Fabrication of flexible and durable functional fabric with high electromagnetic shielding performances based on MXene

Abstract

The functional fabric with high electromagnetic shielding (EMI) performance, durability as well as good handle has been drawing increasing attention. Herein, AgNPs@MXene of high conductivity was prepared by in-situ reduction of AgNO₃ onto MXene. Then, boron-enhanced AgNPs@MXene-PDA coating fabric (BAMP-F) of high properties was fabricated through polydopamine (PDA) coating, AgNPs@MXene assembly, and finally sodium tetraborate (Na₂B₄O₇) densification. Results showed that the surface resistivity of AgNPs@MXene arrived at 7.22 × 10⁻⁴ Ω·m and decreased by one order in comparison with pure MXene. After 0.6 mol/L PDA coating, AgNPs@MXene deposition for 6 times, and 0.02 mol/L Na₂B₄O₇ densification, the surface resistivity of BAMP-F reached 7.08 × 10⁻³ Ω·m and its EMI values of one layer attained 34.51 dB. Compared with AgNPs@MXene-PDA coating fabric (AMP-F), the electrical conductivity of BAMP-F improved by 47.6 % and its electromagnetic shielding performance increased by 42.8 %. BAMP-F possessed good handle and maintained excellent EMI performance after bending for 600 times, washing for 60 min, and tearing.

Keywords

MXene nano-silver electromagnetic shielding conductivity

Introduction

Electromagnetic radiation is considered as the fouth environmental pollution following air, water, and sound pollution, which causes serious harm to human being’s health. Electromagnetic shielding fabrics have been attracting much attention due to the flexibility and the protection of people from electromagnetic waves.¹ The primary focus on electromagnetic shielding fabric lies in how to impart excellent conductivity and durability. The construction of electromagnetic shielding fabric with high performances has become a hot topic.

Electromagnetic shielding fabrics primarily rely on the reflection loss to electromagnetic waves. Their conductivity has the positive correlation with the electromagnetic shielding effectiveness.² So far, most of conductive fabrics have been fabricated by the load of conductive materials at one-, two- or three-dimensional states. Based on percolation, tunneling and field-emission effects, the conductive path was formed onto conductive fabric.^3–5 Conductive materials are mainly divided into four categories: metal material,⁶ carbon-based material,⁷ conductive polymer,⁸ and composites.⁹ Though the metal conductive materials (Au, Ag, Cu) possess high conductivity, their adhesion fastness onto fabrics are poor. While carbon-based materials have the problems of dispersion stability and conductive polymers exhibit the lower electrical conductivity. Consequently, the composite of different conductive materials could achieve the best performances.

MXene (M_n+1X_nT_x) was a two-dimensinal transition metal carbonitride, where n was 1–3; molar denotes transition metal; X denotes C or N; T means fuctional groups −OH, −O, −F.¹⁰ MXene shows the theoretical conductivity of 10⁵ S/m. Due to the narrow band-gap semiconductor characteristics, it possesses excellent electromagnetic shielding and photothermal convension functions.^11,12 In addition, the existence of fuctional groups −OH, −O, −F imparts certain hydrophilcity and bonding with other materials via hygrogen bond. Compared with graphene, MXene has not only covalent bond, but also metal bond and ionic bond, which provides the advantages for composite with other materials. The insertion of metal ions can realize the high conductivity of MXene.¹³ Except Li⁺, other ions (Ag⁺, Mg²⁺, Na⁺, NH⁴⁺) can insert between MXene sheets.¹⁴ The strong reducibility of low valent titanium induces the in-situ growth of nano-silver (AgNPs) onto MXene.^15,16 It not only improves the aggregation of AgNPs, but also promotes the electron transimission by means of Ag⁺ insertion. The electromagnetic shielding efficiency presents positive correlations with the materials’ conductivity. At present, the conductivity of MXene has been influenced by the interspace among MXene sheets.¹⁷ In order to further improve the conductive properties of materials, some researchers induced the densification method through bridging bonds.^18,19 Sodium tetraborate (Na₂B₄O₇) can be used for densification of MXene film by the bonding between borate ions and −OH of MXene.²⁰ The MXene lamella touched closer to form a more compact conductive network.

