Ultra-flexible trilaminar aramid fiber based ANF(Ag/Fe3O4-CNT/rGO) hybrid membrane for high- performance electromagnetic interference shielding

doi:10.21203/rs.3.rs-2110955/v1

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Ultra-flexible trilaminar aramid fiber based ANF(Ag/Fe3O4-CNT/rGO) hybrid membrane for high- performance electromagnetic interference shielding

https://doi.org/10.21203/rs.3.rs-2110955/v1

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With the proliferation of modern integrated electronic and telecommunication systems, high-performance electromagnetic interference (EMI) shielding materials with flexibility, outstanding thermal conductive properties and superior EMI shielding performances are designed to solve the problems of electromagnetic radiation and heat accumulation. Herein, flexible asymmetric trilaminar architecture film with good mechanical properties is prepared via the facile three-step vacuum-assisted filtration (VAF) followed by hot-pressing approach, which is composed of silver-plated aramid nanofibers (ANF-Ag), ANF- Fe₃O₄&CNT (ANF-FC) and ANF-reduced graphene oxide (ANF-rGO) layers. The conductive ANF-Ag and ANF-rGO layers acted as the EMI shielding, thermal conductive layers, and supporting substrate layers. The magnetic ANF-FC layer played the role in synergistically enhancing the EMI shielding performance. The resultant flexible and asymmetric trilaminar hybrid membrane exhibited maximum thermal conductivity of 8.5 W·m^-1K^-1 and EMI SE of 67.5 dB, but also maintained a high tensile strength of 75.5 MPa and superb electrical conductivity of 2.46×10⁶ S/m. This asymmetric trilaminar structures film holds great promise to addresses issues of electromagnetic radiation and heat accumulation for personal smart electronic devices, wearable electronics, electronic telecommunication systems.

Aramid nanofiber

Silver-plated

Asymmetric trilaminar structures

Electromagnetic interference shielding

Thermal conductivity

The popularization of wireless communication and personal electronic devices not only brings great convenience to our life, but also brings some adverse effect such as electromagnetic radiation pollution and interference with surrounding electronic devices, and even a potential threat to human health [1–5]. Hence, it’s essential to develop electromagnetic interference (EMI) shielding materials to eliminate undesirable EMI radiation. Although traditional metal materials have been extensively applicated owing to their satisfactory EMI shielding effectiveness (SE) and excellent electrical conductivity, the practical applications in subtle electronics and many harsh circumstances are limited by their poor chemical corrosion resistance, high density, non-flexibility and narrow shielding frequency range [6–12]. Recently, conductive polymer composites have been extensively investigated for lightweight EMI shielding and thermal interface materials, which have many advantages of corrosion resistance, light weight, elasticity, and low cost [13–16].

Polymers (e.g., plastic [17], rubber [18], fiber [19]) are treated as ideal matrices for modern high-efficiency EMI shielding materials. Among them, aramid nanofiber fiber (ANF) has a negative surface charge, easily forming a strong binding force with other nanocomposites. Generally, conductive particles (e.g., silver nanowire [20–22], graphene [23, 24], carbon nanotube [25, 26] and MXene [27, 28]) or magnetic particles (e.g., cobalt oxide [29, 30], iron oxide [31, 32]) are mechanically mixed with polymers to build a conductive network or magnetic layer in the polymer matrix to achieve satisfactory EMI shielding performance. For instance, Hu et al [33] successfully prepared lightweight, highly conductive and hydrophobic ANF/CNT aerogel films by deprotonation, freeze drying and fluorocarbon resin coating, which exhibited superior electrical conductivity of 230 S/m, EMI SE of > 54 dB over the X-band at the thickness of 568 µm and water contact angle of 137.0°. Haoran Cheng et al.³⁴ prepared Carbon Nanotubes (CNTs) or Graphenes (GNPs) filled PVDF/Fe₃O₄ composites by solution processing and compression molding method. As a result, 8 wt% CNTs and GNPs filled PVDF/Fe₃O₄ composites with high electrical conductivity of 5.9×10^− 3 S/cm and 2.1×10^− 2 S/cm, and superior EMI SE of 32.7 dB and 35.6 dB at a thickness of 1.1 mm.

