High-corrosion-resistance coating material with high-entropy effect and amorphous effect and preparation method of high-corrosion-resistance coating material

Abstract

The invention discloses a high-corrosion-resistance coating material with a high-entropy effect and an amorphous effect and a preparation method of the high-corrosion-resistance coating material, and belongs to the technical field of surface engineering and functional materials. The high-entropy amorphous alloy powder comprises the following alloy raw materials: 21-22 wt% of Fe; % of Co: 22 to 25 wt. % of Cr: 19 to 20 wt.%; % of Mo: 18 to 19 wt.%; % of Ni: 11 to 12 wt.%; % of B: 1.5 to 3.0 wt.%; %, Si: 2.0 to 4.5 wt.%. According to the high-corrosion-resistance coating material with the high-entropy effect and the amorphous effect, the porosity of the coating material is 3.2% or below, the amorphous phase content is 85% or above, and the average microhardness reaches 1120-1180 HV 0.1. The coating provided by the invention shows lower corrosion current, wider passivation interval and higher hardness in a corrosive medium, and is suitable for long-term protection of ocean, aviation and energy equipment.

Description

Technical Field

[0001] This invention belongs to the field of surface engineering and functional materials technology, and relates to a high corrosion-resistant coating material with both high entropy effect and amorphous effect and its preparation method. Specifically, it relates to a high entropy amorphous alloy powder based on a multi-principal high entropy system and having an amorphous structure, and its preparation method for a high amorphous degree corrosion-resistant coating. It is applicable to the surface strengthening technology of key components in aerospace, marine equipment, energy and chemical industry and extreme corrosion and abrasion environments. Background Technology

[0002] Key components operating under extreme corrosion and abrasion conditions, such as compressor blades for aero-engines, propulsion mechanisms for marine equipment, and transmission components for new energy equipment, often face multiple coupled damages during service, including chloride corrosion, impact wear, and temperature fluctuations, which can easily lead to material performance degradation and structural failure. Therefore, developing surface engineering materials with high corrosion resistance, high stability, and high reliability has always been a key focus in materials research and engineering industries.

[0003] Currently, the most widely used high-performance coating systems mainly fall into two categories: high-entropy alloy coatings and amorphous alloy coatings. High-entropy alloys, due to their multi-principal element design strategy, possess structural and thermodynamic characteristics such as high mixing entropy, lattice distortion, slow diffusion, and the "cocktail effect," exhibiting high mechanical strength, good thermal stability, and phase stability. However, high-entropy alloy coatings are generally polycrystalline. When operating in marine environments or chlorinated media, grain boundaries, as sensitive areas for electrochemical corrosion, can accelerate localized corrosion, leading to problems such as pitting corrosion, intergranular corrosion, and stress corrosion cracking. Furthermore, high-entropy alloys often contain multiple active elements, making them prone to potential-driven localized corrosion in electrochemically corrosive environments, thus limiting their corrosion resistance.

[0004] In contrast, amorphous alloys, due to their absence of grain boundaries, dislocations, and isotropic short-range ordered structures, possess naturally high corrosion resistance; especially in chlorine-containing systems, amorphous alloys are better able to avoid grain boundary-induced corrosion. However, amorphous materials have two significant limitations: (1) they are prone to structural relaxation and crystallization under high-temperature conditions of thermal spraying, leading to a decline in their excellent performance; (2) they have insufficient thermal stability, and when the service temperature enters the region above the glass transition temperature, the internal structure rearranges, the corrosion resistance decreases rapidly, and the application range is limited.

[0005] Therefore, high entropy and amorphous materials each have their advantages, but they also have complementary shortcomings:

[0006] In recent years, high-entropy-amorphous composites have been considered an important direction for the development of high-temperature and corrosion-resistant materials. The high-entropy effect introduces the concept of multi-principal element design, suppressing crystal structure formation by increasing configurational entropy, making materials more prone to forming disordered short-range chemical structures, thus achieving a balance between high amorphousness and high thermal stability. When high-entropy design is applied to amorphous systems, it can effectively increase the glass transition temperature (Tg) and the width of the ultracold liquid phase region (ΔTx), reduce the tendency to crystallize, and maintain the structural homogeneity of the coating in the service environment. Simultaneously, specific elements in the high-entropy system, such as Cr, Mo, and Si, can accumulate in the passivation film, forming a denser and more resistant protective film, thereby significantly improving the pitting potential and passivation range stability. Furthermore, the synergistic effect of lattice distortion strengthening and disordered structure can improve the material's toughness and crack resistance, contributing to enhanced overall mechanical reliability of the coating. Therefore, the superposition of the high-entropy effect and the amorphous effect provides a potential pathway for constructing novel coating materials with excellent corrosion resistance and high-temperature service capabilities.

[0007] However, current research and technologies still face key limitations. Existing high-entropy amorphous powders generally experience partial degradation of their amorphous structure during thermal spraying, with crystalline phase precipitation weakening the material's original corrosion resistance. Simultaneously, due to the difficulty in completely avoiding high-speed particle impaction and re-oxidation, aggregated pores, unmelted particles, and electrochemically active defects easily form in the coating, often resulting in a gap between actual corrosion resistance and the material's design expectations. Furthermore, most studies have not systematically verified the stability of the passivation film under high-temperature corrosive environments, nor have they established a positive coupling mechanism between coating structure evolution and performance enhancement. Therefore, achieving a state where the amorphous structure not only does not degrade during deposition but is even further enhanced, and where the coating exhibits superior corrosion resistance compared to pure high-entropy or pure amorphous systems, remains a critical bottleneck that high-entropy amorphous coating technology urgently needs to overcome. Summary of the Invention

[0008] This invention provides a method for preparing high-entropy amorphous alloy powder and its plasma-sprayed coating. By introducing a multi-scale, controllable thermo-kinetic regulation strategy in alloy composition design, rapid powder solidification preparation, and spray deposition process, the powder-coating system achieves a structural transition from high amorphousness to even higher amorphousness, thereby significantly improving the mechanical properties, corrosion resistance, thermal stability, and density of the coating.

