Method for improving interface bonding strength of powder-composite mixed component

Abstract

The invention relates to a method for improving the interface bonding strength of a powder-composite material mixed component, belongs to the technical field of composite material manufacturing, and solves the problems of insufficient interface bonding force and easy stripping failure caused by large difference of physicochemical properties of powder and a composite material matrix in the prior art. The method comprises the following steps: growing a carbon nanotube array vertical to a substrate on the surface of metal or ceramic powder in situ; carrying out laminated assembly on the modified powder and the composite material prepreg; the carbon nano tube is punctured and embedded into the composite material matrix through a hot pressing process, and a firm three-dimensional nano mechanical interlocking structure is formed in an interface area. According to the method, efficient stress transfer and strong interface combination between the powder and the composite material are achieved, the interface shear strength and anti-stripping performance of the composite component are remarkably improved, and the method can be widely applied to manufacturing of lightweight composite parts needing high-reliability connection in aerospace, electronic packaging and high-end equipment.

Description

Technical Field

[0001] This invention relates to the field of composite material manufacturing technology, and in particular to a method for improving the interfacial bonding strength of powder-composite hybrid components. Background Technology

[0002] Powder-composite hybrid components combine the functionality and thermal conductivity of powder materials (such as metals or ceramics) with the lightweight and designability advantages of composite materials, showing broad application prospects in aerospace, electronic packaging, and other fields. However, due to the significant differences in physicochemical properties between powder materials and composite matrix, the low interfacial bonding strength has always been a key bottleneck restricting the development of such components, easily leading to interfacial delamination failure, which seriously affects the structural integrity and service reliability of the entire component.

[0003] Currently, conventional methods for improving the interfacial bonding performance of powder-composite materials all have significant shortcomings. For example, chemical treatment methods such as using silane coupling agents can only establish weak interfacial chemical bonds, with limited improvement in bonding strength (usually less than 30%), and are sensitive to environmental humidity, resulting in poor durability. Micron-level mechanical roughening achieved through sandblasting and laser etching can introduce some mechanical interlocking, but the improvement is limited and easily introduces stress concentration points at the interface, potentially inducing crack initiation. In recent years, researchers have attempted to use carbon nanotubes (CNTs) as reinforcements, such as introducing them into the interfacial layer through solution blending or surface coating. However, because CNTs are prone to aggregation, unevenly distributed at the interface, and randomly oriented, they are difficult to effectively embed into the matrix. In addition, the bonding force with the matrix is ​​weak, making it impossible to construct an efficient and durable three-dimensional nano-interlocking structure. Therefore, the actual reinforcement effect is far lower than theoretical expectations.

[0004] In summary, existing technologies are limited by factors such as low bonding strength, unreasonable interaction scale, or uncontrollable nanostructures, making it difficult to achieve high-strength, high-toughness, and long-term stable bonding at the powder-composite interface. Therefore, developing a new method capable of constructing precisely controllable three-dimensional nano-interlocking structures in situ at the interface has become an urgent technical challenge to be solved in this field. Summary of the Invention

[0005] To address the aforementioned technical problems, this invention provides a method for improving the interfacial bonding strength of powder-composite hybrid components, thereby solving at least one of the problems in the prior art, such as insufficient interfacial bonding force and easy peeling.

[0006] On one hand, the present invention provides a method for improving the interfacial bonding strength of powder-composite hybrid components, comprising the following steps:

[0007] S1. In-situ growth of carbon nanotube arrays perpendicular to the surface of powder material;

[0008] S2. Powder material with carbon nanotube arrays grown on it is laminated and assembled with a composite matrix;

[0009] S3. The carbon nanotubes in the carbon nanotube array are punctured and embedded into the composite material matrix through a hot pressing process, thereby forming a three-dimensional nanomechanical interlocking structure at the interface between the powder and the composite material.

[0010] Furthermore, the powder material is a metal powder or a ceramic powder; the particle size range of the powder material is 10-200 μm.