However, the loading amount and dispersion of absorbing agent are the key to determine the properties of polymer EMI shielding materials. The mechanical properties and flexibility of materials will be readily affected due to high load and low dispersion³⁵. In order to obtain EMI shielding materials with better comprehensive performance, reasonable structural design is fairly significant.^36–41 In the previous report of Yi Li et al.⁴², the alternate multilayer structures of nanofibrillated cellulose/Fe₃O₄&carbon nanotube/Polyethylene oxide (NFC/FC/PEO) films exhibited high conductivity of 3.9×10³ S/m, excellent thermal conductivity of 9.53 W·m^− 1·K^− 1, outstanding EMI SE of 30.3 dB at a thickness of 150 µm and superior mechanical properties (tensile strength of 36.03 MPa, toughness of 2.98 MJ/m³, and elongation at break 19.1%). Similarly, Zhonglei Ma et al.⁴³ fabricated ANF-MXene/AgNW nanocomposite papers with double-layered structures. At the MXene/AgNW content of 20 wt%, the ultra-flexible double-layered nanocomposite papers exhibit outstanding mechanical properties with a tensile strength of 235.9 MPa and fracture strain of 24.8%, as well as superior EMI SE of 48.1 dB and high EMI SE/t of 10688.9 dB·cm^− 1. In addition, due to the multiple attenuation mechanism of electromagnetic waves in space, the high porosity foam structures provide internal multiple reflection space for electromagnetic waves^{44, 45}. Yi Zhang et al employed graphene oxide to prepare an ultralight, highly compressible and broadband and tunable high-performance EMI graphene foam (GF), which had ultrawide qualified frequency bandwidth (RL ≤ -10 dB) of 60.5 GHz under 90% compressive strain⁴⁶. Compared with porous structures, investigations of multilayered structures exhibiting excellent mechanical and EMI SE properties are more meaningful. In this work, the three-layer structure with conductive layer, magnetic layer and thermal conductive layer were innovatively designed. Silver-plated ANF/ANF-Fe₃O₄&CNT/ANF-reduced graphene oxide ANF-(Ag/FC/rGO)) film was constructed via the facile three-step VAF followed by hot-pressing approach. The ANF-Ag and ANF-rGO layer provided the composite films with superb electrical conductivity, outstanding EMI SE, excellent thermal conductivity and maintained mechanical properties. The introduction of magnetic FC particles could increase the absorption of electromagnetic wave and further synergistically improve the EMI shielding performance. Therefore, this work provides a paradigm for designing and constructing flexible and tough composite films with both excellent EMI shielding performance and satisfactory heat removal ability.

2.1. Materials

Kevlar 29 thread was purchased from DuPont, USA. Nano ferroferric oxide (Fe₃O₄, 99%) with the average diameter of 20 nm was obtained from Shanghai Aladdin Biochemical Technology Co., Ltd., China. Multi-walled carbon nanotube (CNT, 90%, length less than 30 µm, external diameter of 10–20 nm) and monolayer graphene oxide (GO, 95%, slice diameter of 0.5-5 µm, thickness of 0.8-1.2nm) were provided by Jiangsu Xianfeng Nano Material Technology Co., Ltd., China. Chemicals including dimethyl sulfoxide (DMSO, AR), potassium hydroxide (KOH, AR), L-Ascorbic acid (LA, 99%), D-(+)-Glucose (DG, 99%), ammonium hydroxide (AH, 2.5%, vol%), silver nitrate (AgNO₃, 99%) were purchased from Shanghai Aladdin Biochemical Technology Co., Ltd., China.