[0009] (I) Composition design and preparation process of high-entropy amorphous alloy powder In terms of alloy composition design, this invention uses Fe as the base element and introduces multi-principal alloying elements such as Co, Cr, Mo, Ni, and Si. By increasing the system configuration entropy and introducing significant atomic size mismatch and negative mixing enthalpy effects, the driving force for crystalline phase formation is reduced and long-range diffusion behavior is suppressed. Simultaneously, amorphous forming elements such as B are introduced to regulate the synergistic evolution of the chemically short-range ordered regions and the amorphous network structure in the alloy system, thereby significantly improving the glass-forming ability of the alloy. Through the above synergistic composition design, the alloy system achieves a higher glass transition temperature (Tg) and a wider ultracold liquid phase region (ΔTx), providing a stable thermodynamic basis for the maintenance and reformation of the amorphous structure during subsequent spraying.

[0010] A high-entropy amorphous alloy powder comprises the following components: Fe: 21-22 wt.%; Co: 22-25 wt.%; Cr: 19-20 wt.%; Mo: 18-19 wt.%; Ni: 11-12 wt.%; B: 1.5-3.0 wt.%; Si: 2.0-4.5 wt.%.

[0011] Preferably, a high-entropy amorphous alloy powder comprises the following components: Fe: 21.34 wt.%; Co: 22.59 wt.%; Cr: 19.91 wt.%; Mo: 18.28 wt.%; Ni: 11.17 wt.%; B: 2.44 wt.%; Si: 4.27 wt.%.

[0012] Preferably, a high-entropy amorphous alloy powder comprises the following components: Fe: 21 wt.%; Co: 25 wt.%; Cr: 19 wt.%; Mo: 18 wt.%; Ni: 11 wt.%; B: 1.5 wt.%; Si: 4.5 wt.%.

[0013] Preferably, a high-entropy amorphous alloy powder comprises the following components: Fe: 22 wt.%; Co: 22 wt.%; Cr: 20 wt.%; Mo: 19 wt.%; Ni: 12 wt.%; B: 3.0 wt.%; Si: 2.0 wt.%.

[0014] In the powder preparation stage, this invention employs vacuum inert gas atomization technology to prepare high-entropy amorphous alloy powder. The process steps include: firstly, placing the alloy raw materials prepared according to the designed ratio into a vacuum induction melting furnace for melting, with the melting temperature of the vacuum induction melting furnace controlled at 1350-1550℃ and the vacuum degree inside the furnace controlled at 10... -3 -10 -4Within the range of Pa, a high-purity inert gas (including one or more of argon (Ar), helium (He), and nitrogen (N2), preferably high-purity argon; all with a purity >99%) is then introduced as a protective atmosphere to fully homogenize the alloy melt. The melt is then introduced into the atomization zone through a ceramic guide tube, and high-purity inert gas at a pressure of 3-6 MPa is used to perform high-speed impact atomization, causing the melt to break into tiny droplets in a very short time. The atomized droplets undergo ultra-fast cooling during flight, with a cooling rate reaching approximately 10⁻⁶ MPa. 5 -10 6 K / s is significantly higher than that of traditional casting and conventional gas atomization processes, thus effectively suppressing crystal nucleation and long-range diffusion behavior, allowing the powder to solidify in an amorphous or quasi-amorphous structure.

[0015] The high-entropy amorphous alloy powder prepared by the above-mentioned vacuum inert gas atomization technology exhibits high sphericity, narrow particle size distribution, and a uniform and dense internal structure. Characterization by X-ray diffraction (XRD) and transmission electron microscopy (TEM) revealed that the powder exhibits typical broad-dispersed amorphous diffraction peaks, with no obvious crystalline diffraction peaks observed. Its amorphous phase content can stably reach over 75%, and in some embodiments, the amorphism is not less than 78%, demonstrating typical broad-dispersed amorphous diffraction peak characteristics without obvious crystalline diffraction peaks. Figure 1 As shown.

[0016] (II) Plasma spraying and multi-stage thermo-kinetic control process for high-entropy amorphous coatings After the high-entropy amorphous alloy powder is prepared, the present invention further achieves the maintenance, reconstruction and densification control of the amorphous structure of the powder during the deposition process through a controlled plasma spraying deposition process, thereby obtaining a high-entropy-amorphous composite coating with high amorphous content, low porosity and continuous and uniform structure.

[0017] Specifically, this invention uses the aforementioned multi-primary-element high-entropy amorphous alloy powder as the spraying material and performs plasma spraying deposition under an Ar-N2 mixed protective atmosphere. By synergistically controlling the parameters of the main gas, auxiliary gas, and carrier gas, a deposition environment with high enthalpy, high velocity, and rapid heat dissipation is constructed. Specifically, the pressure of the main gas Ar is controlled at approximately 45-55 psi, the pressure of the auxiliary gas N2 is approximately 60-70 psi, the pressure of the carrier gas N2 is approximately 55-70 psi, the spraying current is 620-680 A, and the spraying distance is controlled at 100-120 mm, thereby ensuring that the powder achieves sufficient heating in a short time without overheating during flight.

[0018] During the spraying process, the present invention further actively controls the temperature of the substrate (the substrate is the base material, including metal substrates and alloy substrates, which are selected from at least one or more of carbon steel, stainless steel, and low alloy structural steel (specific grades such as Q235 steel, Q345 steel, and 45# steel)) to maintain it within the range of 200-350 ℃, so as to suppress the excessive crystallization of droplets or prolonged heat exposure during the deposition stage, thereby reducing the driving force for the transformation of amorphous phase to crystalline phase from the process level.

[0019] Under the aforementioned parameter window, high-entropy amorphous powders undergo a typical thermal history of instantaneous remelting, high-speed impact, and rapid cooling in plasma jets. By controlling the powder's heating time and deposition cooling conditions, molten or semi-molten powders can undergo secondary rapid solidification on the substrate surface. The cooling rate can reach the same order of magnitude as the rapid solidification conditions in the powder preparation stage, thereby effectively promoting the refreezing and reformation of amorphous structures, increasing the overall amorphous phase ratio of the coating, and significantly reducing the formation of crystalline phases.