Electromagnetic shielding fabrics on the human body are vulnerable to chemical and mechanical attacks in practice, such as sweat, water, bending, and severe cycle washing.^21,22 These greatly hinder their application in daily use. Electromagnetic shielding fabrics should have flexibility and durability under strong external forces such as bending, tearing, washing, rubbing, and so on. There are always lack of firm adhesion between conductive materials and fabric. Under the action of external forces, conductive materials are easily detached from the fabric surface, which leads to the decrease of conductivity. Moreover, owing to the rough and porous texture of fabrics, it is difficult for conductive material to contact closely and form complete conductive network. Several researches have been carried out to improve the conductivity and fastness of conductive fabrics, including the modification of fabric surface,²³ complex of conductive particle and conductive polymer,²⁴ and in-situ deposition of conductive materials onto fabric.²⁵ Among these methods, modification of fabrics may be the most effective route.²⁶ Polydopamine (PDA) possesses ultra-strong adhesiveness due to the rich hydroxyl and amino groups of its structure.²⁷ Pyrocatechol structure can coordinate with metal ions. Accordingly, it is the best candidate to modify the surface of fabric and further bond the conductive materials.

Herein, AgNPs@MXene was prepared by in-situ reduction of Ag⁺ onto MXene. The conductivity of AgNPs@MXene were optimized. AgNPs@MXene was characterized by XRD, SEM-EDS, TEM, and XPS. Then, boron-enhanced AgNPs@MXene-PDA coating fabric (BAMP-F) was fabricated through PDA coating, AgNPs@MXene assembly, and finally Na₂B₄O₇ densification. Effects of dopimane concentration, impregnation times of AgNPs@MXene, and Na₂B₄O₇ concentration on the conductivity of conductive fabric were investigated. The electromagnetic shielding performance, durability and handle of the conductive fabric were evaluated for the potential application.

Materials and methods

Materials

Titanium carbide (Ti₃AlC₂, 200 mesh) was purchased from Bowarth Nanotechnology Co., Ltd Lithium fluoride (LiF), dopamine hydrochloride (DA), tris(hydroxymethyl)aminomethane, and sodium tetraborate (Na₂B₄O₇) were supplied by Shanghai Macklin Biochemical Technology Co., Ltd Hydrochloric acid (HCl, 37%) was provided by Huadong Medicine Co., Ltd Silver nitrate (AgNO₃) was provided by Changzhou Guoyu Environmental Protection Technology Co., Ltd. All chemical reagents were of analytical grade and used without further purification.

Cotton fabric (yarn count: 40 × 40, warp density: 133 threads/10 cm, weft density: 72 threads/10 cm) which went through scouring, mercerization, and bleaching, was obtained from Shanghai Hualun Printing and Dyeing Co., Ltd.

Preparation of AgNPs@MXene

25 mL HCl was poured into a PTFE beaker. Then 1 g LiF was slowly added into HCl at 45°C under stirring. After 5 min, 1 g Ti₃AlC₂ powder was put in the above solution. After reaction for 36 h, the solution was centrifuged at 3500 r/min for 5 min, washed repeatedly until pH surpassed 6, treated by ultrasound for 40 min, and freeze-dried to obtain MXene powder. Subsequently, MXene podwer was uniformly dispersed in the distilled water. AgNO₃ solution was dripped into MXene dispersion. After stirring for 30 min, AgNPs@MXene dispersion was obtained. The preparation route of AgNPs@MXene is shown in Figure 1a.

Figure 1.

Schematic diagram of preparation for (a) multilayer MXene, (b) few-layer MXene, (c) AMP-F, and (d) BAMP-F.

PDA coating on cotton fabric

Tris(hydroxymethyl)aminomethane and HCl adjusted pH value of the solution to 8.5. Then certain amount of dobutamine hydrochloride were added into the solution. Cotton fabrics were soaked into DA solution and stirred at room temperature for 6 h. Finally, PDA coating cotton fabric was rinsed several times to remove the residual PDA, and dried at 60 °C. PDA coating on cotton fabric was shown in Figure 1b.

Fabrication of conductive cotton fabric

First, the PDA coating cotton fabric were immersed into 19 g/L AgNPs@MXene dispersion liquid for 30 min, and dried at 60°C. The above step was repeated for several times to obtain AgNPs@MXene-PDA coating fabric (AMP-F). Second, AMP-F was impregnated into Na₂B₄O₇ solution at different concentrations for 6 h to make the borate ions fully enter into the fabric. Boron-enhanced AgNPs@MXene-PDA coating fabric (BAMP-F) was gained after drying at 60 °C. The fabrication of AMP-F and BAMP-F was shown in Figures 1(c) and (d). The cotton fabric which was directly treated by AgNPs@MXene dispersion liquid was marked as AM-F.

