Composite energetic material with core-shell structure and preparation method of composite energetic material

Abstract

The invention discloses a core-shell structure composite energetic material and a preparation method thereof, and belongs to the field of energetic materials. The composite material comprises a powdery core material and a modified polyamide shell layer coated on the surface of the powdery core material, and the shell layer consists of a polyamide matrix and a cellulose toughening agent (such as CAB). The preparation method adopts an airflow dispersion-interfacial polymerization method, and the particle size is controlled by adjusting the gas-liquid mass ratio. The toughening agent is utilized to destroy hydrogen bonds of polyamide, the crystallinity of the shell layer is reduced, a tough structure with an impact energy buffering effect is constructed, and the problems that a traditional coating layer is fragile and poor in interface bonding force are effectively solved. The material has the advantages of high encapsulation efficiency, narrow particle size distribution and significantly reduced sensitivity, and has wide application prospects in the fields of high-performance propellants and high-power explosives.

Description

Technical Field

[0001] This invention relates to the field of energetic material coating technology, specifically to a core-shell structured composite energetic material prepared by airflow dispersion-interfacial polymerization and its preparation method. Background Technology

[0002] The synergistic optimization of energy output characteristics and safety performance of energetic materials has always been a research focus. The need to improve the energy density of traditional energetic materials (such as nitramines and nitrate esters) is increasingly urgent. To enhance energy, metallic fuels (such as aluminum powder) are usually added; however, aluminum powder is susceptible to environmental oxidation and agglomeration, severely limiting energy release efficiency. Simultaneously, the inherent high mechanical sensitivity of energetic materials (such as friction and impact sensitivity) poses significant safety hazards in manufacturing, storage, transportation, and application. Microencapsulation technology is an effective means to resolve the contradiction between "energy enhancement" and "sensitivity reduction." By physically isolating the energetic core material with a functional shell, the transmission of external stimuli can be reduced, and the stability of metallic fuels can be improved. Currently, existing encapsulation shell materials mainly have the following shortcomings: Traditional wax materials, such as paraffin shells, are low in cost, easy to coat, and can reduce sensitivity to a certain extent, but they have poor thermal stability and low mechanical strength. They are prone to softening or breakage under complex working conditions and cannot provide long-term protection.

[0003] Polymers and fluororubbers: While materials such as polymethyl methacrylate (PMMA) and fluororubber have achieved a balance between insensitivity and processability, some materials have issues such as low energy contribution or poor compatibility with the core material.

[0004] Inorganic materials and novel nanomaterials: Although metal oxides (such as TiO2) or graphene oxide modified layers can significantly improve the performance, their preparation process is complex and costly, and the inorganic shell is brittle, making it difficult to maintain the integrity of the coating structure in large-scale engineering applications.

[0005] Short-chain polyamide materials: There have been attempts to microencapsulate short-chain polyamides such as PA6 and PA66. However, due to the strong polarity and high crystallinity of the molecular chains, the shell of short-chain polyamides often exhibits high brittleness. When subjected to mechanical extrusion or temperature changes, the coating layer is prone to microcracks or even detachment, thus affecting the sealing and isolation effect on the core material.

[0006] Furthermore, due to the extremely high risk inherent in energetic materials, directly conducting large-scale process exploration carries immense risks. Finding a coating material that possesses excellent mechanical strength and thermal stability, while also exhibiting good flexibility and chemical resistance, and establishing a safe and controllable method for constructing core-shell structures, are critical technical problems that urgently need to be solved in the field of high-energy insensitive energetic materials. Summary of the Invention

[0007] To address the shortcomings of existing technologies, this invention provides a technical solution for preparing core-shell structured composite energetic materials: The core of this method lies in using CAB to modify the polyamide shell. By interfering with the formation of hydrogen bonds between polyamide molecular chains through the steric hindrance effect of the macromolecules of CAB, the crystallinity of the shell is greatly reduced (from 33.8% to below 9.26%), thereby obtaining a protective layer with high toughness.

[0008] A core-shell composite energetic material, comprising a core and a shell; The core may include energetic crystal particles, or energetic crystal particles and high-energy metal additives. The shell is a modified polyamide shell covering the surface of the core; The modified polyamide shell comprises a polyamide matrix and a toughening agent.