[0020] Furthermore, by precisely controlling the spray gun scanning method, this invention maintains the overlap rate of the spray gun scanning trajectory within the range of 40%-60%. While ensuring the stability of the single-pass deposition energy density, it achieves sufficient overlap and balanced heat input between adjacent deposition layers, avoiding the formation of local overheating or undermelting areas, thereby promoting the continuous formation and overall densification of the coating.

[0021] Under the synergistic regulation of the aforementioned multiple parameters, a multi-principal element solid solution structure dominated by amorphous phases gradually forms inside the deposition layer. The elements in the coating are uniformly distributed, with only short-range ordered structures or dispersed ordered clusters at the nanoscale, without the formation of continuous grain boundaries or macroscopic grain phases. The porosity of the resulting coating can be controlled below 3.2%, and the amorphous phase content is stably maintained above 85%, exhibiting an overall dense structure, good interlayer bonding, and no obvious interlayer defects.

[0022] Through the above-mentioned plasma spraying deposition and structure control strategy, this invention not only effectively avoids the problem of irreversible decrease in amorphousness during the traditional thermal spraying process, but also achieves the coexistence of maintaining and reconstructing the amorphous structure during the deposition process, laying a key process foundation for obtaining high-entropy amorphous coatings with high bonding strength, high structural stability and excellent service performance.

[0023] Specifically, a method for preparing a high-entropy-amorphous composite coating (i.e., a high-corrosion-resistant coating material that combines high-entropy and amorphous effects) includes the following steps: (a) High-entropy amorphous alloy powder was prepared by rapid solidification of Fe-Cr-Mo-WBC-Si and other multi-principal element systems through gas atomization. The powder particle size distribution was 35-80 μm, and in particular, d10=39.05 μm, d50=50.51 μm, and d90=60.88 μm.

[0024] (b) The high-entropy amorphous powder is used as a spraying material and plasma spraying is performed in an Ar-N2 atmosphere. The spraying parameters include: the main gas Ar pressure is about 45-55 psi, the auxiliary gas N2 pressure is about 60-70 psi, the carrier gas N2 pressure is about 55-70 psi, the spraying current is 620-680 A, and the spraying distance is 100-120 mm.

[0025] (c) During the spraying process, by segmented energy input control and transient thermal history regulation, the high-entropy amorphous powder undergoes a short-term melting-limited overheating-rapid cooling process during flight and deposition. Specifically, the energy input is divided into three stages, and transient thermal history regulation is achieved through a pulsed power output and infrared temperature measurement real-time feedback control system. In the first stage, the energy input power is 20-30kW, which enables the powder to quickly reach a molten state. In the second stage, the energy input power is 35-45kW, combined with an intermittent energy gap of 0.2-0.5ms and a cooling gas (i.e., carrier gas N2) flow rate of 20-30L / min, to achieve limited overheating of 10-50℃. In the third stage, the energy input power is reduced to 0-10kW and the cooling gas flow rate is increased to 40-50L / min, to achieve millisecond-level rapid cooling (transient switching time of each stage <1ms, total transient thermal history period 4-10ms), which promotes the secondary resolidification behavior of powder droplets at the deposition interface, thereby inhibiting crystal nucleus growth and increasing the proportion of amorphous phase in the coating to more than 85%.

[0026] In this invention, the main gas Ar is used to maintain the stability of the plasma arc and provide the basic enthalpy; the auxiliary gas N2 is used to increase the enthalpy and flight speed of the plasma jet to ensure the full melting of the powder; and the carrier gas N2 is used to carry the powder and serve as the main cooling medium, and the thermal history of the powder particles is finely adjusted through transient flow rate control.

[0027] The pulsed power output is provided by a high-response power supply system with a power switching response time of less than 0.5 ms; the infrared temperature measurement real-time feedback control system monitors the temperature of powder particles online and dynamically adjusts the power output and cooling gas flow rate at each stage based on the temperature measurement results.

[0028] The three-stage division is based on the total transient thermal history cycle: The first stage (rapid melting stage) lasts for approximately 30%-50% of the total cycle, or 2-4 ms. The second stage (limited overheating stage) lasts approximately 20%-40% of the total cycle, or 1-3 ms. The third stage (rapid cooling stage) lasts approximately 20%-40% of the total cycle, or 1-3 ms.

[0029] (d) The deposition process is controlled by a reciprocating linear spray gun scanning strategy. Specifically, the spray gun moves at a speed of 0.2-0.5 m / s, with a scanning step of 3-5 mm and a powder feed rate of 30-50 g / min per unit time. Within each total transient thermal history cycle, the energy input is carried out in a reciprocating linear scan according to the above three stages. The overlap rate of adjacent scan tracks is 40-60%, and the energy superposition is 20-30%. This adjusts the single-track deposition width to 6-12 mm, controls the heat input distribution uniformity to >90%, and forms a periodic hot-cold alternation field in the deposition process to weaken the heat accumulation effect and control the substrate temperature within 200-350 ℃. (e) By coordinating and matching the spray gun movement speed, scanning step distance, and powder feed rate per unit time, the deposition energy density is precisely controlled to 30-55 J / mm². 2 Within the window range, the single-layer deposition process can ensure full spreading while avoiding prolonged high-temperature retention, thereby forming a continuous and dense multi-principal element solid solution-amorphous composite structure in the coating. (f) Through the synergistic control of the above processes, a high-entropy-amorphous composite coating with high amorphous phase content (above 85%), uniform structure, high interfacial bonding strength and suppressed crystallization is obtained.

[0030] Preferably, the substrate temperature is controlled at 200-350°C during the spraying step to suppress crystallization during the deposition process.

[0031] Preferably, the overlap rate of the spray gun scanning trajectory is controlled at 40%-60% to achieve continuous forming and densification of the coating.

[0032] Preferably, the porosity of the coating is less than 3.2%, and the amorphous phase content is greater than 85%.

[0033] Preferably, the coating obtained by spraying forms a short-range ordered structure of multiple metals with uniform element distribution and no obvious grain precipitation or crystallization region.