2.2. Preparation of ANF

2.0 g of Kevlar 29 thread and 3 g of KOH were added into 500 mL of DMSO in a round-bottomed flask, and the mixture was magnetically stirred at 50℃ for 7 days. A translucent and red-brown ANF dispersion was obtained, owing to deprotonation and dissociation of macroscopic aramid thread. The ANF dispersion was prepared into homogeneous aqueous dispersion by adding deionized water and ultrasonication.

2.3. Preparation of asymmetric trilaminar nanocomposite membranes

Firstly, the ANF-Ag was prepared by Sliver Mirror Reaction. Briefly, a certain concentration of AgNO₃ were added into the aqueous ANF dispersion (40ml) with a concentration of 0.5mg/ml. After mixing evenly, AH with a concentration of 2.5% were added until the precipitate exactly dissolved, then 10ml DG solution with a concentration of 5wt% were added. Subsequently, the processed ANF dispersion were put in a 50 ℃ oven for 30 minutes to acquire ANF-Ag. Secondly, the magnetic layer was prepared by fully mixing FC with ANF dispersion. Typically, mixture of nano Fe₃O₄ and CNT were added into DMSO with sonicating in an ice bath for 20 minutes. In these cases, the weight ratio of Fe₃O₄ and CNT was set as 2:1. Then 40ml ANF dispersions (0.5mg/ml) were added the FC suspension and sonicated for 20 minutes to acquire the FC/ANF suspension. Thirdly, in order to fabricate ANF-rGO layer, 2mg/ml GO (5ml) aqueous dispersion were added into 40ml aqueous ANF dispersion (0.5mg/ml). After sonicated for 15min, 3ml LA solution with a concentration of 1wt% were added dropwise. Then the processed brown ANF/GO dispersion was reduced into black ANF-rGO after disposed at 95 ℃ for 2h. Finally, the trilaminar nanocomposite membranes were fabricated layer by layer VAF of ANF-Ag, ANF-FC and ANF-rGO, and dried under hot-pressing at 50°C and 1 MPa for 48h.

To explore the effects of AgNO₃ solutions concentrations on the electrical conductivity and EMI shielding performance, asymmetric trilaminar structures films with AgNO₃ solutions concentrations of 10mg/ml, 30mg/ml, 50mg/ml and 70mg/ml were prepared. In these cases, the ANF-rGO layer remains the same, while that the middle layer does not add mixture of FC. For the sake of brevity, the resulting asymmetric trilaminar structures nanocomposite films were labeled as ANF-(Ag_χ/rGO), where χ was defined as concentrations of AgNO₃ contents. Similarly, a series of FC mixtures (5%, 10%, 20% and 30% of the total AFN mass) were employed. In these cases, the ANF-rGO layer remains the same and the ANF-Ag layer remains AgNO₃ with a concentration of 70mg/ml. For the sake of brevity, the resulting asymmetric trilaminar structures nanocomposite were labeled as ANF-(Ag₇₀/FC_ψ/rGO), where ψ was defined as FC contents.

2.4 Characterizations

Scanning electron microscopy (SEM) images and Energy dispersive spectrum (EDS) mappings of the ANF-(Ag/FC/rGO) films were taken on a ZEISS Sigma 300 SEM (Germany). XRD spectra of samples were recorded by Bruker D8 advance X-ray diffractometer (Cu Kα radiation, λ = 0.154 nm, Germany) with a scanning speed of 5°/min from 5° to 90°. The volume resistivity of films was measured on a four-point probe resistivity determiner (280SI, Four Dimensions, USA). The vector network analyzer (VNA, N5244A, Agilent Technologies, USA) was employed to investigate the scattering parameters (S_ij) of such multilayered films. From S11 and S21, the power coefficient of reflectivity (R), transmissivity (T), and absorptivity (A), the total EMI SE (SE_T), reflection (SE_R), and absorption (SE_A) can be calculated as follows:

$$R={\left|{S}_{11}\right|}^{2}={\left|{S}_{22}\right|}^{2},T={\left|{S}_{12}\right|}^{2}={\left|{S}_{21}\right|}^{2}$$

$$A=1-R-T$$

$${S}_{T}=10log\frac{1}{T}$$

$${S}_{R}=10\text{l}\text{o}\text{g}\left(\frac{1}{1-R}\right)$$

$${S}_{A}=10log\frac{1-R}{T}$$

$${S}_{T}={S}_{R}+{S}_{A}$$

Mechanical properties of three-layer films were tested by a universal testing machine (CMT8502, SANS, USA) with a tensile speed of 1 mm/min. An average value of at least 5 tests was taken for each sample. Thermal conductivities were obtained by the equation $\lambda =\alpha \times {C}_{p}\times \rho$, where the λ (W∙m^− 1K^− 1), α (mm²∙s^− 1), C_p (J∙g^− 1K^− 1) and ρ (g∙cm^− 3) represented thermal conductivity, thermal diffusivity, heat capacity and material density, respectively. Laser flash apparatus (LFA 467, NETZSCH, Germany) was employed to characterize the thermal diffusivities and heat capacity of the films.

Schematic diagram was exhibited in Fig. 1, in which ANF-(Ag/FC/rGO) film was fabricated via the facile three-step vacuum-assisted filtration following by hot-pressing approach. Step one, the silver gray ANF-Ag was prepared by Sliver Mirror Reaction, being VAF (VAF I) onto a nylon porous membrane (diameter: 47 mm, pore size: 0.22 µm). Step two, the ANF-FC layer was VAF onto the ANF-Ag layer (VAF Ⅱ) afterwards. Step three, the ANF-rGO layer was VAF onto the ANF- FC layer (VAF Ⅲ). Finally, the trilaminar nanocomposite membranes were completely dried under hot-pressing, due to the hydrogen bonding, the trilaminar nanocomposite film will be tightly combined.

To visually observe the morphology and microstructures of the asymmetric trilaminar structures films, SEM characterizations were systematically performed. As shown in Fig. 2a, the asymmetric trilaminar architecture of ANF-(Ag₇₀/FC₃₀/rGO) films could be clearly identified by the distinct structures and morphology of the one ANF-Ag, ANF-FC and ANF-rGO layer. ANF-Ag and ANF-rGO layer displayed dense lamellar microstructures with slight undulation, and a few gaps inside, which was attributed to the air bubbles generated by the laminated film were not emptied in time. However, the hollow structures were conducive to the absorption of electromagnetic waves^{47, 48}. The ANF-FC layer presented a compact morphology, due to the FC particles were filled with ANF net. In order to further observe the bonding between layers, the interface junctions were scanned. Figure 2b and c shown the binding between ANF- FC layer and ANF-Ag and ANF-rGO, respectively. Whether ANF-FC and ANF-Ag or ANF-rGO, the interfaces were closely combined without visible delamination, owing to the hydrogen bonding between the layers^{21, 49}. The high magnification SEM images of ANF-Ag, ANF-FC and ANF-rGO layers exhibited in Fig. 2d-f illustrated their different structural forms. As shown in Fig. 2d, Ag was uniformly attached to the surface of ANF in the form of clusters and closely filled the gap of ANF, which is the key to the construction of conductive and heat conduction pathways. Figure 2e shown that Fe₃O₄ was distributed in the network interleaved by CNT and ANF. As shown in Fig. 2f, the highly aligned lamellar microstructures of the ANF-rGO indicated graphene and ANF were integrated, which was of great benefit to the mechanical properties and thermal conductivity of the composite film. Since the dispersion of the particles in the ANF matrix is crucial to the performance of the ANF composite film, the element distribution of the composite membrane was characterized. The element mappings exhibited in Fig. 2 (g, h and i) illustrated the selective distribution of Ag, Fe and C elements in ANF-Ag, ANF-FC and ANF-rGO layers respectively, which further validated the successful construction of the asymmetric trilaminar architectures in composite films. In addition, Ag elements were densely and evenly distributed in the top layer (Fig. 2g) and C elements were distributed in each layer (Fig. 2i). It is worth noting that the C element signals in the top layer were weak, owing to the silver-plating layer completely covered the ANF surface and the C element signals were shielded, which further proves the compactness and uniformity of the silver-plating layer. Fe elements (Fig. 2h) were evenly distributed in the middle layer without obvious agglomeration, which further improves the EMI shielding performance of the composite film.