[0009] Furthermore, the energetic crystal particles are one or a mixture of two or more of the following: RDX, HMX, CL-20, TATB, pentaerythritol tetranitrate (PETN), and the above-mentioned simulants; the simulants are o-chlorobenzoic acid (2-ClBA) or triphenylphosphine (PPh3); and the high-energy metal additives are nano-aluminum powder (n-Al), boron (B), and metal borides (AlB2, MgB2, TiB2, etc.).

[0010] Furthermore, the polyamide matrix is ​​one or a mixture of two or more of PA610, PA612, and PA1010; the toughening agent is cellulose acetate butyrate (CAB).

[0011] Furthermore, when the core includes energetic crystal particles and high-energy metal additives, the mass percentage of the energetic crystal particles is 75wt% to 83.3wt% based on the total mass of the core; and the mass percentage of the toughening agent is 1wt% to 15wt% based on the total mass of the shell.

[0012] Furthermore, the average particle size of the core-shell structured composite energetic material is between 300 μm and 1500 μm, and the encapsulation efficiency of the shell layer is not less than 90%.

[0013] The above-mentioned method for preparing core-shell structured composite energetic materials employs an airflow dispersion-interfacial polymerization method, and the steps include: (1) Organic phase preparation: The core material is dispersed in an organic solvent containing acyl chloride monomer, toughening agent and surfactant to form a suspension; (2) Aqueous phase preparation: Prepare an aqueous solution containing diamine monomer and neutralizing agent; (3) Airflow spray: The organic phase suspension is atomized and sprayed into the aqueous phase using an airflow nozzle; the acyl chloride monomer and the diamine monomer undergo a condensation reaction at the droplet interface to generate a modified polyamide shell.

[0014] Furthermore, when the polyamide matrix is ​​PA610, the acyl chloride monomer is sebacate chloride, and the diamine monomer is 1,6-hexanediamine; When the polyamide matrix is ​​PA612, the acyl chloride monomer is dodecanediol chloride, and the diamine monomer is 1,6-hexanediamine; When the polyamide matrix is ​​PA1010, the acyl chloride monomer is sebacate chloride, and the diamine monomer is 1,10-decanediamine; Furthermore, the surfactant is Span-80; the organic solvent is carbon tetrachloride; and the neutralizing agent is sodium hydroxide (NaOH).

[0015] Further, in step (1), the mass ratio of the core material, acyl chloride monomer, toughening agent, surfactant, and organic solvent is 20~50:5~15:1~2:0.5:150; In step (2), the mass ratio of diamine monomer, neutralizing agent and water is 3~5:1~2:100.

[0016] Furthermore, in step (3), the gas-liquid flow ratio (m) is controlled. 3 The particle size of the composite material can be adjusted by using a ratio of 0.8 to 5:1 ( / L).

[0017] The beneficial effects of this invention are: Significantly reduced sensitivity: The tough shell can effectively absorb impact energy and prevent shell rupture.

[0018] Uniform coating: The interfacial polymerization method ensures that the coating layer is free of pores and has good compatibility with metallic aluminum powder.

[0019] Controlled particle size: Airflow dispersion technology enables precise control of particle size in the range of hundreds of micrometers to millimeters. Attached Figure Description

[0020] Figure 1 This is a process flow diagram for preparing the core-shell structured composite material of Example 1 of the present invention.

[0021] Figure 2 The X-ray diffraction patterns are of the core-shell composite materials with different CAB mass ratios of the present invention.

[0022] Figure 3 These are SEM images of different locations of the core-shell composite energetic material of Example 1 of the present invention. a) Overall surface morphology, b) Detailed surface morphology, c) Cross-sectional morphology of the shell, d) Backside morphology of the shell.

[0023] Figure 4The X-ray energy spectrum of the core-shell composite material of Example 1 of the present invention is shown.

[0024] Figure 5 This is the curve showing the relationship between the gas-to-liquid ratio (GLR) and the average particle size in Example 1 of the present invention. Detailed Implementation

[0025] Example 1: Preparation of a core-shell structured composite energetic material (2-ClBA / n-Al@PA610) In this embodiment, o-chlorobenzoic acid (2-ClBA) is used as an energetic material to simulate a substitute. The specific steps are as follows: (1) Preparation of organic phase suspension: 0.15 g of toughening agent cellulose acetate butyrate (CAB) was weighed and placed in a beaker. 15 g of carbon tetrachloride was added as a solvent. The mixture was magnetically stirred at 500 rpm for approximately 10 minutes at 25 °C until the toughening agent was completely dissolved. Then, 0.5 g of monomer sebacyl chloride (SCL) was added, and stirring continued at 500 rpm for 2 minutes to form a transparent organic continuous phase system. Subsequently, 3.0 g of powdered core material o-chlorobenzoic acid (2-ClBA), 1.0 g of high-energy metal additive nano-aluminum powder (n-Al), and 0.05 g of Span-80 were added to the system in two batches. The mixture was dispersed using ultrasonic-assisted dispersion (frequency 40 kHz) for 10 minutes to achieve a highly uniform distribution of solid particles in the organic phase, ultimately obtaining a gray homogeneous suspension.

