Multifunctional Aramid Nanofiber/MXene/Aramid Fiber Composite Fabric with Outstanding EMI Shielding Performance

Abstract

Developing aramid fiber (AF) with electromagnetic interference (EMI) shielding properties is of significant importance for expanding their applications in the military, aerospace, and industrial sectors. Current research on the EMI shielding properties of AF often encounters challenges such as structural damage to the fibers and inadequate shielding performance. In this study, we used vacuum-assisted filtration technology to sequentially deposit aramid nanofiber (ANF) and MXene onto the surface of AF fabric, thus preparing ANF/MXene/AF composite fabric. MXene, with its large specific surface area and excellent electrical conductivity, was used in conjunction with ANF, which acts as an intermediate layer to effectively filter MXene and improve the interfacial adhesion between the MXene and AF. The results showed that, under the combined effects of reflection and absorption, the A20M40 sample achieved an average EMI SE of 78.1 dB in the X-band, meeting the EMI shielding requirements for both civilian and military applications. Additionally, the ANF/MXene/AF composite fabric exhibited excellent electrothermal conversion performance (surface temperature reached 120 °C within 32 s under 5 V) and photothermal performance (surface temperature reached 85 °C after 145 s of exposure to 1500 W/m² light intensity). Furthermore, the flame-retardant performance of the ANF/MXene/AF composite fabric was significantly enhanced compared to the pure AF fabric due to the physical barrier effect of MXene.

1. Introduction

With the development of electronic technology, issues such as electromagnetic interference (EMI) with electronic devices and its impact on human health are becoming more prominent. Aramid fiber (AF), known for its high strength, high temperature resistance, corrosion resistance, and light weight, serves as an indispensable high-performance reinforcement material in fields such as the military, aerospace, and industrial equipment [1]. Developing AF with EMI shielding capabilities can protect military equipment, spacecraft, and electronic devices from EMI, thereby expanding its application range. However, due to the inherent electrical insulation, smoothness, and inert surface properties of AF, there are relatively few reports on the EMI shielding functionality of AF and AF fabric. Most research on enhancing the EMI shielding functionality of AF focuses on coating the fibers with conductive layers. Conductive materials can reduce or eliminate the transmission of electromagnetic waves through mechanisms such as reflection, absorption, and scattering, thus achieving a shielding effect.

Due to their excellent electrical conductivity, high mechanical strength, high-temperature resistance, and good stability, metal materials have important applications in the field of EMI shielding. Tang et al. [2] deposited Ni and Cu onto the surface of AF to form conductive AF with a core–shell structure. The EMI shielding effectiveness (SE) of the prepared Ni/Cu/Ni-coated AF fabric could reach 30 dB. Zhang et al. [3] used a wet process to prepare nonwoven fabrics from Cu and Ni-coated AF. Then, a waterborne polyurethane (WPU) dispersion containing Fe₃O₄ magnetic particles was cast onto the framework of the nonwoven fabric to produce an AF@Ni/Cu/Fe₃O₄/WPU composite film. This composite film exhibited excellent EMI SE in the X-band, achieving 55.8 dB. Li et al. [4] treated AF with oxygen plasma and concentrated sulfuric acid and then used Cu metal organic decomposition ink as a functional coating to graft onto the AF. The resulting Cu/AF fabric exhibited an EMI SE as high as 71 dB. However, the application of metal materials as EMI shielding coatings for AF also presents several challenges. For example, the density of metals is much higher than that of AF, which increases the overall weight of the structure and is disadvantageous for applications requiring lightweight designs. Metal shielding coatings also typically lack sufficient flexibility, limiting their use on surfaces with special shapes and structures. Additionally, in humid, high-temperature, or corrosive environments, metal coatings are prone to oxidation, which leads to a decline in their EMI shielding performance.

