Recent Advances in Design Strategies and Multifunctionality of Flexible Electromagnetic Interference Shielding Materials

Highlights

• Detailed summary of current trends in the advancement of flexible EMI shielding materials.

• The theoretical shielding mechanisms and the latest concept of "green shielding" index (g_s) are outlined.

• Functional applications of flexible EMI shielding materials are introduced from thermal conductivity, hydrophobicity to transparency, sensing even multiple functions.

• Exclusive insights in challenges and future design strategies opportunities for flexible EMI shielding materials are provided.

Abstract

With rapid development of 5G communication technologies, electromagnetic interference (EMI) shielding for electronic devices has become an urgent demand in recent years, where the development of corresponding EMI shielding materials against detrimental electromagnetic radiation plays an essential role. Meanwhile, the EMI shielding materials with high flexibility and functional integrity are highly demanded for emerging shielding applications. Hitherto, a variety of flexible EMI shielding materials with lightweight and multifunctionalities have been developed. In this review, we not only introduce the recent development of flexible EMI shielding materials, but also elaborate the EMI shielding mechanisms and the index for "green EMI shielding" performance. In addition, the construction strategies for sophisticated multifunctionalities of flexible shielding materials are summarized. Finally, we propose several possible research directions for flexible EMI shielding materials in near future, which could be inspirational to the fast-growing next-generation flexible electronic devices with reliable and multipurpose protections as offered by EMI shielding materials.

Introduction

In modern society, electromagnetic radiation has become omnipresent in environment because of the tremendously growing usage of mobile phones, Wi-Fi and Bluetooth devices all around the world. It is reported that the number of wireless local area network (WLAN) connected devices in major cities worldwide has doubled from 2016 to 2021 [1], exposing the public to potential health risk that has yet to be adequately assessed. As early as in 2011, the French International Agency for Research on Cancer (IARC), which was authorized by World Health Organization (WHO), has classified that the electromagnetic radiation within 30 to 300 GHz could be carcinogenic [2]. It is known that 4G network and household appliances like microwave ovens mainly use the frequencies around 2.4 GHz. In recent years, a large number of reports have revealed the adverse effects of electromagnetic radiation in microwave frequencies around 2.4 GHz on the central nervous system of human beings, which could cause sleep disorders and wakefulness [3, 4], learning/memory impairment [5] and physical/cognitive abnormality [6]. In addition, the significantly increased incidences of malignant gliomas and schwannomas in male rats also turn out to be associated with the prolonged exposure to the electromagnetic radiation at 900 MHz to 1.8 GHz [7, 8].

Particularly, the public concern on the safety of electromagnetic radiation is further growing with the rapid advances in 5G technologies very recently. According to the 3rd Generation Partnership Project (3GPP) specification of TS 38.104 [9], the 5G-FR1 (sub-6 GHz) network could cover the 450 MHz to 6 GHz band, while mainly works in the n77 (3.3–4.2 GHz) and n79 (4.4–5.0 GHz) bands. Compared to traditional 4G networks which mainly work at around 2.4 GHz, it is obvious that the emerging 5G networks work at higher frequencies, and thus would emit electromagnetic radiation with higher energy. Therefore, such radiation can cause more serious health and safety issues to human bodies. Moreover, besides these possible health and safety issues to human beings, the electromagnetic radiation could also strongly interfere with the electronic devices [10] due to the interaction between electrons in the metallic conductor and the electric fields in the radiation, resulting in the malfunction of electronic devices [11, 12]. Therefore, the development of corresponding electromagnetic interference (EMI) shielding coatings, layers and devices that could resist harmful electromagnetic pollution is essential for the normally operation of electronic devices [13, 14] and the guarantee of human health and safety [15].