[0011] Furthermore, in S1, the method for in-situ growth of carbon nanotube arrays is chemical vapor deposition, the reaction temperature of which is 550-800℃, the carbon source is acetylene or ethylene, and the growth time is 5-60 minutes.

[0012] Furthermore, in S3, the parameters of the hot pressing process are: pressure 0.1-5MPa, temperature 80-250℃, and time 0.5-4h.

[0013] Furthermore, the ratio of the length of the grown carbon nanotubes to the average particle size of the powder material is 1:5 to 1:1.

[0014] Furthermore, before growing the carbon nanotube array, the powder material is pretreated by immersing it in a solution containing catalyst metal ions, which are one or more of iron, cobalt, or nickel ions, and then drying it to load the catalyst metal particles onto the surface of the powder material.

[0015] Furthermore, the composite matrix is ​​a prepreg; the prepreg includes reinforcing fibers and uncured polymer resin; the hot pressing process simultaneously completes the composite molding and cures the polymer resin.

[0016] Furthermore, the reinforcing fiber is carbon fiber, glass fiber, or aramid fiber; the polymer resin is epoxy resin, phenolic resin, or bismaleimide resin.

[0017] On the other hand, the present invention proposes a powder-composite material hybrid component, including a powder material region and a composite material matrix region. At the interface between the powder material region and the composite material matrix region, carbon nanotubes extending outward from the surface of the powder material and embedded in the composite material matrix are dispersed. The carbon nanotubes and the composite material matrix are entangled with each other to form a three-dimensional nanomechanical interlocking structure.

[0018] Furthermore, the powder-composite material hybrid component is prepared by the method described above, and the component has an interfacial shear strength ≥38MPa and a 90° peel strength ≥95N / mm.

[0019] Compared with the prior art, the present invention can achieve at least one of the following beneficial effects:

[0020] 1) Existing technologies mainly rely on intermolecular forces or micron-level mechanical interlocking, resulting in low interfacial bonding strength and high brittleness. This invention achieves a transformation from "two-dimensional planar adhesion" to "three-dimensional spatial anchoring" by constructing a three-dimensional nanomechanical interlocking structure in the interfacial region. This structure, with its large specific surface area and mechanical interlocking effect, significantly enhances the interfacial load transfer capability. Experimental results show that the interfacial shear strength and 90° peel strength are increased by more than 80% and 100% respectively compared to traditional methods (such as sandblasting or coupling agent treatment), fundamentally solving the problem of easy interfacial peeling failure.

[0021] 2) While traditional reinforcement methods (such as introducing carbon nanotubes through solution blending) can improve static strength to some extent, the random distribution of the reinforcement can easily lead to stress concentration under cyclic loading, thus accelerating fatigue failure. The oriented carbon nanotubes used in this invention can effectively bridge microcracks, promote stress dispersion, and inhibit crack initiation and propagation. Verified by standards such as ASTM D3165, the fatigue life of the resulting hybrid component is more than three times that of components obtained using traditional methods, significantly improving durability and service reliability under dynamic loading conditions.

[0022] 3) Existing interface modification processes (such as solution blending) are often complex and have poor compatibility with existing production lines. The chemical vapor deposition and hot pressing processes used in this invention can both be implemented on existing powder metallurgy and composite material molding equipment (such as autoclaves and molding presses) without major new investment or process modifications, providing a practical and feasible technical approach for the large-scale, low-cost manufacturing of high-performance hybrid components.

[0023] In this invention, the above-described technical solutions can be combined with each other to achieve more preferred combinations. Other features and advantages of this invention will be set forth in the following description, and some advantages may become apparent from the description or be learned by practicing the invention. The objects and other advantages of this invention can be realized and obtained from what is particularly pointed out in the description and drawings. Attached Figure Description

[0024] The accompanying drawings are for illustrative purposes only and are not intended to limit the invention. Throughout the drawings, the same reference numerals denote the same parts.