The XRD patterns were utilized to analyze the crystallographic structures of the samples. Figure 3a exhibited the XRD curves of the ANF-Ag₇₀ and ANF-rGO layer compositions. The two diffraction peaks observed at 10.7° and 21.5° for GO were assigned to (001) and (002) planes of typical graphene oxide crystalline structures. In contrast, the diffraction peak of ANF-rGO disappeared at 10.7°, indicating that graphene oxide was completely reduced^50–52. The ANF presented the diffraction peaks at 20° and 30° corresponding to the (110) and (004) crystal planes of ANF, which coincided with previous reports⁴³. The strong peaks situated at 38.1°, 44.3°, 64.4°, 77.5° and 81.5° in Ag XRD curve corresponded to the (111), (200), 220), (311) and (222) planes of Ag crystals. Figure 3b displayed the XRD curve of each component of ANF-FC₃₀ layer. The strong peaks situated at 30.1°, 35.5°, 43.1°, 57.0° and 62.6° in Fe₃O₄ and ANF-FC₃₀ XRD curve corresponded to the (220), (311), (400), (511), and (440) planes of Fe₃O₄ crystals, respectively. In addition, it’s observed that CNT exhibited three conspicuous peaks at 26.6◦ and 42.6◦, owing to (002) and (100) lattice planes of CNT crystalline structures.

The EMI shielding films with fascinating mechanical properties could be used more widely in the practical application. As shown in Fig. 4a, although the tensile strength of asymmetric trilaminar architecture films exhibited a descending tendency with the introduction of FC particles, the tensile strength of ANF-(Ag₇₀/FC₃₀/rGO) still reached up to 75.5 MPa, which was ascribed to the excellent mechanical properties of the ANF-Ag layer and ANF-rGO layer. In order to show the excellent mechanical property of the ANF-(Ag₇₀/FC₃₀/rGO) films more intuitively. The ANF-(Ag₇₀/FC₃₀/rGO) film was withstood a weight of 500 g (Fig. 4b) and folded into the shape of a paper plane without any crack or fracture (Fig. 4c), indicating the excellent strength and flexibility.

In order to explain the performance change of ANF-Ag films from the perspective of structure, SEM characterizations were systematically performed. Figure 5a exhibited the cross-sectional SEM image of pure ANF film. ANF was highly oriented during AVF and formed a loose and stratified structure. As shown in Fig. 5b-d, the section of ANF-Ag films became dense gradually with the increase of AgNO₃ concentrations, due to the silver-plating layer gradually thickens, filling the voids and defects inside ANF, which was an important factor for ANF-Ag to show excellent conductivity. In addition, it could be found from Fig. 5e that the strong peaks situated at 20° and 30° corresponding to the (110) and (004) crystal planes of ANF gradually disappears with the increase of AgNO₃ solutions concentrations, which further proved that the surface of ANF was gradually covered by Ag.