Characterizations

The morphology of MXene, AgNPs@MXene, and cotton fabric were observed by Field Emission Scanning Electron Microscope (FE-SEM) (Altra 55, Carl Zeiss, German) and analyzed by Transmission Electron Microscope (TEM) (JM-2100, JESCO, Japan). X-Ray Diffraction Spectometry (XRD) (Arl Xtra, Thermo ARL, Switzerland) was used to characterize the Cu Kα radiation (λ = 1.5406 A) at scanning speed of 5 °/min under 40 kV and 200 mA. The energy spectra was determined by X-ray Photoelectron Spectrometer (XPS) (K-Alpha, Thermo Fisher Scientific, USA) equipped with an Al-Ka X-ray source. The functional groups of modified fabric were characterized by Fourier Transform Infrared Spectrometer (Nicolet iS-20, Thermo Fisher, USA). Surface resistivity of the sample was measured using Four-probe Resistance (RTS-9, China). EMI shielding effectiveness (EMI SE) of the circular sample with a diameter of 10 cm was measured via Fabric Electromagnetic Radiation Tester (FY800, China). The washing resistance of the conductive fabric was tested for 10, 20, 30, 40, 50, 60 min by ultrasonic cleaning machine at 240 W (JP-040s, China). The surface resistivity and EMI SE of the conductive fabric was determined after bending for 50, 100, 200, 300, 400, 500, 600 times according to the literature.²² According to AATCC Test Method 202, the hand parameters of the sample were measured through a fabric sensory instrument (PhabrOmeter, Nucybertek, USA).

Results and discussion

AgNPs@MXene with high conductivity

Micro-structure analysis of AgNPs@MXene

MXene was prepared by selective etching and assisted ultrasonic peeling. Then, silver ion was in-situ reduced on MXene in order to further improve the conductivity of MXene. The micro-structure of AgNPs@MXene composite are shown in Figure 2. Compared with Ti₃AlC₂, (104) diffraction peak of MXene almost disappeared and (002) diffraction peak moved towards left (Figure 2(a)). It indicated the removal of Al layers into Ti₃AlC₂ and the increased interlayer spacing between sheets. From XRD spectra of AgNPs@MXene, four new peaks appeared, corresponding to (111), (200), (220) and (311) crystal plane of AgNPs with the face-centred cubic structure. SEM-EDS exhibited the abundant AgNPs on MXene sheets (Figures 2(b) and (c)). The pure MXene sheets possessed the limited conductivity due to the inadequate contact with each other. AgNPs/Ag⁺ could enter into the gap among MXene sheets to enhance the electronic transmission. Consequently, AgNPs@MXene displayed better conductivity than MXene alone. TEM images also demonstrated the successful composite of AgNPs@MXene (Figures 2(d) and (e)). Else, AgNPs had good monodispersion onto MXene. Their size was concentrated on around 50 nm and lattice fringe spacing was 0.24 nm.

Figure 2.

(a) XRD of Ti₃AlC₂, MXene, and AgNPs@MXene; (b) EDS of AgNPs@MXene; (c) SEM images of Ti₃AlC₂ and AgNPs@MXene; (d) and (e) TEM images of AgNPs@MXene and AgNPs.

Conductivity of AgNPs@MXene

The conductivity of AgNPs@MXene at different mass ratios of AgNPs and MXene are displayed in Figure 3a. When the mass ratio of AgNPs and MXene was 3: 10, the sheet resistivity of AgNPs@MXene arrived at the minimum value of 7.22 × 10⁻⁴ Ω·m. Compared with the surface resistivity of pure MXene 5.02 × 10⁻³ Ω·m, the sheet resistivity of AgNPs@MXene decreased by an order of magnitude, which manifested the greater improvement of conductivity. It may be attributed to the filling of AgNPs/Ag⁺ into the interspaces among MXene sheets for the complete conductive path. With the mass ratio of AgNPs and MXene increasing, the sheet resistivity of AgNPs@MXene had the sharp increases. It was attributed to the obvious agglomeration of AgNPs, leading to larger size and uneven distribution of AgNPs. It would affect the improvement of conductivity of AgNPs@MXene.