[0025] Figure 1 A schematic diagram of the nano-stitching structure of the interface region of the powder-composite hybrid component provided by the present invention;

[0026] Figure 2 This is a process flow diagram of the method for improving the interfacial bonding strength of powder-composite hybrid components according to the present invention. Detailed Implementation

[0027] Preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form part of this application and are used together with the embodiments of the present invention to illustrate the principles of the present invention, but are not intended to limit the scope of the present invention.

[0028] On one hand, this invention discloses a method for improving the interfacial bonding strength of powder-composite hybrid components. The "powder-composite hybrid component" refers to a heterogeneous structural component formed by bonding metal or ceramic powder materials with fiber-reinforced polymer matrix composites through a specific process. The core of this invention lies in constructing a three-dimensional nanomechanical interlocking structure (such as...) in the interfacial region. Figure 1 As shown in the figure, it fundamentally breaks through the limitations of traditional methods that rely on physical adsorption or weak chemical bonding, and significantly improves the mechanical properties of the interface.

[0029] The method is as follows Figure 2 As shown, it includes the following steps:

[0030] S1. In-situ growth of carbon nanotube arrays perpendicular to the surface of powder material;

[0031] S2. Powder material with carbon nanotube arrays grown on it is laminated and assembled with a composite matrix;

[0032] S3. The carbon nanotubes in the carbon nanotube array are punctured and embedded into the composite material matrix through a hot pressing process, thereby forming a three-dimensional nanomechanical interlocking structure at the interface between the powder and the composite material.

[0033] Furthermore, the powder material is a metal powder or a ceramic powder; the particle size range of the powder material is 10-200 μm (e.g., 10 μm, 20 μm, 50 μm, 80 μm, 100 μm, 120 μm, 150 μm, 180 μm, 200 μm).

[0034] Furthermore, in S1, the method for in-situ growth of carbon nanotube arrays is chemical vapor deposition, the reaction temperature of which is 550-800℃ (e.g., 550℃, 600℃, 650℃, 700℃, 750℃, 800℃), the carbon source is acetylene or ethylene, and the growth time is 5-60 minutes (e.g., 5 minutes, 10 minutes, 15 minutes, 20 minutes, 30 minutes, 40 minutes, 50 minutes, 60 minutes).

[0035] Furthermore, in S3, the parameters of the hot pressing process are: pressure 0.1-5MPa (e.g. 0.1MPa, 0.5MPa, 1MPa, 2MPa, 3MPa, 4MPa, 5MPa), temperature 80-250℃ (e.g. 80℃, 100℃, 120℃, 150℃, 180℃, 200℃, 220℃, 250℃), and time 0.5-4h (e.g. 0.5h, 1h, 1.5h, 2h, 2.5h, 3h, 3.5h, 4h).

[0036] Furthermore, the ratio of the length of the grown carbon nanotubes to the average particle size of the powder material is 1:5 to 1:1 (e.g., 1:5, 1:4, 1:3.5, 1:3, 1:2.5, 1:2, 1:1).

[0037] Furthermore, before growing the carbon nanotube array, the powder material is pretreated by immersing it in a solution containing catalyst metal ions, which are one or more of iron, cobalt, or nickel ions, and then drying it to load the catalyst metal particles onto the surface of the powder material.

[0038] Furthermore, the composite matrix is ​​a prepreg; the prepreg includes reinforcing fibers and uncured polymer resin, the polymer resin having a mass content of 35% ± 5%. The hot pressing process simultaneously completes the composite molding and cures the polymer resin.

[0039] Furthermore, the reinforcing fiber is carbon fiber, glass fiber, or aramid fiber; the polymer resin is epoxy resin, phenolic resin, or bismaleimide resin.