To develop high-performance and reliable EMI shielding devices, the EMI shielding materials play a fundamental role by absorbing or reflecting incident electromagnetic wave (EMW) to avoid it penetrating across the shielding layer [16, 17]. Generally, the EMWs are composed of magnetic fields and electric fields, which are perpendicular to each other. In this regard, EMI shielding mechanisms can be primarily categorized into electric shielding, magnetic shielding and electric–magnetic coupling EMI shielding [18]. According to the electromagnetic theory, the electric field and magnetic field of high-frequency EMWs that characterize the radiation strength are interdependent to each other; thus, the shielding of either of them can lead to the vanishing of the other. That is the main reason why traditional EMI shielding materials are mostly conductive materials. At present, the EMI shielding materials actually used in our daily life are mostly conductive materials [19]. According to the different requirements on varied occasions, it could be divided into conductive cloth, conductive rubbers, conductive adhesives and conductive coatings. Generally, conductive cloth are mostly used for flexible human-protective equipment; Conductive rubbers and adhesives are more used in electronic devices owing to their high processability and sealing ability, while the adhesives are usually more indispensable and stable. Conductive coatings have already been widely used in furniture such as chassis. However, as the advances in flexible electronic technology, the EMI shielding materials with the low density, high corrosion resistance, superior mechanical flexibility and low-processing-cost features are extremely desirable for practical applications [20].

Meanwhile, with the rapid advances in flexible and wearable electronics [21], the corresponding EMI shielding materials should also possess low density (i.e., lightweight), high thermal stability, appreciable mechanical flexibility and corrosion resistance besides effective EMI shielding performance [22]. Currently, the developed flexible EMI shielding materials are mainly based on carbon materials [23, 24], polymers [25–27] and MXene-based materials [28]. Particularly, MXene materials, as a novel branch of two-dimensional (2D) inorganic materials, are generally known as transition metal carbides, nitrides or carbonitrides. Although MXenes contain metal elements, they have displayed many unique physicochemical properties which are favorable for flexible EMI shielding, while maintaining the metal-comparable high electrical conductivity at the same time. In the past decade, the number of publications related to flexible EMI shielding materials has been increasing quickly [11, 29, 30]. However, this important topic has been rarely summarized systematically in review articles till now.

This review specifically focuses on various flexible EMI shielding materials for advanced flexible electronic devices and equipment, such as intrinsically flexible substrate/matrix materials and composite flexible matrixes (e.g., carbon-based, MXene-based and polymer-based flexible composite materials). Further, we also analyze the EMI shielding mechanisms and the correlation between EMI shielding efficiencies and absorption/reflection components of EMW, based on which the different construction strategies for the shielding materials are illustrated. Furthermore, we also summarize the multifunctional integration of flexible EMI shielding materials toward extended application fields. Finally, current research challenges and prospective research directions are pointed out for future development of advanced flexible shielding materials.

Electromagnetic Shielding and Attenuation Mechanisms

Shielding Modes and Shielding Efficiency

The shielding efficiency (SE) can be used to evaluate the degree of suppression of EM energy for EMI shielding materials at a specific frequency [31]. Figure 1 shows the possible interaction between EMWs and shielding materials. When EMWs reach the surface of shielding material, it first interacts with the surface, then penetrates it and enters the inner part. A part of the EMWs are absorbed by the main body of material, resulting in absorption loss (SE_A) [30, 32, 33]. Those EMWs that are not absorbed by the material are reflected by the material surface, resulting in reflection loss (SE_R). When the absorbed EMWs travel to another interface of the shielding material, they are reflected again, followed by the energy dissipation in the shielding body, leading to multiple reflection loss (SE_M). The three different types of losses, i.e., SE_R, SE_A and SE_M, together make contributions to the attenuation of EMW [26], so the total SE of EMI (SE_T) could be calculated from the sum of the above three effects, as shown in Eq. 1 [18, 23, 26, 34]:

$$\begin{array}{c}{\text{SE}}_T=10{log}_{10}\frac{P_I}{P_T}=20{log}_{10}\frac{E_I}{E_T}=20{log}_{10}\frac{H_I}{H_T}={\text{SE}}_R+{\text{SE}}_A+{\text{SE}}_M\end{array}$$ 1

where ${\text{P}}_{\text{I}}$, ${\text{P}}_{\text{T}}$, ${\text{E}}_{\text{I}}$, ${\text{E}}_{\text{T}}$, ${\text{H}}_{\text{I}}$ and ${\text{H}}_{\text{T}}$ stand for the incident power, transmitted power, incident electric field intensity, transmitted electric field intensity, incident magnetic field intensity and transmitted magnetic field intensity, respectively. Usually, there are three situations that will occur, given the interactions between EMWs and shielding materials, as follows:

Fig. 1.