Carbon materials, known for their excellent electrical conductivity, light weight, and high strength, have garnered widespread attention in the field of EMI shielding. Lee et al. [5] prepared single-walled carbon nanotube/AF composites with a core–shell structure using an impregnation method. They then fabricated a fabric with an EMI SE of 32 dB in the high-frequency band through a sewing process. The synergistic effect between carbon materials and magnetic materials can further enhance the EMI SE of AF. Wang et al. [6] sprayed magnetic Fe₃O₄ and MXene onto the surface of AF fabric and applied an in situ polymerization method to coat polydimethylsiloxane, ensuring a strong bond between Fe₃O₄, MXene, and the fabric, thereby extending its service life and imparting excellent hydrophobicity. The EMI SE of the AF fabric reached 40.78 dB. To enhance the interfacial performance between the AF and the conductive layer, Wang et al. [7] treated the AF fabric with an alkaline solution and vacuum plasma to introduce more active groups on the surface, increasing its hydrophilicity. They then used a spraying-drying method to coat MXene on the fiber surface, forming a conductive network. The EMI SE of the single-layer fabric in the X-band reached 35.7 dB. Li et al. [8] performed alkaline etching on the AF fabric and then used in situ polymerization to grow vertically aligned polyaniline (PANI) nanowire arrays on the fiber’s surface. They subsequently used an impregnation method to modify the surface with MXene nanosheets. To further improve the fabric’s durability, they applied a polyetherimide (PEI) layer on the surface. The resulting PEI/MXene/PANI/AF fabric achieved a maximum EMI SE of 31.87 dB.

MXene, as a member of the family of two-dimensional transition metal carbides or carbonitrides, exhibits excellent electrical conductivity, a large specific surface area, superior mechanical properties, and abundant surface functional groups, making it widely studied in the field of EMI shielding fabrics [9,10,11,12]. However, there are still several challenges and issues associated with applying MXene to the surface of AF. On one hand, the EMI SE of AF coated with pure MXene currently reaches a maximum of only 35.7 dB [7], and when combined with Fe₃O₄, it can achieve only up to 40.78 dB [6], limiting its application in fields with higher EMI shielding requirements. On the other hand, due to the smooth surface and strong chemical inertness of AF, the interfacial adhesion between the MXene layer and the fiber is poor. To address this, methods such as plasma treatment and acid–base etching are commonly employed to increase the number of active groups on the AF surface [4,7,8]. However, these methods can damage the AF structure, leading to a reduction in its mechanical properties [1].

Therefore, this research aims to use vacuum-assisted filtration technology to fabricate a layered structure on the surface of AF, incorporating an aramid nanofiber (ANF) interlayer and a MXene conductive layer to achieve EMI shielding functionality for AF fabric (Scheme 1). Leveraging the porous nature of AF fabric, the vacuum-assisted filtration method is employed to deposit MXene nanosheets onto the surface of AF fabric. This method not only avoids damaging the AF structure but also enhances the adhesion between the conductive layer and AF fabric compared to spraying or dip-coating methods. Moreover, it is easy to operate and suitable for large-scale production. The use of ANF as the interlayer serves a dual purpose: on one hand, it can fill the larger gaps in the AF fabric, facilitating efficient MXene filtration; on the other hand, the structural similarity between ANF and AF enables strong interactions through hydrogen bonding and π-π stacking with the AF fabric, while the nanofiber structure of ANF increases the surface roughness of the fabric, promoting more hydrogen bonding between the hydroxyl groups on the MXene surface and the AF matrix, thereby enhancing the interfacial adhesion between MXene and AF fabric. In this study, the surface and cross-sectional morphology of the composite fabric were characterized using scanning electron microscopy (SEM), and the EMI shielding, electrothermal conversion, photothermal conversion, and flame-retardant properties of the composite fabric were evaluated.

2. Materials and Methods

2.1. Materials

The AF (K49) and AF fabric were provided by DuPont (Wilmington, DE, USA) and TayHo (Yantai, China), respectively. Dimethyl sulfoxide (DMSO) and KOH were purchased from Xilong Scientific Co., Ltd. (Shantou, China). HCl and LiF were supplied by Yantai Far East Fine Chemicals Co., Ltd. (Yantai, China) and Sinopharm Chemical Reagent Co., Ltd. (Shanghai, China), respectively. Ti₃AlC₂ powder was obtained from Ningbo Jinlei Nanomaterials Technology Co., Ltd. (Ningbo, China).

2.2. Preparation of ANF

The AFs were cut into approximately 1 cm segments, sequentially washed with acetone and ethanol in a Soxhlet extractor for 12 h each, and then dried at 60 °C for future use. A total of 4.0 g of AF, 16 mL of deionized water, 4.0 g of KOH, and 400 mL of DMSO were added to a round-bottom flask and stirred vigorously at room temperature for 6 h, resulting in a dark red ANF/DMSO dispersion with an ANF concentration of 9.6 mg/mL. DMSO was then added to dilute the ANF concentration to 2.4 mg/mL. Finally, five times the volume of deionized water relative to the ANF/DMSO dispersion was added, and the mixture was subjected to high-energy sonication for 15 min using an ultrasonic cell disruptor, resulting in a light yellow ANF/DMSO/H₂O dispersion with an ANF concentration of 0.4 mg/mL.