[0040] The following provides a detailed explanation of the above steps and preferred conditions:

[0041] Specifically, in step S1, the powder is first pretreated with a catalyst. The direct purpose of this step is to provide nucleation sites for the vapor-phase growth of CNTs. Metal (e.g., titanium alloy, aluminum alloy) or ceramic (e.g., alumina, silicon carbide) powders with an average particle size of 10-200 μm are impregnated in a solution containing catalyst metal ions (e.g., iron, cobalt, nickel ions). For example, solutions of salts such as ferric nitrate or cobalt chloride can be used, preferably at a concentration of 0.01-0.5 mol / L, for an impregnation time of 30-180 minutes. Subsequently, the powder is dried at 80-120°C, allowing the catalyst precursor to be loaded onto the powder surface. During subsequent CVD heating, the precursor decomposes and reduces to nanoscale metal droplets, where carbon atoms dissolve and precipitate in a supersaturated state, forming CNTs. The size and distribution of the catalyst particles directly determine the density, coarseness, and uniformity of the grown CNTs, having a decisive impact on the final interface enhancement effect.

[0042] Subsequently, in-situ growth of CNT arrays is performed. Chemical vapor deposition (CVD) is the preferred method, with the reaction temperature strictly controlled between 550-800℃. Setting this parameter range is crucial for achieving high-quality, oriented CNT arrays: below 550℃, catalyst activity is insufficient, carbon source decomposition efficiency is low, CNT growth is slow or incomplete, and it is difficult to form a regular array; above 800℃, it may cause lattice damage to the powder matrix or the already grown CNTs. Acetylene or ethylene is preferred as the carbon source, and the growth time is 5-60 minutes. By controlling this parameter window, the diameter, wall number, and length of the CNTs can be effectively adjusted.

[0043] The length of the grown CNTs must be strictly controlled to be 1:5 to 1:1 relative to the average particle size of the powder. If the CNTs are too long (ratio > 1:1), they are prone to entanglement and collapse during subsequent processing, destroying their orientation and making effective penetration impossible. If the CNTs are too short (ratio < 1:5), they cannot achieve sufficient penetration depth and are difficult to form a strong mechanical anchor. This optimal range ensures that the CNTs have sufficient anchoring length while maintaining their uprightness and orientation independence, allowing them to efficiently penetrate the resin matrix like countless tiny "nanoprobes" during hot pressing.

[0044] Specifically, in step S2, the modified powder and prepreg (such as carbon fiber / epoxy resin, glass fiber / bismaleimide resin prepreg) are laminated and assembled according to the designed configuration. The laminated assembly includes forming an integral structure by stacking the modified powder and prepreg in layers, which can be implemented by methods such as lay-up (e.g., laying the prepreg layer by layer in the designed direction, while dispersing the modified powder between or within the layers).

[0045] The prepreg includes reinforcing fibers (such as carbon fiber, glass fiber, or aramid fiber) and uncured polymer resin (such as epoxy resin, phenolic resin, or bismaleimide resin). During the lamination process, layered stacking can be achieved by manual or automated placement, and the powder can be uniformly dispersed or gradient-distributed within or between layers.

[0046] Specifically, in step S3, the hot-pressing process is the final step in achieving nanomechanical interlocking. Its parameters (pressure 0.1-5 MPa, temperature 80-250℃, time 0.5-4 h) need to be precisely matched with the curing process of the composite matrix. If the temperature is too low (<80℃) or the pressure is too low (<0.1 MPa), the resin viscosity will be high and the flowability will be poor, making it difficult for CNTs to effectively penetrate and embed. If the temperature is too high (>250℃) or the pressure is too high (>5 MPa), it may lead to resin degradation, fiber damage, or crushing of CNTs.

[0047] Specifically, for epoxy resin systems, the hot-pressing temperature is preferably 120-180℃; for bismaleimide resin systems, it is preferably 180-230℃. The pressure is typically preferably 1-3 MPa.