EMW propagation model in EMI shielding materials

(i) When EMWs reach the material surface, the incident waves get reflected due to the discontinuous impedance on the surface of the material in contact with the air [26]. This reflection only requires the discontinuity of the impedance on the intersecting surface [31, 35]. After simplifying Fresnel’s equation for a highly conductive shielding materials, the reflection loss from the front to the back of the shield can be expressed as follows [36, 37]:

$$\begin{array}{c}{\text{SE}}_R\left(\mathit{dB}\right)=20lg\frac{{\left(\eta +{\eta }_0\right)}^2}{4\eta {\eta }_0}=39.5+10lg\frac{\sigma }{2\pi f\mu }\end{array}$$ 2

where η₀ and η are the impedances of the free space and shielding material, respectively, μ, σ and f represent the permeability, conductivity of shielding material and incident EMW frequency, respectively. Obviously, SE_R increases with improving conductivity, indicating that the electrical conductivity is extremely important to achieve strong reflection loss for shielding material. However, the reflection loss is not only affected by conductivity. The EMW frequency and permeability of the shielding layer also play a part.

(ii) A part of the EMWs may not be reflected while entering the material. They would be gradually converted into the forms of dielectric loss, magnetic loss and conduction loss during the propagation process [26, 38–42]. This consumption is called absorption attenuation. Generally, the absorbing material can completely absorb the EMWs inside under normal circumstances. Magnetic permeability and dielectric constant are always used to quantitatively reflect the transmission and reflection properties of absorbing materials, respectively [43–46]. The SE_A for conducting and non-magnetic shielding materials could be expressed [37, 47]:

$$\begin{array}{c}{\text{SE}}_A\left(\mathit{dB}\right)=20lg{e}^{\alpha d}=20\left(\frac{d}{\delta }\right)lge=8.68\left(\frac{d}{\delta }\right)=8.7d\sqrt{\pi f\mu \sigma }\end{array}$$ 3

where α is the attenuation constant and δ is the penetration or skin depth. This is a useful parameter for shielding and means the distance below the surface where the electric field intensity is reduced to 1 e⁻¹ of the intensity of initial incident wave [48]. The conductivity and thickness are the main factors of absorption, while permeability and permittivity determine absorption loss [49].

(iii) When the EMWs that are not consumed inside the material reach another surface of the material, they again encounter the interface between the material and the air, and then return to the interiors of the material again [50, 51]. This kind of reflection is called multiple reflection [52–54]. Multiple reflections from the front and back of the shielding material lower EMI SE. SE_M could be calculated as follows [37]:

$$\begin{array}{c}{\text{SE}}_M\left(\mathit{dB}\right)=20lg\left(1-e^{-2\alpha d}\right)=20lg\left(1-e^{-\frac{2d}{\delta }}\right)\end{array}$$ 4

SE_M is highly relied on thickness, and when thickness is near or greater than skin depth, or when SE_T reaches above 15 dB, SE_M can be ignored. However, when the skin depth thickness is larger than the thickness, multiple reflections must be considered when studying the shielding effectiveness [55–58]. The shielding capability can be enhanced by increasing additional interfaces within the shielding material. An interface with mismatched impedance characteristics results in additional internal scattering, also known as internal multiple reflection, which increases the absorption loss [59]. Internal scattering should be different from aforementioned multiple reflection The former caused by additional internal interfaces within the shield greatly increases absorption loss and overall shielding effectiveness, while multiple reflections occur between front and rear surfaces of the shield reduce shielding effectiveness [60–63].