[0026] (2) Preparation of aqueous reaction solution Pour 300 mL of deionized water into a beaker to provide the aqueous environment for interfacial polymerization. Add 10.5 g of monomer 1,6-hexanediamine (HDA) and 3 g of sodium hydroxide (NaOH) sequentially. Stir magnetically for 20 minutes to ensure the amine monomer is fully dissolved and forms a clear, transparent alkaline aqueous solution.

[0027] (3) Airflow dispersion process The organic phase suspension prepared in step (1) was delivered to a gas-flow coaxial nebulizer at a stable flow rate of 10 mL / min using a constant-flow peristaltic pump. Compressed air carrier gas was turned on, and the nebulizer gas flow rate was adjusted to 1.5 m³ / min. 3 / h (gas-liquid flow ratio of 2.5 m) 3 / L). Under the shearing action of high-speed airflow, the organic phase liquid flow containing the core material is sheared and dispersed into a controlled droplet group with a particle size in the range of 300-1600 μm. The vertical distance between the atomizer outlet and the aqueous phase liquid surface is adjusted to 15 cm, so that the droplets are vertically introduced into the aqueous phase reaction zone under the synergistic effect of the carrier gas and gravity.

[0028] (4) Interfacial polymerization reaction When the organic phase droplets enter the aqueous phase, the Schotten-Baumann mechanism facilitates a transient condensation reaction between HDA dissolved in the aqueous phase and SCL on the droplet surface at the carbon tetrachloride / water biphase interface. The reaction is carried out at 25 °C in a weakly alkaline environment, constructing a dense three-dimensional polyamide 610 (PA610) network of amide bonds on the surface of the core particles (2-ClBA and n-Al). Due to the presence of CAB, the resulting PA610 shell is affected by steric hindrance during growth, forming a low-crystallinity, tough coating structure.

[0029] (5) Post-treatment and washing and drying After the reaction lasted for 10 minutes, the resulting composite microspheres were collected by vacuum filtration. The microspheres were washed three times with 50 mL of deionized water and twice with 20 mL of anhydrous ethanol to remove unreacted monomers and impurities remaining on the surface. The washed microspheres were then dried in a 40 °C oven for 30 minutes to obtain dried spherical composite microspheres (labeled 2-ClBA / n-Al@PA610), in which the toughening agent accounted for 7.8 wt% of the shell layer.

[0030] Results: Spherical particles with an average diameter of 850 μm were obtained, with an encapsulation efficiency of 94.47%.

[0031] Comparative Example 1: Preparation of Mechanically Mixed Control Group Sample (Sample-M) To demonstrate the superiority of the core-shell structure of this invention, a mechanically mixed sample with the same composition but without a core-shell structure was prepared as a control.

[0032] (1) Pretreatment: Place o-chlorobenzoic acid and nano aluminum powder in a desiccator with a relative humidity of less than 10% for 24 hours to equilibrate.

[0033] (2) Quantitative ingredient preparation: Weigh 3.0 g of o-chlorobenzoic acid and 1.0 g of nano aluminum powder according to a mass ratio of 3:1.

[0034] (3) Step-by-step grinding: Place o-chlorobenzoic acid in a mortar and pre-grind for 1 minute to eliminate large particle lumps; add nano aluminum powder and manually grind at a frequency of 50 rpm / min for 10 minutes, scraping the wall every 2 minutes to eliminate local agglomerates; then grind in a directional manner by alternating clockwise and counterclockwise force for 5 minutes to enhance the micro-mixing uniformity.

[0035] (4) Screening and filtration: Pass the mixed powder through a 300-mesh stainless steel sieve to remove obvious undispersed agglomerates.

[0036] (5) Storage: The obtained grayish-white homogeneous powder is sealed and stored in a desiccator with built-in silica gel desiccant for later use.

