30 minutes, and the supernatant rich in few-layer MXene was collected. The precipitate consisted of incompletely exfoliated thick sheets, which could be recycled. The MXene powder was obtained by vacuum filtration and vacuum drying at 60°C for 12 hours. Atomic force microscopy (AFM) analysis showed that the obtained MXene sheets were primarily 8-15 atomic layers thick (approximately 8-15 nm) with a lateral dimension of 8-15 μm.

[0193] Properties: Yield strength 655MPa, conductivity 73% IACS, hardness (HV) 208.

[0194] It should be understood that, in order to simplify this disclosure and aid in understanding one or more of the various aspects of the invention, features of the invention are sometimes grouped together in a single embodiment, figure, or description thereof in the above description of exemplary embodiments of the invention. However, this method of disclosure should not be interpreted as reflecting an intention that the claimed invention requires more features than expressly recited in each claim. Rather, as reflected in the claims, inventive aspects lie in fewer than all the features of the foregoingly disclosed embodiments. Therefore, the claims, following the detailed description, are hereby expressly incorporated into that detailed description, wherein each claim itself is a separate embodiment of the invention.

[0195] Although the invention has been described with reference to a limited number of embodiments, those skilled in the art will understand from the foregoing description that other embodiments are conceivable within the scope of the invention described herein. Furthermore, it should be noted that the language used in this specification has been chosen primarily for readability and instructional purposes, and not for the purpose of interpreting or limiting the subject matter of the invention. Therefore, many modifications and variations will be apparent to those skilled in the art without departing from the scope and spirit of the appended claims. The disclosure of the invention is illustrative and not restrictive, and the scope of the invention is defined by the appended claims.

[0196] The above description is only a preferred embodiment of the present invention. It should be noted that for those skilled in the art, several improvements and modifications can be made without departing from the principle of the present invention, and these improvements and modifications should also be considered within the scope of protection of the present invention.

Claims

1. A material for an electromagnetic railgun guide rail, characterized in that, include: 5-20 nm nano-precipitates dispersed in a copper matrix; MXene sheets are continuously distributed at the grain boundaries, while the nano-MAX phase is distributed within the grains; The nano-precipitated phase, MXene sheets, and nano-MAX phase form a continuous reinforcement network.

2. The material for an electromagnetic railgun guide rail according to claim 1, characterized in that, It is composed of the following components by mass percentage: Ti: 1.0~3.0%, Be: 0.5~1.5%, Co: 0.2~1.0%, with the balance being Cu.

3. The material for an electromagnetic railgun guide rail according to claim 1, characterized in that, Yield strength ≥700MPa, tensile strength ≥750 MPa, elongation ≥8%, electrical conductivity (20℃) ≥80% IACS, Vickers hardness ≥220HV.

4. A method for preparing a material for an electromagnetic railgun guide rail according to any one of claims 1 to 3, characterized in that, Includes the following steps: Step 1, Pretreatment of the MXene-enhanced phase: Mix the MXene precursor with lithium fluoride and hydrochloric acid, with a molar ratio of lithium fluoride to MXene precursor of (7.5~8):1, and a mass ratio of MXene precursor to hydrochloric acid of 1:(20~30). The hydrochloric acid is a 9M or 12M HCl solution. Stir at 350~400 rpm for 36~48 hours in a water bath at 35-45℃. After etching, wash by centrifugation until neutral, and then perform stepwise ultrasonic treatment: First, perform preliminary exfoliation by ultrasonication for 20-40 minutes at 80-200W and an ice-water bath, and then perform deep stratification by ultrasonication for 30-60 minutes at 200-300W and 55-65℃. The ultrasonicated solution is then subjected to a 2000-3000... Centrifuge at low speed (rpm) for 20-30 minutes, and collect the supernatant rich in few-layer MXene; filter the supernatant under vacuum and dry it under vacuum at 50-60℃ for 12-24 hours to obtain few-layer MXene powder; set aside for later use. Step 2, Pretreatment of MAX-reinforced phase: Add an appropriate amount of anhydrous ethanol as a process control agent to the MAX phase powder in a planetary ball mill. The mass-volume ratio of MAX phase powder to anhydrous ethanol is 1:

2. Ball mill at 300-400 rpm for 10-20 hours under high-purity argon protection. The ball-to-material ratio is 8-10:1 to obtain flaky MAX phase powder. Step 3, melting and pulverization of Cu-Ti-Be-Co matrix alloy: Melting is carried out in a vacuum medium-frequency induction furnace at a melting temperature of 1450-1550℃, with electromagnetic stirring to ensure uniform composition; the uniform alloy liquid is further superheated to maintain a superheat of 100℃ above the liquidus line, and then the superheated alloy liquid is guided to flow out through a guide tube. At the nozzle of the guide tube, the superheated alloy liquid is broken into fine droplets by argon gas preheated at 40-50℃ and 3-5 MPa, and finally Cu-Ti-Be-Co alloy powder with a particle size range of 15-53 μm is obtained. Step 4, Construction and Interface Engineering of Composite Powder: The Cu-Ti-Be-Co alloy powder obtained in Step 3 and the few-layer MXene powder obtained in Step 1 are placed together in a ball mill jar. The amount of few-layer MXene powder added is 0.5~5.0 wt% of the total mass of Cu-Ti-Be-Co alloy powder. Anhydrous ethanol is used as the process control agent, and the mass-to-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol is 1:

2. High-energy ball milling is carried out under argon protection, with a ball-to-material ratio of 8-10:1, a ball milling speed of 250-350 rpm, and a ball milling time of 6-10 minutes. h, to obtain core-shell structure one; then, the lamellar MAX phase powder obtained in step two is blended with core-shell structure one, the amount of lamellar MAX phase powder added is 0.5-5.0 wt% of the total amount of Cu-Ti-Be-Co alloy powder, anhydrous ethanol is used as the process control agent, the mass-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol is 1:2, high-energy ball milling is carried out under argon protection, ball-to-material ratio is 8-10:1, ball milling speed is 250-350 rpm, ball milling time is 6-10 h, to obtain core-shell structure two; Step 5, densification sintering: The core-shell structure II is densified by spark plasma sintering (SPS). The sintering parameters are: temperature 600-900℃, pressure 20-50 MPa, vacuum degree less than 5 Pa, heating rate 100-200℃ / min, and holding time 5-15 minutes to obtain the sintered copper alloy. Step 6, Solution treatment + multi-stage aging treatment: First, the sintered copper alloy is subjected to solution treatment at a temperature of 800~900℃ for 0.5~2 hours, and the alloy is water-quenched to room temperature within 1 minute after solution treatment. Secondly, perform the first stage of aging: keep warm at 450-500℃ for 1-2 hours; Then, the second stage of aging is carried out: heat preservation at 380-420℃ for 2-4 hours.

5. The preparation method according to claim 4, characterized in that, In step one, the MXene precursor includes Ti3AlC2; the particle size of the MXene precursor ranges from 18 to 25 μm; after the treatment in step one, the lateral size of the MXene reinforcing phase is 1-5 μm and the thickness is 1-5 nm.

6. The preparation method according to claim 4, characterized in that, In step two, the MAX phase powder includes Ti2AlN; the original size of the MAX phase powder is in the micrometer range, and after the treatment in step two, the thickness of the MAX reinforcing phase is between 50-200 nm, and the lateral size is between 0.5-2 μm.

7. The preparation method according to claim 4, characterized in that, In step four, the following replacement scheme is adopted: Pretreatment: Place 50-100 g of Cu-Ti-Be-Co alloy powder obtained in step 3 into a tube furnace and heat treat it at 200-300℃ and a flow rate of 80-100 sccm for 20-30 minutes to form a 5-10 nm oxide layer on its surface, thus obtaining slightly oxidized alloy powder. 50-100 g of the slightly oxidized alloy powder was dispersed in 500 mL of a few-layer MXene aqueous solution with a concentration of 1-10 mg / mL prepared in step one, i.e., containing 0.5-5 g of MXene, to obtain a mixed system; then, the self-assembly process was initiated by ultrasound: the mixed system was placed in a CNC ultrasonic cleaner and ultrasonically dispersed for 10-30 minutes at a power range of 100-300 W and a temperature of 20-40°C. After ultrasonic pretreatment, the mixture is transferred to a mechanical stirrer and stirred continuously at 200-300 rpm for at least 12 hours to complete the self-assembly process. After drying, core-shell structure one is obtained. Then, the lamellar MAX phase powder obtained in step two is blended with core-shell structure one. The amount of lamellar MAX phase powder added is 0.5-5.0 wt% of the total Cu-Ti-Be-Co alloy powder. Anhydrous ethanol is used as the process control agent. The mass-volume ratio of Cu-Ti-Be-Co alloy powder to anhydrous ethanol is 1:

2. High-energy ball milling is carried out under argon protection with a ball-to-material ratio of 8-10:1, a ball milling speed of 250-350 rpm, and a ball milling time of 6-10 h to obtain core-shell structure two.

8. The preparation method according to claim 4, characterized in that, In step five, the following alternative is adopted: densification is carried out by hot isostatic pressing (HIP). The sintering process includes: inserting the core-shell structure II into a low-carbon steel sheath, evacuating and sealing it; placing the low-carbon steel sheath in a hot isostatic pressing furnace and holding it at a temperature range of 800~900℃ and an argon pressure of 100~200 MPa for 90~180 minutes.

9. The application of a material for an electromagnetic railgun guide according to any one of claims 1 to 3 in high-load electromagnetic railguns, characterized in that, High load is an impact of at least 3000N within 2.5 milliseconds.

10. An electromagnetic railgun, made from the material for an electromagnetic railgun guide rail as described in any one of claims 1 to 3.

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