[0048] In this process, the hot-pressing process simultaneously achieves resin curing and CNT insertion. The polymer resin in the prepreg melts upon heating, its viscosity decreases, and it flows and impregnates the powder and CNTs under pressure. The vertically aligned CNTs, driven by pressure, penetrate the softened resin, subsequently undergoing cross-linking and curing, firmly locking the CNTs within the solidified matrix network, ultimately forming a strong three-dimensional nanomechanical interlocking interface. The heating rate is preferably controlled at 1-5℃ / min, and the cooling rate is preferably 1-3℃ / min to ensure a good match between the resin melting / curing process and the CNT insertion process, and to avoid interface damage caused by thermal stress.

[0049] The "three-dimensional nanomechanical interlocking structure" is specifically characterized by: one end of a directional CNT array firmly growing on the surface of powder particles, and the other end directionally penetrating and embedding into the composite matrix, forming a spatial three-dimensional interpenetrating network in the interface region. This structure replaces the traditional weak intermolecular adsorption with a strong mechanical interlocking mechanism.

[0050] Furthermore, to further enhance the thermal and electrical conductivity of the interface, the grown CNTs can be further modified, such as by electroless plating to deposit a layer of metallic nickel on the CNT surface, or by vapor deposition to coat a silicon carbide coating. This approach can retain the original reinforcing effect of CNTs while increasing their chemical compatibility and bonding strength with the substrate, and even constructing a continuous multifunctional network, thus broadening the application scenarios of the components.

[0051] The key to this invention lies in the high degree of synergy between the various steps, specifically reflected in the following two aspects:

[0052] On the one hand, the vertical CNT array is the structural prerequisite for achieving nano-puncture, providing the physical basis for mechanical interlocking; on the other hand, the precisely controlled hot pressing process is the technological guarantee for effective embedding, ensuring that the resin has suitable fluidity and ultimately cures and locks in place. The two complement each other and are indispensable, working together to complete the fundamental transformation from simple surface adhesion to a robust three-dimensional nanomechanical interlocking structure.

[0053] On the other hand, catalyst pretreatment steps (precursor concentration, impregnation time, drying process) determine the prerequisites for CNT growth (catalyst particle size, distribution, and activity); while CVD growth parameters (temperature, time, carbon source) directly regulate the final morphology of CNTs (density, orientation, tube diameter, and length). Only through precise matching and synergistic optimization of the preceding and following steps can high-density, highly oriented CNT arrays be obtained on the powder surface.

[0054] On the other hand, the present invention also provides a powder-composite material hybrid component, including a powder material region and a composite material matrix region. At the interface between the powder material region and the composite material matrix region, carbon nanotubes extending outward from the surface of the powder material and embedded in the composite material matrix are dispersed. The carbon nanotubes and the composite material matrix are entangled with each other to form a three-dimensional nanomechanical interlocking structure.

[0055] Furthermore, the component is prepared by the method described above.

[0056] This structure differs fundamentally from existing technologies that use random dispersion of CNTs to reinforce interfaces through simple blending or coating. The three-dimensional interlocking structure of this invention enables stress to be efficiently transferred from the composite matrix to the powder material via oriented CNTs. Its "bridging" effect effectively inhibits the initiation and propagation of microcracks, forcing cracks to deflect or requiring more energy to overcome the pull-out resistance of the CNTs. This significantly improves stress distribution, avoids stress concentration at the interface, and fundamentally solves the problem of poor CNT-reinforced interfaces in the past. Experimental measurements show that this structure increases the interfacial shear strength of components to ≥38MPa, the 90° peel strength to ≥95N / mm, and improves fatigue life by 3 times under the ASTM D3165 standard test.

[0057] In summary, the innovation of this invention lies in the first-time creative combination of the two key technical steps of "in-situ growth of vertical CNT arrays on powder surface" and "hot pressing puncture molding". Through the synergistic optimization of process parameters in each step, a significant synergistic enhancement effect is generated, successfully solving the traditional problems of CNT dispersion, orientation and interfacial wettability in composite materials.

[0058] The present invention will be described in more detail below through specific embodiments. These embodiments are merely descriptions of the best implementation of the invention and do not limit the scope of the invention in any way.