[0037] Example 2 (Real Material Prediction): In Example 1, 2-chlorobenzoic acid (2-ClBA) was replaced with RDX crystals, while all other process parameters remained unchanged. The resulting material exhibited a core-shell morphology and toughened shell structure similar to that of Example 1. The particles were spherical with an average diameter of 450 μm to 820 μm and an encapsulation efficiency of 94.2%.

[0038] Example 3 The acyl chloride monomer in Example 1 was replaced with dodecyl dichloro, while the other process parameters remained unchanged. The resulting material exhibited a core-shell morphology and toughened shell structure similar to that of Example 1. The particles were spherical with an average diameter of 680 μm to 1150 μm and an encapsulation efficiency of 93.7%.

[0039] Example 4 The diamine monomer in Example 1 was replaced with 1,10-decanediamine, while the other process parameters remained unchanged. The resulting material exhibited a core-shell morphology and toughened shell structure similar to that of Example 1. The particles were spherical with an average diameter of 310 μm to 590 μm and an encapsulation efficiency of 91.5%.

[0040] Example 5 The nano-aluminum powder (n-Al) in Example 1 was replaced with the metal boride AlB2, while all other process parameters remained unchanged. The resulting material exhibited a core-shell morphology and toughened shell structure similar to that of Example 1. The particles were spherical with an average diameter of 890 μm to 1420 μm and an encapsulation efficiency of 90.8%.

[0041] The prepared core-shell composite materials with different CAB ratios were further characterized by X-ray diffraction (XRD). The results showed that the polyamide 610 shell without CAB modification exhibited characteristic diffraction signals at 2θ = 21.6°, 24.2°, and 26.7°, confirming that ordered crystalline regions were formed inside the material through intermolecular hydrogen bonding and other interactions. When CAB was introduced into the system, the intensity of the characteristic diffraction peaks of polyamide 610 showed a significant attenuation trend. The crystallinity was calculated according to formula (1) to investigate the effect of cellulose acetate butyrate content on the flexibility of the shell of the composite energetic material.

[0042] (1) In the formula X c It is the percentage of crystallinity of the composite material. A c It is the total integral area of ​​the crystallization diffraction peaks. A a It is the integral of the amorphous scattering halo.

[0043] With increasing CAB content, the crystallinity decreased from 33.8% in pure nylon (0wt% CAB) to 13.93% in the composite material (5.3wt% CAB) and further to 9.26% in the composite material (7.8wt% CAB), indicating that the incorporation of CAB effectively disrupted the orderly packing of polymer molecular chains. This disruption of the crystalline structure is beneficial for increasing the degree of freedom of movement of polymer chain segments, creating favorable microstructural conditions for improving the toughness of the polyamide 610 shell. Besides reducing crystallinity and improving shell toughness, the addition of CAB can also help stabilize the o-chlorobenzoic acid powder and nano-aluminum powder in carbon tetrachloride by increasing the viscosity of the organic phase, preventing particle aggregation, increasing the solid content of the organic phase, and ensuring uniform distribution of the core material within the microcapsules. During interfacial polymerization, CAB can reduce the interfacial tension between carbon tetrachloride and water, stabilize the microdroplet morphology, and promote the uniform formation of the polyamide film.

[0044] Further characterization of the core-shell composite material prepared in Example 1 was performed using scanning electron microscopy (SEM). The results showed that the prepared energetic composite material exhibited a regular spherical structure, indicating high droplet stability during the interfacial polymerization reaction, with no significant deformation or breakage. The surface displayed a uniformly distributed porous structure (Figure 3b), which can be attributed to the evaporation of organic solvents within the microspheres during the preparation process. During solvent evaporation, phase separation occurred in the polymer matrix, forming a porous structure on the microsphere surface. The uniform distribution of surface pores provides favorable conditions for the material's energy release performance. The shell cross-sectional morphology (Figure 3c) clearly showed that the microsphere coating thickness was uniform, ranging from 20 to 30 μm. The cross-sectional morphology revealed a highly dense shell structure with no obvious pores. The uniformity of the shell thickness indicates a good balance between monomer diffusion rate and reaction conditions during the interfacial polymerization reaction. The formation of the highly dense structure suggests a high cross-linking density and tight molecular chain arrangement during the reaction, which is beneficial for improving the material's mechanical strength and barrier properties. The absence of obvious pores confirms that the solvent evaporation process was properly controlled and did not damage the structural integrity of the material.