Figure 3.

(a) Surface resistivity of AgNPs@MXene at different mass ratios of AgNPs and MXene; (b) XPS survey spectra for AgNPs@MXene, MXene and Ti₃AlC₂; (c) Ti 2p spectra for AgNPs@MXene and MXene, (d) Ag 3days spectra for AgNPs@MXene.

To elucidate the possible self-reduction mechanism, the surface composition and chemical states of AgNPs@MXene, MXene, and Ti₃AlC₂ were displayed in Figure 3(b)–(d). Compared with Ti₃AlC₂, F1s and Ag 3D signals were clearly observed in AgNPs@MXene (Figure 3(b)). Seen from Figures 3(c) and (a) distinct peak of MXene at 464.1 eV was classified as Ti(IV) 2p_3/2. From the wide peak of 453–462 eV in MXene, Ti(II) (∼457.4 eV) and Ti(III) (∼461.6 eV) appeared.¹³ The self-reduction process onto AgNPs@MXene made the transformation of Ti (II) and Ti(III) into Ti(IV). It was observed that the peaks of Ti(IV) at ∼460 eV and ∼465 eV.²⁸ At the same time, the representative peaks of Ag 3d_5/2 and Ag 3d_3/2 (Figure 3(d)) were located at ∼ 367.6 and ∼ 373.7 eV, respectively, and cleaved at ∼ 6.0 eV,²⁹ which indicated the successful formation of Ag(0). Almost all the silver particles are in the Ag(0) state, and the peak characteristics of Ag⁺ and Ag²⁺ were not obvious, suggesting the Ag(0) state. It further proved that the low Ti(II) and Ti(III) species had strong reduction activity.

Conductive fabric based on AgNPs@MXene

In order to obtain conductive fabric of high conductivity and fastness, the adhesive layer and conductive layer was incorporated onto the surface of cotton fabric. Conductive fabric was first coated by PDA. Then AgNPs@MXene was assembled onto the surface of PDA modified cotton fabric by Van Der Waals force, hydrogen bond and metal chelation. Finally, AgNPs@MXene-PDA coating fabric was treated by Na₂B₄O₇ to further improve its conductivity.

Effects of dopamine concentration on the conductivity of AMP-F

The structure of PDA has rich amino and hydroxyl groups. Therefore, it shows the strong adhesion ability and can make the firm binding between conductive material and fabric. In addition, the functional groups of PDA coordinated with silver ion of AgNPs, which enhanced the binding of AgNPs@MXene. The concentrations of dopamine influenced the conductivity of AgNPs@MXene-PDA coating fabric (AMP-F).

Figure 4a exhibits the surface resistivity of AMP-F at different dopamine concentrations for one impregnation of AgNPs@MXene. It was found that the surface resistivity of AMP-F decreased, reached the lowest value of 8.96 × 10⁻² Ω·m at 0.6 mol/L dopamine, and then increased. Compared with the surface resistivity of AgNPs@MXene treated fabric (AM-F) 50.4 × 10⁻² Ω·m, the surface resistivity of AMP-F decreased by 82.2 %. It demonstrated that PDA coating contributed to the improvement of conductivity for the conductive fabric based on AgNPs@MXene. It might be attributed to the roughness chang of the fabric’s surface, which was confirmed in SEM images of the fabrics. Seen from Figure 4(c), the surface of cotton fabric after PDA coating became smoother. It was also observed from Figures 4(d) and (e) that AMP-F possessed smoother surface than AM-F. The smoothness of the substrate contributed to the completeness of conductive path formation for conductive materials.³⁰ Accordingly, AgNPs@MXene would form good conductive path on the surface of PDA coating fabric.

Figure 4.

(a) Surface resistivity of AMP-F at different dopamine concentrations for one impregnation of AgNPs@MXene; SEM images of (b) cotton fabric, (c) PDA coating fabric, (d) AM-F, and (e) AMP-F.