[0059] Example 1

[0060] This embodiment provides a method for improving the interfacial bonding strength of titanium alloy / carbon fiber composites, including the following steps:

[0061] S1. In-situ growth of carbon nanotube arrays perpendicular to the surface of Ti-6Al-4V titanium alloy powder (average particle size of about 50 μm): The powder was first immersed in 0.05 mol / L ferric nitrate ethanol solution for 30 minutes, and then vacuum dried at 80 °C for 2 hours to ensure uniform loading of the catalyst precursor; then, the treated powder was placed in a tubular chemical vapor deposition (CVD) furnace and heated to 650 °C under an argon / hydrogen mixed protective atmosphere (volume ratio 9:1), and then 50 sccm of acetylene (C2H2) was introduced as a carbon source and reacted for 15 minutes, finally growing a carbon nanotube array with a length of about 12±2 μm and perpendicular orientation on the powder surface;

[0062] S2. The titanium alloy powder with CNT arrays grown thereon is laminated and assembled with uncured carbon fiber / epoxy resin prepreg (wherein the mass content of epoxy resin prepreg is 35%) according to the design.

[0063] S3. Place the assembly in a hot press and maintain it at a pressure of 1.5 MPa and a temperature of 150°C for 2 hours. During this process, the epoxy resin melts and solidifies, while the carbon nanotubes puncture and embed into the composite matrix under pressure, ultimately forming a robust three-dimensional nanomechanical interlocking structure at the interface.

[0064] Example 2

[0065] The difference from Example 1 is as follows:

[0066] In S1, silicon carbide (SiC) ceramic powder with an average particle size of about 80 μm was used to replace titanium alloy powder; the catalyst solution was changed to 0.03 mol / L cobalt nitrate solution, the impregnation time was 40 minutes, and the drying conditions were 100℃ for 1.5 hours; the CVD process parameters were adjusted to: reaction temperature 720℃, carbon source changed to ethylene (C2H4), and reaction time 20 minutes.

[0067] In S2, glass fiber / phenolic resin prepreg is used as the composite matrix;

[0068] In S3, the hot pressing process parameters are adjusted accordingly to: pressure 2.0MPa, temperature 170℃, and time 1.5 hours, to adapt to the curing characteristics of phenolic resin.

[0069] Example 3

[0070] The difference from Example 1 is as follows:

[0071] In S1, 6061 aluminum alloy powder with an average particle size of about 30 μm was used instead of titanium alloy powder; the catalyst solution was changed to a 0.08 mol / L nickel chloride (NiCl2) solution, the impregnation time was 20 minutes, and the drying conditions were 70℃ for 3 hours; the CVD process parameters were adjusted to: reaction temperature 580℃, a mixed gas consisting of acetylene (40 sccm) and hydrogen (20 sccm) was introduced as a carbon source, and the reaction time was 25 minutes.

[0072] In S2, aramid fiber / bismaleimide resin prepreg is used as the composite matrix;

[0073] In S3, the hot pressing process parameters are adjusted to: pressure 0.8MPa, temperature 210℃, and time 3 hours, to adapt to the high-temperature curing process of bismaleimide resin.

[0074] Comparative Example 1

[0075] The only difference from Example 1 is that step S1 is omitted, no modification is performed on the titanium alloy powder, and the original powder and prepreg are directly used for S2 lay-up and S3 hot pressing.

[0076] Comparative Example 2

[0077] The only difference from Example 1 is that step S1 is changed to physically mixing commercially purchased multi-walled carbon nanotubes with titanium alloy powder by mechanical stirring, in an attempt to make CNTs adhere to the powder surface.

[0078] Comparative Example 3

[0079] The only difference from Example 1 is that the temperature in the S3 hot pressing process is reduced to 60°C (other parameters remain unchanged).

[0080] Performance Testing and Results Analysis

[0081] The interfacial shear strength (ASTM D1002 or equivalent standard) and 90° peel strength (ASTM D3167 or equivalent standard) of the specimens prepared in each embodiment and comparative example were tested, and the results are shown in Table 1.