[0034] Preferably, the cooling rate during rapid solidification powdering is 10. 5 -10 6 K / s enables the powder to obtain a stable amorphous structure during the solidification stage.

[0035] Preferably, the coating is predominantly amorphous, with an amorphous phase content of ≥85%. It allows for the presence of ≤5% (volume fraction) of dispersed nanoscale ordered clusters or discontinuous nanocrystals, but the coating does not contain continuous grain boundaries or macroscopic grain phases, exhibiting an overall dense, continuous structure without obvious interlayer defects. The coating has a uniform overall thickness, ranging from approximately 350 to 400 μm.

[0036] The present invention relates to the application of a high-entropy amorphous alloy powder in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0037] The present invention provides the application of a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components of new energy equipment.

[0038] The present invention provides a high-entropy amorphous alloy powder with an amorphous phase content that can stably reach over 75%.

[0039] This invention provides a highly corrosion-resistant coating material that combines high entropy and amorphous effects. The coating porosity can be controlled below 3.2%, and the amorphous phase content is stably maintained above 85%. The overall structure exhibits dense microstructure, good interlayer bonding, and no obvious interlayer defects. The average microhardness reaches 1120-1180 HV. 0.1 .

[0040] The present invention has the following beneficial effects: This invention discloses a high-entropy amorphous alloy powder, a highly corrosion-resistant coating material exhibiting both high-entropy and amorphous effects, and its preparation method, belonging to the technical fields of surface engineering and corrosion-resistant protective materials. The powder is based on a multi-principal component design, using Fe-Co-Cr-Mo-Ni as the matrix and introducing non-metallic elements such as B and Si. Through the synergistic regulation of atomic radius mismatch, negative mixing enthalpy, and high mixing entropy, the glass-forming ability and structural metastability of the system are improved. The powder is prepared using vacuum induction atomization at 10... 5 -10 6 High-sphericity, high-flowability, and high-amorphous-content metallic glass powder is obtained under rapid quenching conditions at K / s. The coating is deposited via plasma spraying, utilizing optimized gas pressure, current, and spray distance to induce short-time remelting and rapid solidification of the powder during deposition. This achieves efficient transfer of the powder to the coating's amorphous structure, maintaining or even enhancing its amorphousness. The resulting coating structure is dense and uniform, without significant crystallization or defects, combining the low-diffusion characteristics of a high-entropy system with the grain-boundary-free features of an amorphous structure. The coating of this invention exhibits lower corrosion current, a wider passivation range, and higher hardness in corrosive media. Compared to traditional high-entropy coatings and single-metal glass coatings, it possesses superior corrosion resistance and service reliability, making it suitable for long-term protection of marine, aerospace, and energy equipment. Attached Figure Description

[0041] Figure 1The images show the SEM morphology, XRD pattern, TEM morphology and corresponding SAED image of the high-entropy amorphous alloy powder of the present invention, wherein (a) is the SEM morphology, (b) is the XRD pattern, (c) is the TEM morphology and (d) is the SAED image. Figure 2 The cross-sectional morphology and XRD pattern of the high-entropy amorphous alloy coating of the present invention are shown, wherein (a) is the cross-sectional morphology and (b) is the XRD pattern; Figure 3 The results show the comparison of the potentiodynamic polarization curves of the high-entropy amorphous alloy coating of the present invention with those of a pure amorphous coating and a pure high-entropy alloy coating with similar composition systems in a 3.5 wt.% NaCl solution. Figure 4 The XPS analysis results and AFM surface morphology of the passivation film on the surface of the high-entropy amorphous alloy coating of the present invention are shown; wherein, (a) and (b) are XPS analysis images, and (c) is an AFM surface morphology image. Detailed Implementation

[0042] 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

[0043] A method for preparing a high-entropy amorphous alloy powder pair includes the following steps: Step one: Place the alloy raw materials prepared according to the design ratio into a vacuum induction melting furnace for melting, and control the vacuum degree inside the furnace at 10. -3 -10 -4 Within the Pa range, a high-purity inert gas is then introduced as a protective atmosphere to fully homogenize the alloy melt. Step two involves introducing the molten alloy into the atomization zone through a ceramic guide tube. High-purity inert gas at a pressure of 5 MPa is then used to impact and atomize the molten alloy, breaking it into tiny droplets. These atomized droplets undergo ultra-rapid cooling during flight, with a cooling rate reaching 10⁻⁶. 5 -10 6 K / s, ultimately yielding high-entropy amorphous alloy powder with an amorphous phase content of over 75%.

[0044] A method for preparing a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect includes the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 50 psi, the auxiliary gas N2 pressure was 60 psi, the carrier gas N2 pressure was 60 psi, the spraying current was 640 A, and the spraying distance was 110 mm. During the spraying process, energy input is divided into three stages: The first stage, the rapid melting stage, involves an energy input of 25kW and lasts for 3ms. The second stage, namely the restricted overheating stage, involves an energy input power of 40kW combined with an intermittent energy gap of 0.4ms and a cooling gas flow rate of 25L / min to achieve restricted overheating of 30℃. This stage lasts for 2ms. The third stage, the rapid cooling stage, involves reducing the energy input power to 5kW and increasing the cooling gas flow rate to 45L / min to achieve millisecond-level rapid cooling. This stage lasts for 2ms. Transient switching time for each stage is less than 1ms, and the total transient thermal history period is 7ms. The deposition process was controlled by a reciprocating linear spray gun scanning strategy. The spray gun moved at a speed of 0.3 m / s, a scanning step of 4 mm, a powder feed rate of 40 g / min per unit time, and performed reciprocating linear scanning according to the above three-stage energy input in each total transient thermal history cycle. The overlap rate of adjacent scanning tracks was 50%, and the energy superposition was 25%, thereby adjusting the single-track deposition width to 9 mm and controlling the heat input distribution uniformity to >90%. During the spray gun scanning process, the substrate temperature was controlled at around 280℃.