Effects of AgNPs@MXene impregnation times on the conductivity of AMP-F

The amount of conductive materials onto the fabric influence the conductivity. Surface resistivity of AMP-F and AM-F after multiple impregnation of AgNPs@MXene are presented in Figure 5. It demonstrated that the surface resistivity of AMP-F decreased with impregnation times increasing and reached the lowest value of 1.35 × 10⁻² Ω·m after six impregnation times. It existed the firm binding between AgNPs@MXene and PDA coating fabric due to hydrogen bonds of functional groups. More AgNPs@MXene onto PDA coating fabric contributed to the construction of the integral conductive path. Besides, compared with AM-F, the surface resistivity of AMP-F had sharp decreases regardless of impregnation times. The surface resistivity of AMP-F decreased by 65.5 % after six impregnation times in comparison with AM-F. It also verified that PDA coating was beneficial for the formation of complete conductive path for AgNPs@MXene onto fabric.

Figure 5.

Surface resistivity of AMP-F and AM-F under different AgNPs@MXene impregnation times.

Effect of sodium tetraborate concentration on the conductivity of BAMP-F

In order to further improve the conductivity of AMP-F, Na₂B₄O₇ was employed. Figure 6a gives the surface resistivity of boron-enhanced AgNPs@MXene-PDA coating fabric (BAMP-F) after the treatment of Na₂B₄O₇ at different concentrations. It arrived at the lowest value of 7.08 × 10⁻³ Ω·m at 0.02 mol/L Na₂B₄O₇. Compared with AMP-F and AM-F, the surface resistivity of BAMP-F decreased by 47.6 % and 81.9 %, respectively. SEM images of the cross section of conductive layer onto BAMP-F were displayed in Figures 6(b) and (c). There were pores among MXene sheets and the stack was not dense (Figure 6(b)). After Na₂B₄O₇ treatment, the conductive layer had fewer voids and a denser structure (Figure 6(c)). Certain amount of borate ion reacted with –OH of MXene surface, which made the MXene lamella closer. The denser conductive network was formed.

Figure 6.

(a) Surface resistivity of BAMP-F treated by Na₂B₄O₇ at different concentrations; SEM images of the cross section of conductive layer onto BAMP-F: (b) without Na₂B₄O₇ treatment and (c) after 0.02 mol/L Na₂B₄O₇ treatment.

XRD diagram in Figure 7a showed that the peak (002) of MXene existed before Na₂B₄O₇ densification, indicating the existence of gaps between MXene sheets. However, the peak (002) further weakened after Na₂B₄O₇ densification, suggesting the closer stack between MXene sheets. As seen in Figure 7(b)–(d), boron element appeared in boron-enhanced AgNPs@MXene. A new C-O-B peak at 281.8 eV presented in boron-enhanced AgNPs@MXene.²⁰ It elucidated that the covalent bridging between boron ions and −OH of MXene surface.

Figure 7.

(a) XRD of boron-enhanced AgNPs@MXene and AgNPs@MXene; XPS spectra of boron-enhanced AgNPs@MXene and AgNPs@MXene: (b) the total spectra, (c) carbon spectra of AgNPs@MXene, and (d) carbon spectra of boron-enhanced AgNPs@MXene.

Electromagnetic shielding performance of BAMP-F

In order to meet the requirements for daily use, electromagnetic shielding performances of BAMP-F and AMP-F at bands ranging from 30 MHz to 3030 MHz were tested in Figures 8(a) and (b). At 200 MHz, EMI SE values of BAMP-F and AMP-F were 34.51 dB and 24.16 dB, respectively. Compared with AMP-F, it increased by 42.8%. Under three layers of fabrics, EMI SE values of BAMP-F and AMP-F increased to 58.70 dB and 57.43 dB, respectively. It implied that 99 % electromagnetic waves could be shielded. BAMP-F would meet the commercial applications on electromagnetic shielding (≥20 dB). Electromagnetic shielding mechanism of BAMP-F was presented in Figure 8(c). Most incident electromagnetic energy was reflected by AgNPs@MXene conductive layer due to impedance mismatch. Reflection loss of BAMP-F to electromagnetic waves played the main role. Residual electromagnetic waves penetrated into conductive layer, experienced multiple refelection and energy adsorption until being fully dissipated.³¹ Moreover, the abundant polar groups and local defect of MXene produced dipole to enhance the electromagnetic shielding performance. Furthermore, Table 1 lists the comparison for EMI shielding property of different fabrics. It was found that EMI shielding performance of BAMP-F in this work lay in the medium level in comparison with other fabrics reported in literature.

Figure 8.

Electromagnetic shielding performance of (a) AMP-F and (b) BAMP-F at different layers; (c) Electromagnetic shielding mechanism of BAMP-F.