[0082] Table 1. Interfacial performance test results of each group of samples.

[0083]

[0084] As can be seen from the data in Table 1, Examples 1-3 of the present invention, by in-situ growing vertical CNT arrays and hot-pressing to construct a three-dimensional nanomechanical interlocking structure, achieved significant improvements in interfacial shear strength and 90° peel strength compared to the baseline group of Comparative Example 1. Among them, Example 1 showed the best performance, with a shear strength of 45.2 MPa and a peel strength of 125 N / mm, with improvement rates of 87.5% and 108.3%, respectively. In contrast, Comparative Example 2, which used a physical mixing method of CNTs, had limited enhancement effect (improvement rate ≤20%) due to uneven CNT dispersion, random orientation, and weak bonding. Comparative Example 3, due to insufficient hot-pressing temperature, resulted in poor resin flowability and insufficient CNT penetration and embedding, with negligible performance improvement (improvement rate <10%). This fully demonstrates the necessity and effectiveness of the synergistic effect of "in-situ growth of vertical arrays" and "optimized hot-pressing penetration" in achieving strong interfacial bonding in the method of the present invention.

[0085] The above description is only a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any changes or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in the present invention should be included within the scope of protection of the present invention.

Claims

1. A method for improving the interfacial bonding strength of powder-composite hybrid components, characterized in that, Includes the following steps: S1. An array of carbon nanotubes perpendicular to the surface of the powder material is grown in situ on the surface of the powder material; S2. The powder material with carbon nanotube arrays grown on it is stacked and assembled with the composite matrix; S3. The carbon nanotubes in the carbon nanotube array are punctured and embedded into the composite material matrix through a hot pressing process, thereby forming a three-dimensional nanomechanical interlocking structure at the interface between the powder and the composite material.

2. The method according to claim 1, characterized in that, In S1, the powder material is a metal powder or a ceramic powder; the particle size range of the powder material is 10-200 μm.

3. The method according to claim 1 or 2, characterized in that, In S1, the method for in-situ growth of carbon nanotube arrays is chemical vapor deposition, the reaction temperature of chemical vapor deposition is 550-800℃, the carbon source is acetylene or ethylene, and the growth time is 5-60 minutes.

4. The method according to claim 1, characterized in that, In S3, the parameters of the hot pressing process are: pressure 0.1-5MPa, temperature 80-250℃, and time 0.5-4h.

5. The method according to claim 1, characterized in that, In S3, the ratio of the length of the carbon nanotube to the average particle size of the powder material is 1:5 to 1:

1.

6. The method according to claim 1, characterized in that, In S3, before growing the carbon nanotube array, the powder material is pretreated by immersing it in a solution containing catalyst metal ions and then drying it so that the catalyst metal particles are loaded onto the surface of the powder material. And / or, the catalyst metal ion is one or more of iron, cobalt or nickel ions.

7. The method according to claim 1, characterized in that, In S2 and S3, the composite material matrix is ​​a prepreg; the prepreg includes reinforcing fibers and uncured polymer resin; And / or, the hot pressing process simultaneously completes the composite molding and cures the polymer resin.

8. The method according to claim 7, characterized in that, The reinforcing fiber is carbon fiber, glass fiber, or aramid fiber; the polymer resin is epoxy resin, phenolic resin, or bismaleimide resin.

9. A powder-composite material hybrid component, comprising a powder material region and a composite material matrix region, characterized in that, At the interface between the powder material region and the composite matrix region, carbon nanotubes extending outward from the surface of the powder material and embedded in the interior of the composite matrix are dispersed. The carbon nanotubes and the composite matrix are intertwined to form a three-dimensional nanomechanical interlocking structure.

10. The powder-composite material hybrid component according to claim 9, characterized in that, The component is prepared by the method of any one of claims 1-8, and the interfacial shear strength of the component is ≥38MPa, and the 90° peel strength is ≥95N / mm.

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