[0045] This embodiment describes the application of a high-entropy amorphous alloy powder in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0046] This embodiment describes the application of a highly corrosion-resistant coating material that combines high entropy and amorphous effects in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment. Implementation effect verification

[0047] Through the composition design, rapid solidification powder preparation and plasma spraying deposition process of the above-mentioned multi-principal element high-entropy amorphous alloy composition system (see Table 1 below), this invention constructs a material system with synergistic effects of high entropy, amorphous effect and rapid solidification kinetics, and realizes the stable evolution of powder-coating structure from high amorphousness to even higher amorphousness.

[0048] Table 1. Composition of high-entropy amorphous alloys

[0049] Calculation and evaluation results show that, based on the aforementioned composition system, the atomic radius mismatch parameter δ of this alloy is 14.29, the enthalpy of mixing ΔHmix is ​​-23.06 kJ / mol, and the entropy of mixing ΔSmix reaches 15.66 J·K.-1 ·mol -1 All values ​​fall within the preferred range for typical high-entropy amorphous materials. Thermal analysis results show that its glass transition temperature Tg and crystallization temperature Tx are 904 K and 938 K, respectively, and the ultracold liquid region ΔTx is 34 K. This demonstrates that the system can maintain a stable amorphous state under heating cycles, remelting, and rapid solidification environments, providing a reliable thermodynamic basis for the retention and recombination of amorphous materials during coating deposition.

[0050] In the powder preparation stage, vacuum induction gas atomization technology provides 10 5 ~10 6 The rapid solidification environment at K / s enables the powder to achieve high sphericity and a narrow particle size distribution (d10 = 39.05 μm, d50 = 50.51 μm, d90 = 60.88 μm), thereby ensuring good flowability and uniform energy absorption during the spraying process. Benefiting from the low diffusivity and short-range ordered structure strengthening effect of the high-entropy system, a dense and stable amorphous network forms within the powder, making high amorphousness the structural basis for subsequent coating formation.

[0051] During the coating formation process, this invention utilizes an optimized combination of the pressures of the main gas (Ar), auxiliary gas (N2), and carrier gas (N2), as well as the spraying current and distance (central parameters: main gas 50 psi, auxiliary gas 60 psi, carrier gas 60 psi, current 640 A, distance 110 mm) to construct a deposition field with high enthalpy, high velocity, and high cooling rate. This induces the powder droplets to undergo brief remelting during their flight phase and achieve secondary rapid solidification on the substrate surface. The high entropy effect of the multi-principal system increases the resistance to nucleation, while non-metallic elements such as B and Si enhance the stability of the amorphous framework. This not only maintains the amorphous phase content of the coating but also exhibits "higher amorphousness than the powder" in some regions, such as... Figure 2 As shown in the figure. This result breaks through the inherent limitation of "the amorphousness of the coating will inevitably decrease" in the traditional thermal spraying system, indicating that the present invention realizes the refreezing and structural reconstruction of amorphous structures during the spraying process.

[0052] In terms of mechanical properties, the coating of this invention exhibits high hardness and good resistance to local deformation under the combined effect of high-entropy solid solution strengthening, lattice distortion energy gain, and amorphous disordered structure, with an average microhardness of up to 1180 HV. 0.1 The strength is significantly higher than that of high-entropy alloys in similar systems. The amorphous phase provides uniform strength output, while the high-entropy phase stabilizes the high-bonding-energy structure, enabling the coating to resist the initiation of microcracks caused by residual stress during spraying and improving the high brittleness characteristics of pure amorphous coatings. In addition, due to the low diffusion characteristics that inhibit crystallization and element migration, the coating maintains a highly homogeneous structural distribution, which is beneficial to improving impact resistance and durability.

[0053] Regarding corrosion resistance, electrochemical analysis of the coating of this invention in 3.5 wt.% NaCl solution showed that the corrosion current density was significantly lower than that of the pure high-entropy and pure amorphous control systems. The corrosion current of conventional high-entropy coatings is approximately 6 μA / cm. 2 Limited passivation capability; corrosion current of amorphous coatings can be reduced to 3 μA / cm. 2 However, the passivation potential is low, resulting in insufficient stability of the passivation region. The coating of this invention exhibits even lower corrosion current density (as low as 3 μA / cm²) in testing. 2 It also features significantly improved passivation region width and higher passivation film stability, such as... Figure 3 As shown. Its mechanism mainly includes: (1) The selective enrichment of Cr and Mo elements promotes the formation of a dense passivation film, enhancing the resistance to pitting corrosion (e.g. Figure 4 (as shown); (2) Amorphous structures lack rapid corrosion paths such as grain boundaries and sub-grain facets; (3) The low diffusivity of high-entropy solid solutions inhibits the dissolution rate of cations, reducing the probability of passivation film rupture. The chemical complexity provided by the high-entropy effect and the dense disordered structure brought about by the amorphous effect work together to enable the coating to achieve synergistic passivation capabilities superior to a single system.

[0054] Figure 1 This document presents the SEM morphology, XRD pattern, TEM morphology, and corresponding SAED image of the high-entropy amorphous alloy powder described in this embodiment. The SEM morphology shows that the prepared powder exhibits good sphericity, uniform particle size distribution, and a smooth surface, demonstrating good flowability and sprayability. The XRD pattern shows a distinct, broad, diffuse peak in the shape of a steamed bun near 2θ≈45°, with no sharp crystalline diffraction peaks observed, indicating that the powder possesses typical amorphous structural characteristics. The TEM morphology reveals the absence of regular lattice fringes within the powder, and the corresponding SAED image shows diffuse halo characteristics, further confirming that the prepared powder has an amorphous structure and lacks long-range ordered crystalline atomic arrangement.

[0055] Figure 2 This document presents the cross-sectional morphology and structural characterization results of the high-entropy amorphous alloy coating prepared by plasma spraying of the high-entropy amorphous alloy powder in this embodiment. The coating cross-section shows a dense structure with good interlayer bonding, a porosity of less than 3%, and a uniform overall thickness of approximately 380 μm. The XRD pattern of the coating also exhibits a broad, diffuse amorphous peak near 2θ≈45°, and its dispersion characteristics are more pronounced than those of the powder, indicating that the amorphous structure of the coating was effectively maintained during the spraying deposition process, and even further enhanced in local areas, demonstrating significant amorphous structural characteristics.