[0045] Further energy dispersive spectroscopy (EDS) characterization was performed on the core-shell composite material prepared in Example 1. Correlation analysis between the characteristic (Al Kα1) two-dimensional distribution and SEM morphology showed that Al elements exhibited a uniform spatial distribution in the sample, but the signal intensity was significantly attenuated, attributed to the X-ray shielding effect of the polyamide shell. Quantitative characterization revealed that when the shell thickness reached 20 μm, the absorption of X-rays by the polyamide matrix reduced the effective detection depth to below the core region of the aluminum nanoparticles. This phenomenon directly confirms that the microencapsulation coating process successfully achieved the spatial confinement construction of the core-shell structure. SEM cross-sectional morphology analysis further verified the integrity of the shell structure: the aluminum nanoparticles were completely coated by a continuous and dense polyamide shell, and the shell thickness was positively correlated with the X-ray shielding effect. Notably, the presence of the core material did not significantly interfere with the interfacial polymerization kinetics of 1,6-hexanediamine and sebacyl chloride, indicating that the coating system effectively maintained the chemical controllability of the shell film formation process while preserving the functional properties of the core layer. Two-dimensional distribution imaging analysis using characteristic X-ray energy dispersive spectroscopy (C Kα1_2, O Kα1, Cl Kα1, and N Kα1_2) revealed a uniform and continuous distribution of Cl and N elements on the microcapsule surface, a phenomenon highly consistent with theoretical predictions regarding the chemical composition of the polyamide shell. The simultaneous and uniform distribution of Cl (derived from sebacyl chloride monomer) and N (derived from 1,6-hexanediamine monomer) confirms that the two monomers formed a complete amide bond network structure through interfacial polymerization. Combined with the gradient distribution of C and O elements, it can be further inferred that the polyamide shell possesses dense cross-linking properties, with no localized insufficient monomer reaction or phase separation. These results validate the high-efficiency construction quality of the polyamide shell at the molecular scale, and its chemical homogeneity and structural density provide crucial guarantees for the mechanical stability and core layer protection effectiveness of the microcapsules.

[0046] Further, the shell-to-shell composite material prepared in Example 1 was tested using an improved solenoid extraction method to determine the shell-to-shell ratio and encapsulation efficiency. The experimental procedure for determining the shell ratio and encapsulation efficiency is as follows: (1) Pretreatment of filter cartridge: After covering the numbered glue-free filter cartridge with filter paper, dry it in an oven at 100±2 ℃ for 2 h, place it in a desiccator to cool to constant weight, and record the initial mass a (the humidity of the experimental environment is <70%); (2) Pretreatment of sample: After grinding the sample to be tested, dry it at 100±2 ℃ for 3 h, transfer it to a desiccator to cool naturally to room temperature, accurately weigh an appropriate amount of sample and load it into the pretreated filter cartridge, and record the total mass b; (3) Organic phase extraction: Place the sample-loaded filter cartridge into a Soxhlet extractor, inject 1.67 times the siphon volume of ethyl acetate to ensure that the sample-loaded filter cartridge is submerged, connect the condensation system and continuously extract in a constant temperature oil bath at 90 ℃ (control the siphon frequency 10-15 min / time) until no white solid precipitates in the extract (about 6-12 h). After extraction, take out the filter cartridge, place it in a ventilated place to evaporate the solvent, and then dry the filter cartridge at 80 ℃ for 30 h. After min, place it in a desiccator to cool to constant weight; (4) Inorganic phase treatment: Slowly add 5wt% sodium hydroxide solution to the above filter cartridge until the black color of the sample powder fades. (5) Final value determination: After the reaction, the filter cartridge is dried at 100 ℃ for 1 h, placed in a desiccator to cool to constant weight, and the final value c is recorded. The shell material mass is calculated by subtracting the c value from the a value.

[0047] The formulas for calculating the shell-to-material ratio and encapsulation ratio (2-5) are shown below. (2) (3) (4) (5) Three sets of repeatable experiments were conducted under the same conditions as in Example 1, and the calculated data are shown in Table 1: Table 1. Data on shell material ratio and encapsulation efficiency.

[0048] After averaging the three sets of data, the final result is that the composite energetic material has a shell material ratio of 42.54 wt%, a core material ratio of 57.46 wt%, and an encapsulation rate of 94.47 wt%.