2.3. Preparation of MXene

First, 3.2 g of LiF was added to a polytetrafluoroethylene container containing 40 mL of 9 mol/L HCl solution. The mixture was magnetically stirred for 20 min to dissolve the LiF. Then, 2 g of Ti₃AlC₂ was slowly added, and the mixture was stirred at 45 °C for 24 h to carry out the etching process. After etching, the mixture was centrifuged at 4000 rpm, and the precipitate was washed until the pH of the supernatant became neutral. The washed precipitate was mixed with a certain volume of deionized water and transferred to a three-neck flask. Nitrogen gas was introduced as a protective atmosphere, and the mixture was ultrasonicated in an ice-water bath at a frequency of 40 kHz for 2 h to facilitate delamination. Finally, the mixture was centrifuged at 5000 rpm for 40 min, and the upper-layer MXene dispersion was collected and sealed for storage. A certain volume of the MXene dispersion was dried and weighed, yielding an MXene concentration of 8.0 mg/mL.

2.4. Preparation of ANF/MXene/AF Composite Fabric

The AF fabric, after being washed with acetone and ethanol and then cut into circles with a diameter of 4 cm, was placed into a sand core filter for vacuum-assisted filtration to prepare the ANF/MXene/AF composite fabric. First, 20 mL of ANF dispersion was added to the filter for filtration, followed by the addition of varying volumes of MXene dispersion (0, 10, 20, 30, and 40 mL) for filtration. Finally, the composite fabric was dried at 45 °C for 4 h. The ANF/MXene/AF composite fabrics prepared with 20 mL of ANF dispersion and different volumes of MXene dispersion were named A20M0, A20M10, A20M20, A20M30, and A20M40, respectively.

2.5. Characterization

The microstructure of MXene and AF was characterized using a high-resolution field emission transmission electron microscope (TEM), Talos F200X G2, produced by Thermo Fisher Scientific, Waltham, MA, USA. SEM imaging was conducted using the MIRA LMS field emission scanning electron microscope from TESCAN, Brno, Czech Republic, with an accelerating voltage of 3 kV for morphology imaging and 15 kV for mapping, employing the SE secondary electron detector. Prior to testing, samples were gold-coated for 45 s using the Quorum SC7620 sputter coater. X-ray diffraction (XRD) measurement was performed using a SmartLab SE X-ray diffractometer from Rigaku, Tokyo, Japan, with a scanning range of 5° to 65° and a scanning speed of 5°/min. Fourier transform infrared (FTIR) spectroscopy was carried out using the Nicolet iS50 spectrometer from Thermo Scientific, Waltham, MA, USA. The thermoelectric conversion performance was tested using a DC power supply, while the photothermal conversion performance was evaluated using a BBZM-1 xenon lamp from Bobei Lighting, Xuancheng, China. Real-time surface temperature monitoring during thermoelectric and photothermal tests was conducted using an FLIR ONE PRO infrared thermal camera from Teledyne FLIR, Wilsonville, OR, USA. The EMI shielding performance of the composite fabric was tested in the 8.2–12.4 GHz (X-band) frequency range using a ZNB20 vector network analyzer from Rohde & Schwarz, Munich, Germany. Scattering parameters (S₁₁ and S₂₁) were obtained using the waveguide method, and the reflection coefficient (R), transmission coefficient (T), reflection EMI shielding effectiveness (SE_R), absorption EMI shielding effectiveness (SE_A), multiple internal reflections (SE_M), and total EMI shielding effectiveness (SE_T) were calculated based on Equations (1)–(5).

$$R={\left|S_{11}\right|}^2$$

(1)

$$T={\left|S_{21}\right|}^2$$

(2)

$${\mathit{SE}}_R=-10\lg (1-R)$$

(3)

$${\mathit{SE}}_A=-10\lg ({\displaystyle \frac{T}{1-R}})$$

(4)

SE_T = SE_A + SE_R + SE_M

When SE_T ≥ 10 dB, the SE_M can be negligible.