[0056] Figure 3The results show a comparison of the potentiodynamic polarization curves of the high-entropy amorphous alloy coating described in this embodiment with those of a pure amorphous coating and a pure high-entropy alloy coating with similar composition systems in a 3.5 wt.% NaCl solution. It can be seen that the high-entropy amorphous alloy coating of this invention exhibits the lowest corrosion current density, indicating that its corrosion rate is significantly lower than that of the control coating system. Simultaneously, the initial passivation potential of this coating is significantly lower than that of the pure high-entropy alloy coating, while its overpassivation potential is comparable to that of the pure amorphous coating, thus forming a wider effective passivation range and exhibiting superior and more stable passivation behavior. In contrast, the passivation ability of ordinary high-entropy alloy coatings is relatively weak.

[0057] Figure 4 The XPS analysis results (a, b) and AFM surface morphology (c) of the passivation film on the surface of the high-entropy amorphous alloy coating described in this embodiment are shown. XPS analysis results indicate that the passivation film on the coating surface is rich in stable passivation products such as Cr2O3 and high-valence Mo oxides, which are beneficial to improving the chemical stability and protective ability of the coating in corrosive environments. AFM surface morphology shows that the coating surface exhibits a densely distributed fine needle-like structure with minimal overall surface undulation, indicating that the passivation film structure is dense and continuous, which helps to further inhibit the penetration of corrosive media.

[0058] In summary, this invention, through a technical route of composition design, rapid solidification, high-enthalpy deposition, and secondary resolidification, maintains high amorphous stability in the material system during both the powder and coating stages, and achieves further structural optimization. Through a synergistic mechanism of multi-element coupling, low-diffusion strengthening, and short-range ordering, the coating exhibits stronger resistance to dissolution and passivation film integrity in corrosive media. In terms of mechanical properties, it demonstrates significant solid solution strengthening and high reliability. This system overcomes the limitations of unavoidable crystallization and porosity in traditional amorphous coating thermal spraying, and also overcomes the weakness of insufficient stability in conventional high-entropy alloy passivation films, establishing an advanced protective coating material that combines high amorphousness, high density, and long-term service stability.

[0059] As demonstrated by the above performance verifications, the material system of this invention outperforms simple high-entropy or traditional metallic glass materials in both hardness and corrosion resistance. The high-entropy effect provides solute dragging and phase stabilization capabilities, while the amorphous effect eliminates stress concentration sources such as dislocations and grain boundaries. These two factors synergistically produce a significant improvement in structural stability, environmental tolerance, and mechanical toughness. This strengthening mechanism not only improves the service life of the coating but also expands its application prospects in marine structures, gas turbine components, and equipment used in extremely corrosive environments, demonstrating outstanding practical value.

[0060] Example 2 A high-entropy amorphous alloy powder, characterized in that it comprises the following alloy raw materials: Fe: 21 wt.%; Co: 25 wt.%; Cr: 19 wt.%; Mo: 18 wt.%; Ni: 11 wt.%; B: 1.5 wt.%; Si: 4.5 wt.%.

[0061] A method for preparing a high-entropy amorphous alloy powder pair includes the following steps: Step one: Place the alloy raw materials prepared according to the design ratio into a vacuum induction melting furnace for melting, and control the vacuum degree inside the furnace at 10. -3 -10 -4 Within the Pa range, a high-purity inert gas is then introduced as a protective atmosphere to fully homogenize the alloy melt. Step two involves introducing the molten alloy into the atomization zone through a ceramic guide tube. High-purity inert gas at a pressure of 3 MPa is then used to impact and atomize the molten alloy, breaking it into tiny droplets. These atomized droplets undergo ultra-rapid cooling during flight, with a cooling rate reaching 10⁻⁶. 5 -10 6 K / s, ultimately yielding high-entropy amorphous alloy powder with an amorphous phase content of over 75%.

[0062] This embodiment provides a high-corrosion-resistant coating material for a high-entropy amorphous alloy powder that combines both high-entropy and amorphous effects. The coating material is characterized by a porosity below 3.2%, an amorphous phase content above 85%, uniform overall coating thickness of approximately 350 μm, and an average microhardness of 1120 HV. 0.1 .

[0063] A method for preparing a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect includes the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 45 psi, the auxiliary gas N2 pressure was 65 psi, the carrier gas N2 pressure was 55 psi, the spraying current was 620 A, and the spraying distance was 100 mm. During the spraying process, energy input is divided into three stages: The first stage, the rapid melting stage, involves an energy input of 20kW and lasts for 2ms. The second stage, namely the limited overheating stage, involves an energy input power of 3kW combined with an intermittent energy gap of 0.2ms and a cooling gas flow rate of 20L / min to achieve limited overheating of 10℃. This stage lasts for 1ms. The third stage, the rapid cooling stage, involves reducing the energy input power to 0kW and increasing the cooling gas flow rate to 40L / min to achieve millisecond-level rapid cooling. This stage lasts for 1ms. Transient switching time for each stage is less than 1ms, and the total transient thermal history period is 4ms. A reciprocating linear spray gun scanning strategy was employed to control the deposition process. The spray gun moved at a speed of 0.2 m / s, with a scanning step size of 3 mm, a powder feed rate of 30 g / min, and performed reciprocating linear scanning according to the three-stage energy input described above within each total transient thermal history cycle. The overlap rate of adjacent scanning trajectories was 40%, and the energy superposition was 20%, thereby adjusting the single-pass deposition width to 6 mm and controlling the heat input distribution uniformity to >90%. During the spray gun scanning process, the substrate temperature was controlled at approximately 200℃.

[0064] This embodiment describes the application of a high-entropy amorphous alloy powder in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0065] This embodiment describes the application of a highly corrosion-resistant coating material that combines high entropy and amorphous effects in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0066] Example 3 A high-entropy amorphous alloy powder, characterized in that it comprises the following alloy raw materials: Fe: 22 wt.%; Co: 22 wt.%; Cr: 20 wt.%; Mo: 19 wt.%; Ni: 12 wt.%; B: 3.0 wt.%; Si: 2.0 wt.%.