[0049] Furthermore, ten different gas-liquid ratio parameters (GLR=) were set through the system. Q g / Q l ,in Q g For gas flow rate, Q l(Liquid flow rate), except for the gas-liquid ratio, the experimental conditions for each group were the same as in Example 1. At least 150 atomized droplet samples were collected under each experimental condition, and their particle size distribution characteristics were statistically analyzed. Based on the experimental data (as shown in Table 2), a quantitative correlation model between the gas-liquid ratio and droplet size was established using regression analysis.

[0050] Table 2. Data on atomized droplet samples

[0051] The relationship curve between the gas-to-liquid ratio (GRR) and the average particle size obtained from fitting the experimental data is shown in Figure 5. The experimental data were subjected to regression analysis using a quadratic polynomial model, and its mathematical expression (7) is: (7) In the formula, x is the gas-liquid ratio ( Q g / Q l ), y is the average particle size ( D a (μm). Goodness of fit R 2 =0.9993, the model and experimental data are in excellent agreement. Based on this mathematical model, gradient design of microsphere size can be achieved by precisely adjusting the gas-liquid ratio parameter. This particle size controllability strategy directly affects the combustion wave propagation rate and energy release spatial uniformity of composite energetic materials by changing the specific surface area and mass transfer characteristics of microspheres, providing a quantifiable and controllable process basis for the functional customization of propellants or explosives.

Claims

1. A core-shell structured composite energetic material, characterized in that, Includes the core and shell; The core may include energetic crystal particles, or energetic crystal particles and high-energy metal additives. The shell is a modified polyamide shell covering the surface of the core; The modified polyamide shell comprises a polyamide matrix and a toughening agent.

2. The core-shell structured composite energetic material according to claim 1, characterized in that: The energetic crystal particles are one or a mixture of two or more of the following: RDX, Octogen, hexanitrosa-isowurtzite, 1,3,5-triamino-2,4,6-trinitrobenzene, pentaerythritol tetranitrate, and the above-mentioned simulants; the high-energy metal additives are nano-aluminum powder, boron, and metal borides.

3. The core-shell structured composite energetic material according to claim 1, characterized in that: The polyamide matrix is ​​one or a mixture of two or more of PA610, PA612, and PA1010; the toughening agent is cellulose acetate butyrate.

4. The core-shell structured composite energetic material according to claim 1, characterized in that: When the core comprises energetic crystal particles and high-energy metal additives, the energetic crystal particles account for 75 wt% to 83.3 wt% of the total mass of the core; and the toughening agent accounts for 1 wt% to 15 wt% of the total mass of the shell.

5. The core-shell structured composite energetic material according to claim 1, characterized in that: The average particle size of the core-shell structured composite energetic material is between 300 μm and 1500 μm, and the encapsulation efficiency of the shell is not less than 90%.

6. A method for preparing a core-shell structured composite energetic material according to any one of claims 1-5, characterized in that, The airflow dispersion-interfacial aggregation method is employed, and the steps include: (1) Organic phase preparation: The core material is dispersed in an organic solvent containing acyl chloride monomer, toughening agent and surfactant to form a suspension; (2) Aqueous phase preparation: Prepare an aqueous solution containing diamine monomer and neutralizing agent; (3) Airflow spray: The organic phase suspension is atomized and sprayed into the aqueous phase using an airflow nozzle; the acyl chloride monomer and the diamine monomer undergo a condensation reaction at the droplet interface to generate a modified polyamide shell.

7. The preparation method according to claim 6, characterized in that: When the polyamide matrix is ​​PA610, the acyl chloride monomer is sebacate chloride, and the diamine monomer is 1,6-hexanediamine; When the polyamide matrix is ​​PA612, the acyl chloride monomer is dodecanediol chloride, and the diamine monomer is 1,6-hexanediamine; When the polyamide matrix is ​​PA1010, the acyl chloride monomer is sebacate chloride, and the diamine monomer is 1,10-decanediamine.

8. The preparation method according to claim 6, characterized in that: The surfactant is Span-80; the organic solvent is carbon tetrachloride; and the neutralizing agent is sodium hydroxide.

9. The preparation method according to claim 6, characterized in that: In step (1), the mass ratio of the core material, acyl chloride monomer, toughening agent, surfactant, and organic solvent is 20~50:5~15:1~2:0.5:150; In step (2), the mass ratio of diamine monomer, neutralizing agent and water is 3~5:1~2:

100.

10. The preparation method according to claim 6, characterized in that: In step (3), the particle size of the composite material is adjusted by controlling the gas-liquid flow ratio between 0.8 and 5:1.

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