As depicted in Fig. 1, the mechanisms of shielding EMWs in the medium through realizing the loss of EMWs are the reflection loss, multiple reflection loss and absorption loss [46, 47, 64]. For non-magnetic media, a continuous conductive path is formed on the surface that could result in an effective EMW reflection loss. The charged dipole and current path of the medium can effectively convert the energy of the EMWs into other energies (such as heat), realizing electromagnetic loss [65–69]. For magnetic media, the resonance or deflection of the magnetic dipoles mainly contributes to EMW absorption loss (SE_A). The mechanisms of EMI shielding in the medium with multiple heterogeneous interfaces are mainly dominated by multiple reflection losses [64, 70–74]. Through the internal multiple reflections of EMWs that increase the propagation distance in the medium, the EMWs are attenuated [75–78].

At present, vector network analyzers are generally used for the EMI shielding ability test. Incident waves and transmitted waves can be represented mathematically by S-parameters ($S_{11}$ and $S_{21}$). Therefore, it is possible to calculate the ability of the material to reflect, absorb and shield EMWs according to Eqs. 5–10 [79]:

$$\begin{array}{c}R={\left|S_{11}\right|}^2\end{array}$$ 5

$$\begin{array}{c}T={\left|S_{21}\right|}^2\end{array}$$ 6

$$\begin{array}{c}A=1-R-T\end{array}$$ 7

$$\begin{array}{c}{\text{SE}}_R=-10lg\left(1-R\right)\end{array}$$ 8

$$\begin{array}{c}{\text{SE}}_A=-10lg\left(\frac{T}{1-R}\right)\end{array}$$ 9

$$\begin{array}{c}{\text{SE}}_T={\text{SE}}_R+{\text{SE}}_A=-10lgT\end{array}$$ 10

where R, A and T represent the energy coefficients reflected, absorbed and transmitted, respectively, revealing the true EMW energy loss. However, SE_R, SE_A and SE_T represent the ability to reflect, absorb and total shield EMWs, respectively. These two sets of indicators are easy to be misunderstood, because EMI shielding materials with high absorption capacity (SE_A) do not necessarily absorb most of the energy of EMWs. This is because EMWs could only enter the material after reflection [80–83]. The reflection capacity (SE_R) describes the ratio of the reflected energy to the incident energy, and the absorption capacity (SE_A) describes the ratio of the absorbed energy to the energy entering the material. Obviously, the denominators are different when calculating SE_R and SE_A.

Index for "Green EMI Shielding"

For EMI shielding, a problem that cannot be ignored is that high-performance EMI shielding materials are usually composed of highly conductive materials, which can cause very strong secondary reflections. The strong reflected waves generate more significant electromagnetic radiation through mutual superposition and mutual interference, creating an additional adverse EM environment. This issue should be considered in EMI shielding materials seriously, but unfortunately it is usually neglected [84, 85].

With rapid development in human society, the emphasis should also be laid on green shielding of EMI, where "green" means less harm on external and/or internal environment of materials [84]. The ultimate goal of green electromagnetic interference shielding materials is to obtain low reflection and high shielding capability. This means that electromagnetic waves are mainly consumed in the form of absorption to protect the electronics on both sides of the shielding material. Cao et al. proposed the concept of green index (g_s) for the first time and expounded the concept of "green shielding" materials [29]. Besides, they summarized the new requirements for "green EMI shielding" materials and gave the analytical method that defines the green index (g_s) with the corresponding formula (Eq. 11):

$$\begin{array}{c}{\text{g}}_{\text{s}}=\frac{1}{{\text{S}}_{11}^2}-\frac{{\text{S}}_{21}^2}{{\text{S}}_{11}^2}-1\end{array}$$ 11

where S₁₁ and S₂₁ represent input reflection coefficient and the transmission coefficient from input to output, respectively. S₁₁ and S₂₁ are expressed as follows (Eqs. 12 and 13):