[0067] A method for preparing a high-entropy amorphous alloy powder pair includes the following steps: Step one: Place the alloy raw materials prepared according to the design ratio into a vacuum induction melting furnace for melting, and control the vacuum degree inside the furnace at 10. -3 -10 -4 Within the Pa range, a high-purity inert gas is then introduced as a protective atmosphere to fully homogenize the alloy melt. Step two involves introducing the molten alloy into the atomization zone through a ceramic guide tube. High-purity inert gas at a pressure of 6 MPa is then used to impact and atomize the molten alloy, breaking it into tiny droplets. These atomized droplets undergo ultra-rapid cooling during flight, with a cooling rate reaching 10⁻⁶. 5 -10 6K / s, ultimately yielding high-entropy amorphous alloy powder with an amorphous phase content of over 75%.

[0068] This embodiment yields a highly corrosion-resistant coating material that combines high entropy and amorphous effects. The coating material has a porosity of less than 3.2%, an amorphous phase content of more than 85%, uniform overall thickness of approximately 400 μm, and an average microhardness of 1150 HV. 0.1 .

[0069] A method for preparing a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect includes the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 55 psi, the auxiliary gas N2 pressure was 70 psi, the carrier gas N2 pressure was 70 psi, the spraying current was 680 A, and the spraying distance was 120 mm. During the spraying process, energy input is divided into three stages: The first stage, the rapid melting stage, has an energy input power of 30kW and lasts for 4 ms. The second stage, namely the limited overheating stage, involves an energy input power of 45kW, combined with an intermittent energy gap of 0.5ms and a cooling gas flow rate of 30L / min, to achieve limited overheating of 50℃. This stage lasts for 3ms. The third stage, the rapid cooling stage, involves reducing the energy input power to 10kW and increasing the cooling gas flow rate to 50L / min to achieve millisecond-level rapid cooling. This stage lasts for 3 ms. Transient switching time for each stage is less than 1ms, and the total transient thermal history period is 10ms. A reciprocating linear spray gun scanning strategy was employed to control the deposition process. The spray gun moved at a speed of 0.5 m / s, with a scanning step size of 5 mm, a powder feed rate of 50 g / min, and performed reciprocating linear scanning according to the three-stage energy input described above within each total transient thermal history cycle. The overlap rate of adjacent scanning trajectories was 60%, and the energy superposition was 30%, thereby adjusting the single-pass deposition width to 12 mm and controlling the heat input distribution uniformity to >90%. During the spray gun scanning process, the substrate temperature was controlled at approximately 350℃.

[0070] This embodiment describes the application of a high-entropy amorphous alloy powder in key components operating under extreme corrosion and abrasion conditions. These key components include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0071] This embodiment describes the application of a highly corrosion-resistant coating material that combines high entropy and amorphous effects in key components operating under extreme corrosion and abrasion conditions. The key components operating under extreme corrosion and abrasion conditions include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

[0072] Example 4 The only difference between this embodiment and Embodiment 1 is that: A high-entropy amorphous alloy powder comprises the following components: Fe: 21.5 wt.%; Co: 23 wt.%; Cr: 20 wt.%; Mo: 18.5 wt.%; Ni: 11.5 wt.%; B: 2.0 wt.%; Si: 3.5 wt.%.

[0073] Example 5 The only difference between this embodiment and Embodiment 1 is that: A high-entropy amorphous alloy powder comprises the following components: Fe: 21 wt.%; Co: 24 wt.%; Cr: 19.5 wt.%; Mo: 18.5 wt.%; Ni: 11.5 wt.%; B: 2.5 wt.%; Si: 3.0 wt.%.

[0074] Example 6 The only difference between this embodiment and Embodiment 1 is that: A method for preparing a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect includes the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 48 psi, the auxiliary gas N2 pressure was 65 psi, the carrier gas N2 pressure was 65 psi, the spraying current was 660 A, and the spraying distance was 105 mm; the rest were the same as in Example 1.

[0075] Example 7 The only difference between this embodiment and Embodiment 1 is that: A method for preparing a highly corrosion-resistant coating material that combines high entropy effect and amorphous effect, characterized by comprising the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 52 psi, the auxiliary gas N2 pressure was 68 psi, the carrier gas N2 pressure was 62 psi, the spraying current was 650 A, and the spraying distance was 115 mm; the rest were the same as in Example 1.

[0076] Comparative Example 1 The only difference between this comparative example and Example 1 is that: The spray gun performs a reciprocating linear scan with an energy input of 30kW, instead of the three-stage energy input of Example 1.

[0077] The porosity of the coating material obtained in this comparative example is 6.5%, which is significantly higher than that of the embodiments in this application. Due to the uncontrollable thermal history of the deposition process, local crystallization behavior occurs in the coating, reducing the amorphous phase content to 65%, and the average microhardness reaches 820 HV. 0.1 .

[0078] Comparative Example 2 The only difference between this comparative example and Example 1 is that: During the spraying process, the energy input of the spray gun is divided into two stages, instead of the three-stage energy input of Example 1.

[0079] Specifically, the energy input during the spraying process is divided into two stages: The first stage, the rapid melting stage, involves an energy input of 25kW and lasts for 3ms. The second stage, namely the restricted overheating stage, involves an energy input power of 40kW combined with an intermittent energy gap of 0.4ms and a cooling gas flow rate of 25L / min to achieve restricted overheating of 30℃. This stage lasts for 2ms. The transient switching time for each stage is less than 1ms, and the total transient thermal history period is 5ms.

[0080] The coating material obtained in this comparative example has a porosity of 5.0%, an amorphous phase content of 72%, and an average microhardness of 900 HV. 0.1 .

[0081] Under the above conditions, due to the lack of a subsequent rapid cooling stage, the cooling rate of the powder droplets at the deposition interface is insufficient, resulting in localized crystal growth and crystallization, which leads to the deterioration of the coating structure and performance.