3. Results and Discussion

3.1. Microstructure of ANF and MXene

The ANF was prepared by deprotonating AF. As shown in Figure 1a, the ANF exhibits a fibrous structure with a diameter ranging from approximately 8 to 25 nm. Further, the chemical structure of ANF was characterized by FTIR spectroscopy (Figure 1f). Characteristic peaks at 3320, 1644, 1507, and 1302 cm⁻¹ correspond to the stretching vibrations of N-H, C=O, C=C, and Ph–N, respectively. Additionally, peaks at 1540 and 1255 cm⁻¹ are attributed to the bending vibrations of C–N and N–H. These results indicate that ANF retains the backbone structure of the AF, which consists of aromatic rings and amide bonds [13,14].

Ti₃AlC₂ was etched using LiF and HCl, and the SEM images before and after etching are shown in Figure 1b and Figure 1c, respectively. As seen in Figure 1b, Ti₃AlC₂ exhibits a three-dimensional densely stacked bulk structure. After etching, the Al atomic layers are removed, resulting in a layered accordion-like structure (Figure 1c), indicating the successful etching of Ti₃AlC₂ into Ti₃C₂T_x MXene. Upon ultrasonic dispersion, the accordion-like Ti₃C₂T_x MXene transforms into single-layer MXene nanosheets, as shown in Figure 1d, which display a thin and transparent morphology. The MXene was further characterized by XRD. As seen in Figure 1e, Ti₃AlC₂ shows a sharp diffraction peak at 2θ = 38.68°, corresponding to the (104) plane [15]. This peak disappears after etching, as the Al atomic layers are removed. A sharp diffraction peak corresponding to the (002) plane is observed at 2θ = 9.5° for Ti₃AlC₂, while in the MXene diffraction pattern, the (002) peak shifts to 2θ = 6.2°, indicating that the interlayer spacing of MXene is expanded after etching and delamination compared to Ti₃AlC₂ [16,17]. The chemical structure of the MXene nanosheets was further characterized by FTIR spectroscopy. As shown in Figure 1f, characteristic peaks at 3449, 2924, and 592 cm⁻¹ correspond to the stretching vibrations of –OH, C–H, and Ti–O groups, respectively [16,18,19].

3.2. Morphology of ANF/MXene/AF Composite Fabric

Figure 2a shows photographs of the surface and bending state of the ANF/MXene/AF composite fabrics. It can be observed that the MXene coating is uniformly applied to the surface of the AF, and when the composite fabric is bent, the MXene coating does not exhibit cracking or delamination. SEM was further employed to characterize the surface morphology of the ANF/MXene/AF composite fabric. As shown in Figure 2b, the surface of the pure AF fabric is smooth, with some gaps between the fibers. After a certain amount of ANF was deposited on the surface of the AF fabric (Figure 2c), these gaps were partially filled by the nanofiber-like ANF, which formed a strong connection with the fabric through hydrogen bonding. Further deposition of varying amounts of MXene (Figure 2d–g) resulted in the formation of a uniform and continuous MXene layer on the fabric surface, suggesting that once the gaps in the fabric were filled by ANF, the MXene nanosheets could be effectively retained on the surface during the vacuum-assisted filtration process. It was also observed that the dark-colored MXene dispersion became colorless and transparent after filtration, which confirmed the retention of MXene nanosheets on the fabric surface. Elemental mapping of the A20M30 fabric surface (Figure 2f’) indicates a uniform distribution of Ti, C, O, and N across the surface, with Ti providing evidence of the uniform dispersion of MXene. Figure 2g shows that the MXene layer is uniformly and continuously deposited over large areas of the fabric surface, even at the intersections of the warp and weft, where the gaps are relatively large. Figure 2h and Figure 2h’ show the cross-sectional morphology and high-magnification images of the A20M20 sample, respectively. It can be seen that the ANF/MXene composite film has a uniform thickness of approximately 8 μm. From Figure 2h’, it is apparent that the ANF/MXene composite film adheres tightly to the AF fabric, which is likely attributed to the ability of MXene to form strong hydrogen bonds with both ANF and the fabric. Additionally, the large specific surface area and numerous surface functional groups of ANF provide more active sites, further enhancing the interaction between MXene and the fabric.