It is acknowledged that the EMI shielding property of materials was closely related to outstanding electrical conductivity. As shown Fig. 6a, like most polymers, ANF film showed excellent electrical insulation. But with the introduction of Ag, ANF-(Ag/rGO) films exhibited the superb electrical conductivity at high concentrations of AgNO₃, the value of electrical conductivity from 9.7×10^− 17 S/m for ANF to striking 2.37×10⁶ S/m for ANF-(Ag₇₀/rGO), the corresponding average EMI SE was tremendously elevated from 0.03 dB to 45.4 dB (Fig. 6b). This phenomenon could be explained by the fact that gradually increasing silver plating on ANF surface provided large area and continuous conductive networks, that could be confirmed by SEM images of ANF-Ag films with different AgNO₃ solutions concentrations (Fig. 5b-d). As shown in Fig. 6b-d, the total EMI shielding properties followed a parallel tendency to the shifting electrical conductivity. Especially, the maximal value of 46.5 dB was reached for the EMI SE of ANF-(Ag₇₀/rGO) corresponding to the reflection efficiency (R-C) has also increased sharply, reaching 0.973.

Unexpectedly, as shown Fig. 7a, the introduction of FC made little contribution to electrical conductivity of the film. Visually, by augmenting FC content from 5wt% to 30wt%, the corresponding electrical conductivity was slightly elevated from 2.38 × 10⁶ S/m to 2.46 × 10⁶ S/m, which was attributed to FC increased the flow path of current-carrying charges, but this has no advantage over silver plating. Moreover, the bright LED lamps (insets) also demonstrate the superb electrical conductivity of the three-ply nanocomposite membranes. In order to estimate the effect of FC content in three-ply architecture films, the EMI shielding performances of ANF-(Ag₇₀/rGO) and ANF-(Ag₇₀/FC/rGO) films with different FC contents were detailly compared. As shown in Fig. 7b, the pure ANF film had extremely low EMI SE of merely 0.003 dB in X-band, which was almost transparent to electromagnetic wave, owing to inherent electrical insulation. In comparison, both ANF-(Ag₇₀/rGO) and ANF-(Ag₇₀/FC/rGO) films displayed the satisfactory EMI shielding performance (༞45 dB), which much higher the demand for commercial EMI shielding materials (> 20 dB in X-band) ⁵³. In detail, the EMI SE maximum values of ANF-(Ag₇₀/rGO) and ANF-(Ag₇₀/FC₃₀/rGO) films were 46.2 and 67.5 dB, respectively. Obviously, total EMI shielding properties can be improved by increasing FC contents, which was attributed to more compact and perfect magnetic networks built by increased FC, contributing to the largely enhanced multiple reflections of the electromagnetic wave between Fe₃O₄ and CNT. In addition, the shielding efficiency of ANF-(Ag₇₀/FC₃₀/rGO) film was as high as 99.99995%, signifying only 0.00005% transmission of the incident electromagnetic wave with 99.99995% blockage.

As shown in Fig. 7c, the average total EMI SE (SE_T), absorbing EMI SE (SE_A) and reflected EMI SE (SE_R) of the X-band were calculated, respectively, to theoretically understand the EMI shielding mechanism of ANF-(Ag/FC/rGO) films. It’s found that SE_A values were a little higher than SE_R values, which was attributed to incremental moving charge carriers with the construction of the conductive network⁵⁴. However, the absorption efficiency (A-C) and reflection efficiency (R-C) of asymmetric trilaminar architecture films in Fig. 7d showed that all the films possessed R-C ≈ 0.98 far larger than A-C ≈ 0.02, indicating the shielding mechanism of the asymmetric trilaminar architecture films was dominated by reflection. This phenomenon could be attributed to the strong reflection of electromagnetic waves by highly conductive films before allowing it to transmit through the surface⁵⁵. Significantly, the A-C was slightly elevated as the FC contents ascended, which authenticated the absorption effect of FC on electromagnetic wave, due to the enhanced multiple reflection and magnetic loss. The shielding mechanism of the asymmetric trilaminar architecture film was schematically depicted in Fig. 8.