Table 1.

The comparison for EMI shielding property of different fabrics.

Sample	EMI SE (dB)	References
PANI/MXene/CF fabric	26	³²
PEG/PEDOT: PSS decorated cotton fabric	65.6	³³
rGO/Ag decorated cotton fabric	27.36	³⁴
HFO/MXene modified fabrics	33.28	³⁵
Cotton/AgNWs/PVDF@GO composite fabrics	50	³⁶
Cotton/rGO/NiWP fabric	30	³⁷
Carbon black coated cotton fabric	30.8	³⁸
BAMP-F	34.51	This work

Durability of BAMP-F

MXene possessed a few functional groups –OH, –O, and –F which could form hydrogen bonds with amino and pyrocatecdiol groups of PDA. Moreover, the functional groups of PDA coordinated with silver ion of AgNPs. As a result, it existed the firm binding between AgNPs@MXene and PDA coating fabric. AgNPs@MXene could construct the integral conductive path onto the fabric. Durability of BAMP-F was investigated and compared with cotton fabric directly treated by AgNPs@MXene (AM-F).

Figure 9 shows the stability of surface resistivity and EMI SE of BAMP-F and AM-F after bending, ultrasonic washing, and tearing. After 600 bending, washing for 60min, and tearing, surface resistivity of BAMP-F had a slight increase and EMI SE values of BAMP-F lowered a little bit. However, surface resistivity of AM-F exhibited sharp increase and EMI SE values of AM-F decreased to a large extent. It demonstrated that BAMP-F could remained the performance stability under external action, showing good durability. It was ascribed to the hydrogen-bonding interactions between AgNPs@MXene conductive layer and PDA adhensive layer.

Figure 9.

Stability of surface resistivity and EMI SE of BAMP-F and AMP-F: (a) bending, (b) ultrasonic washing, (c) tearing, (d) photos before and after tearing.

Handle of BAMP-F

The hand parameters of the modified fabrics are listed in Table 2. PDA coating made the handle of cotton fabric feel a little better. PDA covered the surface of the fiber and meantime decreased the roughness of the fiber, which was affirmed in SEM images of fabrics of Figure 4. However, the hand feeling of BAMP-F was not significantly changed. It might be that the conductive layer was covered on PDA coating fiber rather than directly coated on the surface of the cotton fabric.

Table 2.

Handle of cotton fabric before and after treatment.

Sample	Stiffness	Compliance	Smoothness
Cotton fabric	38.53	83.24	80.76
0.2-PDA cotton fabric	37.53	84.75	79.40
0.4-PDA cotton fabric	37.61	83.10	80.94
0.6-PDA cotton fabric	37.62	83.12	80.77
0.8-PDA cotton fabric	38.51	83.57	80.06
BAMP-F	39.85	83.87	80.21

Conclusion

AgNPs@MXene composites with excellent electrical conductivity were successfully prepared by in-situ reduction of AgNO₃ by MXene, and its surface resistivity reached 7.22 × 10⁻⁴ Ω·m.

The optimum surface resistivity of BAMP-F arrived at 7.08 × 10⁻³ Ω·m after coating by 0.6 mol/L dopamine, impregnating by AgNPs@MXene for 6 times and densifying by 0.02 mol/L Na₂B₄O₇. Compared with AMP-F and AM-F, the surface resistivity of BAMP-F decreased by 47.6 % and 81.9 %, respectively. Its electromagnetic shielding performance arrived at 34.51 dB and increased by 25.8 % in comparison with AMP-F. BAMP-F also exhibited good handle and durability such as bending-resistance, water-resistance, and tear-resistance.

Footnotes

Acknowledgements

This work was financially supported by National Natural Science Foundation of China (NO. 51703202) and the Fundamental Research Funds of Zhejiang Sci-Tech University (No. 2021Q003).

Declaration of conflicting interests

The author(s) declared no potential conflicts of interest with respect to the research, authorship, and/or publication of this article.

Funding

The author(s) disclosed receipt of the following financial support for the research, authorship, and/or publication of this article: This work was supported by the National Natural Science Foundation of China (NO. 51703202) and the Fundamental Research Funds of Zhejiang Sci-Tech University (No. 2021Q003).