3.3. EMI Shielding Performance of ANF/MXene/AF Composite Fabric

The EMI shielding performance of ANF/MXene/AF composite fabrics was tested. As shown in Figure 3a,b, with the increase in the MXene coating amount, the EMI SE of the composite fabric gradually increased in the X-band (8200–12,400 GHz). Specifically, the average SE_T of A20M30 is approximately 39.2 dB, which meets the standard for civilian EMI shielding. Meanwhile, the average SE_T of A20M40 reaches 78.1 dB, which satisfies the requirements for military-grade EMI shielding. This demonstrates that the ANF/MXene/AF composite fabric exhibits excellent EMI shielding performance, significantly surpassing other functionalized AF fabrics reported in the literature [2,4,5,6,7,8].

The EMI shielding mechanism of the ANF/MXene/AF composite fabric primarily involves two modes: absorption and reflection. Figure 3b presents the average SE_A and SE_R of different samples. As the MXene coating amount increases, both SE_A and SE_R values gradually rise, with SE_A always higher than SE_R for all samples, indicating that absorption loss dominates. Figure 3c further elucidates the EMI shielding mechanism of the ANF/MXene/AF composite fabric. When electromagnetic waves are incident on the surface of the composite fabric, a portion of the electromagnetic waves is reflected by the surface electrons of MXene or emitted due to the impedance mismatch between MXene and air, subsequently escaping into the external space [7,20]. Another portion of the electromagnetic waves penetrates into the interior of the composite fabric, where the abundant free electrons on the surface of MXene interact with the electric field component of the electromagnetic wave, generating currents that cause ohmic loss, thus weakening the intensity of the electromagnetic waves. Additionally, due to the large specific surface area and layered structure of MXene, the electromagnetic waves entering the composite fabric undergo multiple reflections or scattering between the MXene layers, further dissipating their energy. Therefore, with the increase in the number of MXene layers, the absorption loss of electromagnetic waves also increases. Simultaneously, some of the electromagnetic waves that enter the composite fabric are reflected back to the external space after multiple reflections, and this reflection also increases with the number of MXene layers, leading to a higher reflection loss as the MXene coating amount increases.

3.4. Electrothermal Conversion Performance of ANF/MXene/AF Composite Fabric

The electrothermal conversion performance of the ANF/MXene/AF composite fabric was evaluated by recording the surface temperature changes over time at different applied voltages using an infrared thermography camera. As shown in Figure 4a, at a voltage of 5 V, all samples, except for A20M10, exhibited an increase in surface temperature, which eventually stabilized. Notably, the A20M40 sample reached 120 °C within 32 s of power application and stabilized shortly thereafter. The steady-state temperatures at the surface of the A20M10, A20M20, A20M30, and A20M40 composite fabrics under 5 V were 23 °C, 50 °C, 78 °C, and 128 °C, respectively. This demonstrates that, as the amount of MXene increases, the composite fabric exhibits enhanced photothermal conversion performance. According to Joule’s law, the higher the applied DC voltage, the more thermal energy is converted, resulting in higher achievable temperatures for the heating element. Furthermore, the surface temperature changes of the A20M40 sample at different voltages were tested, as shown in Figure 4b. At 1 V, 2 V, 3 V, 4 V, and 5 V, the steady-state surface temperatures of A20M40 were 23 °C, 34.5 °C, 55° C, 95 °C, and 128 °C, respectively. This result confirms that A20M40 can effectively meet the heating requirements of wearable heaters. Figure 4c presents infrared images of the A20M40 sample at 100 s under different voltages, showing a relatively uniform temperature distribution across the sample. Figure 4d illustrates the relationship between the input voltage squared (U²) and the corresponding steady-state temperature, with a strong linear correlation observed. This suggests that the heating process can be controlled by adjusting the input voltage. Figure 4e shows the surface temperature–time curve of A20M40 under cyclic voltage applications of 2 V and 4 V. As seen from the graph, the highest surface temperature of the sample at 4 V remains stable without significant decay after 60 s, demonstrating excellent cyclic stability.