It’s well known that outstanding thermal conductivity was a crucial factor for evaluating EMI shielding materials. The thermal conductivity (TC) of the asymmetric trilaminar architecture of ANF-(Ag_70/FC/rGO) films was studied and Fig. 9a described the thickness and thermal conductivity of neat ANF and asymmetric trilaminar architecture films with different FC contents. As a control, the pristine ANF film exhibited the thinnest thickness of 56 µm and poor in-plane TC of only 0.39 W·m^− 1K^− 1. By contrast, the ANF-(Ag₇₀/FC/rGO) films boasted the minimum value of 5.8 W·m^− 1·K^− 1 with 5 wt% FC contents, which was 1387% higher than the pristine ANF film. It was visual that the TC of ANF-(Ag₇₀/FC₃₀/rGO) reached up to 8.5 W·m^− 1K^− 1, which was enhanced by 2079% in comparison with that of pristine ANF film, owing to the perfect thermal conduction pathway constructed by Ag and rGO in ANF-Ag and ANF-rGO layers, respectively. In addition, the FC particles filled the voids of ANF, leading to the intermediate layer denser, and conducing to heat conduction. In order to reflect the progressiveness of our efforts, the comparison of EMI SE and TC in the asymmetric trilaminar architecture of ANF-(Ag₇₀/FC/rGO) films with the reported values of other representative polymeric EMI shielding materials was summarized in Fig. 9b. Obviously, it was quite difficult to possess superb EMI SE and TC for polymer-based composites simultaneously⁴². However, the EMI SE and TC of our ANF-(Ag/FC/rGO) films prevailed over most of reported composites in previous literature, which authenticated that the design idea was valuable and competitive to obtain ANF composite films with excellent comprehensive properties.

In summary, we have successfully prepared flexible and asymmetric ANF-(Ag₇₀/FC₃₀/rGO) trilaminar membrane with excellent thermal conductivity and mechanical properties via the facile three-step vacuum-assisted filtration following by hot-pressing approach. The ANF-Ag and ANF-rGO layers not only provided continuous conductive network for electron and heat conduction, endowing superb electrical conductivity of 2.37 × 10⁶ S/m and thermal conductivity of 8.5 W·m^− 1 K^− 1, but also played a role as the supporting substrate, giving high tensile strength of 75.5 MPa. The ANF-FC layer synergistically enhanced the EMI shielding performance of composite membrane. Remarkably, ANF-(Ag₇₀/FC₃₀/rGO) film exhibited a maximum EMI SE of 67.5 dB, due to the enhanced multiple reflections at the internal interfaces. This investigation provided an efficient strategy into the design and fabrication of flexible and mechanically strong ANF papers with both excellent EMI SE and thermal conductivity, which had considerable prospects in areas such as robot joints, military, and wearable electronics.

Funding

This work was supported by National Natural Science Foundation of China (52101243), “100-level” Innovative Talents Project of Guizhou Province China ([2016] 5653), Natural Science Foundation of Guangdong Province (2020A1515010886) and Science and Technology Planning Project of Guangzhou (202102010373).

Conflict of Interest The authors declare that they have no conflict of interest.

Author's contribution:

Xinwang Gu: Data curation, Writing-original draft. Hongmei Qin: Investigation. Dandan Dong: Formal analysis. Caihong Wang: Visualization. Shengjun Lu: Supervision, Methodology, Resources. Yufei Zhang: Supervision, Data curation. Haosen Fan: Writing - review & editing, Supervision. Jian Xu: Writing - review & editing.

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No competing interests reported.

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Ultra-flexible trilaminar aramid fiber based ANF(Ag/Fe3O4-CNT/rGO) hybrid membrane for high- performance electromagnetic interference shielding

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Abstract

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1. Introduction

2. Experimental Section

2.1. Materials

2.2. Preparation of ANF

2.3. Preparation of asymmetric trilaminar nanocomposite membranes

2.4 Characterizations

3. Results And Discussion

4. Conclusions

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References

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