ORCID iD

Lili Wang

References

Lakhe

Prehn

Habib

, et al. Process safety analysis for Ti3C2Tx MXene synthesis and processing. Ind Eng Chem Res 2019; 58: 1570–1579. DOI: 10.1021/acs.iecr.8b05416

Liu

Wang

, et al. Improvement of the electromagnetic properties of blended electromagnetic shielding fabric of cotton/stainless steel/polyester based on multi-layer MXenes. Text Res J 2022; 92: 1495–1505.

Xue

Chen

Yin

, et al. Superhydrophobic conductive textiles with antibacterial property by coating fibers with silver nanoparticles. Appl Surf Sci 2012; 258: 2468–2472. DOI: 10.1016/j.apsusc.2011.10.074

Jeong

Nishikawa

Itou

, et al. Electrical characteristics of a new class of conductive adhesive. Mater Trans 2005; 46: 2276–2281.

Hussain

. Dielectric relaxation of glass particles with conductive nano-coatings. J Phys D: Appl Phys 2009; 42: 064002. DOI: 10.1088/0022-3727/42/6/064002

Wang

Zhou

. Layered machinable and electrically conductive Ti2AlC2 and Ti3AlC2 ceramics: a review. J Mater Sci 2010; 26: 385–416. DOI: 10.1016/S1005-0302(10)60064-3

Dang

Holmes

Zhao

, et al. Enhancing anaerobic digestion of complex organic waste with carbon-based conductive materials. Bioresour Technol 2016; 220: 516–522. DOI: 10.1016/j.biortech.2016.08.114

Agari

Uno

. Thermal conductivity of polymer filled with carbon materials: Effect of conductive particle chains on thermal conductivity. J Appl Polym Sci 1985; 30: 2225–2235. DOI: 10.1002/app.1985.070300534

Jiang

Moon

, et al. Surface functionalized silver nanoparticles for ultrahigh conductive polymer composites. Chem Mater 2006; 18: 2969–2973. DOI: 10.1021/cm0527773

10.

Greaves

Mende

Wang

, et al. Investigating the rheology of 2D titanium carbide (MXene) dispersions for colloidal processing: progress and challenges. J Mater Res 2021; 36: 4578–4600.

11.

Wang

Han

, et al. MXene/wood-derived hierarchical cellulose scaffold composite with superior electromagnetic shielding. Carbohydr Polym 2021; 254(117033). DOI: 10.1016/j.carbpol.2020.117033

12.

Fan

, et al. Sheet-to-layer structure of SnSe2/MXene composite materials for advanced sodium ion battery anodes. New J Chem 2021; 45(4): 1944–1952. DOI: 10.1039/D0NJ04788K

13.

Zou

Zhang

Guo

, et al. Synthesis of MXene/Ag composites for extraordinary long cycle lifetime lithium storage at high rates. ACS Appl Mater & Inter 2016; 8(34): 22280–22286. DOI: 10.1021/acsami.6b08089

14.

Zhang

Zou

, et al. Self-reduction synthesis of new MXene/Ag composites with unexpected electrocatalytic activity. ACS Sustainable Chem & Eng 2016; 4(12): 6763–6771. DOI: 10.1021/acssuschemeng.6b01698

15.

Xia

Zhang

Jiang

, et al. Facile preparation of high strength, lightweight and thermal insulation Polyetherimide/Ti3C2Tx MXenes/Ag nanoparticles composite foams for electromagnetic interference shielding. Compos Commun 2022; 29: 101028. DOI: 10.1016/j.coco.2021.101028

16.

Rajavel

Zhu

, et al. MXene/metal oxides-Ag ternary nanostructures for electromagnetic interference shielding. Chem Eng J 2020; 399(125791). DOI: 10.1016/j.cej.2020.125791

17.

Amiri

Chen

Bee Teng

, et al. Porous nitrogen-doped MXene-based electrodes for capacitive deionization. Energy Storage Mater 2020; 25: 731–739. DOI: 10.1016/j.ensm.2019.09.013

18.

Fan

Wang

Xie

, et al. Modified MXene/Holey graphene films for advanced supercapacitor electrodes with superior energy storage. Adv Sci 2018; 5(1800750). DOI: 10.1002/advs.201800750

19.

Xin

. Possibility of bare and functionalized niobium carbide MXenes for electrode materials of supercapacitors and field emitters. Mater & Des 2017; 130: 512–520. DOI: 10.1016/j.matdes.2017.05.052

20.