3.5. Photothermal Conversion Performance of ANF/MXene/AF Composite Fabric

MXene exhibits strong light absorption capabilities and can almost completely convert absorbed light energy into heat [21], making MXene-modified materials highly promising in photothermal conversion applications such as seawater desalination [22], wastewater purification [23], and sterilization systems [24]. To explore the potential applications of ANF/MXene/AF composite fabric, this study investigates the photothermal conversion performance of the composite fabric. A xenon lamp was used to simulate sunlight, and a solar radiation meter was employed to measure the irradiation power density. Figure 5a shows the temperature–time curves and corresponding infrared images of different samples under an irradiation power density of 1500 W/m². It can be observed that, as irradiation time increased, the surface temperature of all samples first rose and then stabilized. Moreover, with increasing MXene content, the rate of temperature rise became more pronounced. For the A20M40 sample, the surface temperature reached 85 °C within 145 s of irradiation. After 300 s of irradiation, the temperatures of the A20M10, A20M20, A20M30, and A20M40 samples were 68 °C, 77 °C, 82 °C, and 89 °C, respectively. Figure 5b presents the temperature–time curves of the A20M30 sample under different irradiation power densities. As the irradiation power density increased, the surface temperature of the sample at 300 s reached 37 °C, 57 °C, 82 °C, and 107 °C, respectively. Figure 5c further demonstrates that the temperature increases linearly with the irradiation power density, suggesting that the photothermal performance of the composite fabric is controllable. To test the cyclic performance of the composite fabric, the surface temperature–time curve of the A20M30 sample was recorded during cyclic light on/off processes (Figure 5d). The results indicate that the surface temperature of the sample did not decay after each 60 s light exposure, demonstrating excellent repeatability and stability of the composite fabric’s photothermal performance.

3.6. Flame Retardancy of ANF/MXene/AF Composite Fabric

Due to the repetitive aromatic ring units in the polymer backbone, aramid fibers exhibit certain heat resistance and flame retardancy. In this study, the flame retardancy of pristine AF fabric and A20M30 composite fabric was compared using a vertical burning test (Figure 6). When the pristine AF fabric was exposed to an alcohol lamp flame for 90 s, approximately half of the fibers had already undergone carbonization. In contrast, the composite fabric exhibited a significantly lower degree of carbonization after the same duration, indicating superior flame retardancy of the composite fabric compared to the pristine AF fabric. The enhancement in flame retardancy can primarily be attributed to the two-dimensional nanosheet structure of MXene, which forms a protective layer during combustion. This protective layer acts as a barrier, isolating the fabric from oxygen and heat, thereby slowing down the spread of flames and the transfer of heat. Furthermore, as the burning process progresses, the thermal decomposition of MXene forms a stable and dense TiO₂ layer along with a carbonized layer, which provides additional physical shielding and helps suppress flame propagation [7,25,26,27].

To conclude, the ANF/MXene/AF composite fabric offers excellent EMI shielding performance, effectively protecting aerospace equipment and wearable devices from EMI. Its electrothermal and photothermal properties also make it ideal for smart clothing and heating devices, enabling precise temperature control. Additionally, the flame-retardant nature of aramid fibers further enhances the safety of the equipment.

4. Conclusions

In this study, a series of ANF/MXene/AF composite fabrics were fabricated by layer-by-layer deposition of ANF and MXene on the surface of AF fabric using vacuum-assisted filtration technology. ANF, as an interlayer, can not only achieve efficient filtration of MXene but also provide more active sites to enhance the interface interaction between MXene and AF. Due to the excellent conductivity and nanosheet structure of MXene, electromagnetic waves can be reflected and absorbed by the MXene layer. As a result, the ANF/MXene/AF composite fabric exhibits outstanding electromagnetic shielding performance, with average SET of 39.2 dB and 78.1 dB for the A20M30 and A20M40 samples, respectively, meeting the requirements for electromagnetic shielding in both civilian and military applications. At a voltage of 5 V, the steady-state temperature on the surface of the A20M40 composite fabric can reach 128 °C, with heating performance controllable by adjusting the input voltage, as well as good cycling stability; thus, the ANF/MXene/AF composite fabric shows potential for use as a wearable heater. Moreover, the ANF/MXene/AF composite fabric exhibits excellent photothermal conversion performance. Under an irradiation power density of 1500 W/m² for 300 s, the temperatures of the A20M10, A20M20, A20M30, and A20M40 samples reach 68 °C, 77 °C, 82 °C, and 89 °C, respectively, while maintaining good controllability and cycling stability. Finally, due to the physical barrier effect of MXene, the flame retardancy of the ANF/MXene/AF composite fabric has been significantly improved compared to the pristine AF fabric. In conclusion, the ANF/MXene/AF composite fabric developed in this study demonstrates superior EMI shielding performance, as well as good electrothermal conversion, photothermal conversion, and flame-retardant properties, which could further expand the potential applications of AF fabrics.