[0082] Comparative Example 3 The only difference between this comparative example and Example 1 is that: During the spraying process, the energy input of the spray gun is divided into two stages, instead of the three-stage energy input of Example 1.

[0083] Specifically, the energy input during the spraying process is divided into two stages: The first stage, the rapid melting stage, involves an energy input of 25kW and lasts for 3ms. The second stage, the rapid cooling stage, involves reducing the energy input power to 5kW and increasing the cooling gas flow rate to 45L / min to achieve millisecond-level rapid cooling. This stage lasts for 2ms. The transient switching time for each stage is less than 1ms, and the total transient thermal history period is 5ms.

[0084] The coating material obtained in this comparative example has a porosity of 5.5%, an amorphous phase content of 70%, and an average microhardness of 850 HV. 0.1 .

[0085] Under the above conditions, due to the lack of stable control over the thermal state of the molten droplets during the restricted overheating stage, the powder droplets exhibit localized incomplete melting during flight and deposition, resulting in insufficient interlayer bonding and increased porosity defects.

[0086] In the foregoing description of exemplary embodiments of the invention, various features of the invention are sometimes grouped together in a single embodiment, figure, or description thereof. However, this disclosure should not be construed as reflecting an intention that the claimed invention requires more features than expressly recited in each claim. Rather, as reflected in the claims, the inventive aspect lies in fewer than all 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.

[0087] 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.

[0088] 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 high-entropy amorphous alloy powder, characterized in that, The alloying raw materials include: Fe: 21-22 wt.%; Co: 22-25wt.%; Cr: 19-20 wt.%; Mo: 18-19 wt.%; Ni: 11-12 wt.%; B: 1.5-3.0 wt.%; Si: 2.0-4.5wt.%.

2. The method for preparing a high-entropy amorphous alloy powder pair according to claim 1, characterized in that, Includes the following steps: Step one, the alloy raw materials prepared according to the design proportion are placed in a vacuum induction melting furnace for melting, the vacuum degree in the furnace is controlled at 10 -3 -10 -4 Pa, then high-purity inert gas is introduced as a protective atmosphere to make the alloy melt fully homogenized; Step two, then the alloy melt is introduced into the atomization zone through a ceramic nozzle, and the alloy melt is impacted and atomized by high-purity inert gas with a pressure of 3-6 MPa, so that the alloy melt is broken into small droplets; the droplets formed by atomization undergo ultrafast cooling in the flight process, and the cooling rate can reach 10 5 -10 6 K / s, and finally high-entropy amorphous alloy powder is obtained, and the amorphous phase content reaches more than 75%.

3. The method for preparing a high-entropy amorphous alloy powder pair according to claim 2, characterized in that, High-purity inert gases include one or more of argon, helium, and nitrogen; The melting temperature of the vacuum induction melting furnace is 1350-1550℃.

4. A highly corrosion-resistant coating material comprising the high-entropy amorphous alloy powder of claim 1, characterized in that, The coating material has a porosity of 3.2% or less, an amorphous phase content of 85% or more, and an average microhardness of 1120-1180 HV 0.1 .

5. The method for preparing a highly corrosion-resistant coating material possessing both high entropy effect and amorphous effect according to claim 4, characterized in that, Includes the following steps: High-entropy amorphous alloy powder was used as the coating material, and plasma spraying was carried out in an Ar-N2 atmosphere. The spraying parameters included: the main gas Ar pressure was 45-55 psi, the auxiliary gas N2 pressure was 60-70 psi, the carrier gas N2 pressure was 55-70 psi, the spraying current was 620-680 A, and the spraying distance was 100-120 mm. During the spraying process, energy input is divided into three stages: The first stage, namely the rapid melting stage, involves an energy input power of 20-30kW. This stage lasts for 30%-50% of the total transient thermal history period, or 2-4 ms. The second stage, namely the limited overheating stage, involves an energy input power of 35-45kW combined with an intermittent energy gap of 0.2-0.5ms and a cooling gas flow rate of 20-30L / min to achieve limited overheating of 10-50℃. The duration of this stage is 20%-40% of the total transient thermal history cycle, i.e., 1-3ms. The third stage, namely the rapid cooling stage, involves reducing the energy input power to 0-10kW and increasing the cooling gas flow rate to 40-50L / min to achieve millisecond-level rapid cooling. This stage lasts for 20%-40% of the total transient thermal history cycle, i.e., 1-3 ms. Transient switching time at each stage is <1ms, and the total transient thermal history period is 4-10ms; The deposition process is controlled by a reciprocating linear spray gun scanning strategy. The spray gun moves at a speed of 0.2-0.5 m / s, with a scanning step of 3-5 mm and a powder feed rate of 30-50 g / min per unit time. Within each total transient thermal history cycle, the reciprocating linear scanning is performed according to the three-stage energy input mentioned above. The overlap rate of adjacent scanning trajectories is 40-60%, and the energy superposition is 20-30%, thereby adjusting the single-channel deposition width to 6-12 mm and controlling the heat input distribution uniformity to >90%.

6. The method for preparing a highly corrosion-resistant coating material possessing both high entropy effect and amorphous effect according to claim 5, characterized in that, During the spray gun scanning process, the substrate temperature is controlled within 200-350℃.

7. The method for preparing a highly corrosion-resistant coating material possessing both high entropy effect and amorphous effect according to claim 6, characterized in that, The substrate includes metal substrates and alloy substrates, and the metal substrates and alloy substrates are selected from at least one or more of carbon steel, stainless steel, and low alloy structural steel.

8. The application of the high-entropy amorphous alloy powder according to claim 1 in key components operating under extreme corrosion and abrasion conditions, characterized in that, Key components that operate under extreme corrosion and abrasion conditions include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

9. The application of a high corrosion-resistant coating material with both high entropy and amorphous effects as described in claim 4 in key components operating under extreme corrosion and abrasion conditions, characterized in that... Key components that operate under extreme corrosion and abrasion conditions include aero-engine compressor blades, marine equipment propulsion mechanisms, and transmission components for new energy equipment.

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