Wan

Chen

, et al. High-strength scalable MXene films through bridging-induced densification. Science 2021; 37(6563): 96–99. DOI: 10.1126/science.abg2026

21.

Feng

Hou

Jia

, et al. Preparation and characterization of epoxy resin filled with ti3c2tx mxene nanosheets with excellent electric conductivity. J Nanomater2020; 10(1): 162. DOI: 10.3390/nano10010162

22.

Cheng

Zhang

Tian

, et al. Highly efficient mxene-coated flame retardant cotton fabric for electromagnetic interference shielding. Ind Eng Chem 2020; 59(31): 14025–14036. DOI: 10.1021/acs.iecr.0c02618

23.

Luo

Gao

Luo

, et al. Superhydrophobic and breathable smart MXene-based textile for multifunctional wearable sensing electronics. Chem Eng J 2021; 406(126898). DOI: 10.1016/j.cej.2020.126898

24.

Sengun

Kesim

Caglar

, et al. Characterization of designed, transparent and conductive Al doped ZnO particles and their utilization in conductive polymer composites. Powder Technology 2020; 374: 214–222.

25.

Barani

Miri

Sheibani

. Comparative study of electrically conductive cotton fabric prepared through the in situ synthesis of different conductive materials. Cellulose 2021; 28: 6629–6649.

26.

Sivakumar

Nian

Teng

. Poly(o-toluidine) for carbon fabric electrode modification to enhance the electrochemical capacitance and conductivity. Journal of Power Sources 2005; 144: 295–301.

27.

Cheng

Ran

, et al. In situ reduction of TiO2 nanoparticles on cotton fabrics through polydopamine templates for photocatalysis and UV protection. Cellulose 2017; 25: 1413–1424.

28.

Zhong Zhong

Liu

Wang

, et al. Ti3C2 MXene/Ag2ZnGeO4 Schottky heterojunctions with enhanced photocatalytic performances: Efficient charge separation and mechanism studies. Separation and Purification Technology 2021; 278: 119560.

29.

Wang

, et al. Ice-templated MXene/Ag-epoxy nanocomposites as high-performance thermal management materials. ACS Applied Materials & Interfaces 2020; 12: 24298–24307.

30.

Wang

, et al. Fabrication of durable and conductive cotton fabric using silver nanoparticles and PEDOT:PSS through mist polymerization. Applied Surface Science 2022; 592: 153314.

31.

Weng

Alhabeb

, et al. Layer‐by‐layer assembly of cross‐functional semi‐transparent mxene‐carbon nanotubes composite films for next‐generation electromagnetic interference shielding. Ad. Funct Mater 2018; 28: 1803360.

32.

Yin

Wang

, et al. Multilayer structured PANI/MXene/CF fabric for electromagnetic interference shielding constructed by layer-by-layer strategy. Colloids and Surfaces A: Physicochemical and Engineering Aspects 2020; 601(125047).

33.

Ghosh

Ganguly

Remanan

, et al. Fabrication and investigation of 3D tuned PEG/PEDOT: PSS treated conductive and durable cotton fabric for superior electrical conductivity and flexible electromagnetic interference shielding. Compos Sci Technol 2019; 181(107682).

34.

Ghosh

Ganguly

Das

, et al. Fabrication of reduced graphene oxide/silver nanoparticles decorated conductive cotton fabric for high performing electromagnetic interference shielding and antibacterial application. Fibers and Polym 2019; 20: 1161–1171.

35.

Zheng

Tang

Cheng

, et al. Superhydrophobic hollow magnetized Fe3O4 nanospheres/MXene fabrics for electromagnetic interference shielding. J Alloys Compd 2023; 934: 167964.

36.

Jia

Ding

Sun

, et al. A controllable gradient structure of hydrophobic composite fabric constructed by silver nanowires and polyvinylidene fluoride microspheres for electromagnetic interference shielding with low reflection. Compos Part A Appl Sci and Manu 2022; 156: 106884.

37.

Ding

Wang

, et al. Layered cotton/rGO/NiWP fabric prepared by electroless plating for excellent electromagnetic shielding performance. Cellulose 2019; 26: 8209–8223.

38.

Ghosh

Mondal

Ganguly

, et al. Carbon nanostructures based mechanically robust conducting cotton fabric for improved electromagnetic interference shielding. Fibers and Polym 2018; 19: 1064–1073. DOI: 10.1007/s12221-018-7995-4