$$\begin{array}{c}{\text{S}}_{11}=\frac{\text{r}\left(1-{\text{e}}^{-{\text{i2nk}}_0\text{d}}\right)}{1-{\text{r}}^2{\text{e}}^{-{\text{i2nk}}_0\text{d}}}\end{array}$$ 12

$$\begin{array}{c}{\text{S}}_{21}=\frac{1-{\text{r}}^2}{1-{\text{r}}^2{\text{e}}^{{\text{- i2nk}}_0\text{d}}}{\text{e}}^{-{\text{ink}}_0\text{d}}\end{array}$$ 13

where n, k₀ and d represent refractive index, vacuum wave number and sample thickness, respectively. R could be obtained from Eq. 14:

$$\begin{array}{c}\text{r}=\frac{\text{Z}-1}{\text{Z + 1}}\end{array}$$ 14

where Z is the impedance matching of sample, and could be calculated by Eq. 15:

$$\begin{array}{c}Z=\sqrt{\frac{{\mu }_r}{{\epsilon }_r}}tanh\left[\frac{2j\pi fd}{c}\sqrt{{\mu }_r{\epsilon }_r}\right]\approx \sqrt{\frac{{\mu }_r}{{\epsilon }_r}}\end{array}$$ 15

In addition, S₁₁ and S₂₁ are related to frequency (f), temperature (T) and sample thickness (d). Therefore, g_s can be described by Eq. 16:

$$\begin{array}{c}{g}_s=\frac{1}{{\left|S_{11}(f,T,d)\right|}^2}-\frac{{\left|S_{21}\left(f,T,d\right)\right|}^2}{{\left|S_{11}\left(f,T,d\right)\right|}^2}-1=g_s(f,T,d)\end{array}$$ 16

The "green" materials depend on two key factors including the effective shielding effect (SE) and outstanding impedance matching and absorption loss.

High SE means that human being or working space (internal environment) can be protected from electromagnetic radiation, while good impedance matching could promote the absorption and restrict the secondary reflection of EMW, improving the SE_A for high g_s [85–87]. Generally, efficient shielding materials usually show a SE of ≥ 30 dB and a g_s of ≥ 1 [29]. The "green EMI shielding" materials should not only reduce the transmission of EMWs, but also dissipate EMWs as much as possible to achieve "green EMI shielding."

Construction Strategies for Flexible EMI Shielding Materials

With the increasing use of highly integrated portable electronic devices, flexible EMI shielding devices are expected to be thin and light [88–90]. It is also believed that satisfactory electrical conductivity, complex permittivity and permeability are critical factors toward efficient EMI shielding. Meanwhile, materials with hierarchical structures (like porous, hollow-like) show great potential in EMI shielding. "Green EMI shielding" effects achieved in the materials themselves will cause less additional environmental hazard from the lower secondary reflection. Most of the EMWs radiated into the materials will be consumed by multiple reflections [76, 91].

Some materials inherently possess good flexibility such as high degrees of bendability, twistability and foldability. Otherwise, they have to be combined with mechanical support materials to achieve flexible shielding. Therefore, depending on whether mechanical reinforcement is required, flexible shielding materials could be divided into two categories, including intrinsically flexible materials (graphene aerogel, 3D graphene foam, MXene foam, carbon nanotube sponge and fibrous polymer) and flexible composite material (nanoscale carbon composite flexible materials, flexible MXene-based composite materials and polymer-based flexible composite materials), as illustrated in Fig. 2 [92].

Fig. 2.

Classification of flexible EMI shielding materials

Intrinsically Flexible EMI Shielding Matrixes

Intrinsically flexible EMI shielding matrixes are required to possess not only outstanding EMI shielding capabilities but also good flexibility. Aerogels, sponges, films or foams with highly porous 3D network composed of ultrahigh contents of gas phases and a solid matrix [93] show decent mechanical properties. Due to their unique physical characteristics including ultralow density, large openings as well as ultrahigh surface area, they can be promising candidates of intrinsically flexible EMI shielding materials.

Versatile Nanocarbon Matrixes from Aerogels, Sponges, Films to Foams Based on Graphene and CNTs

Graphene aerogel has been utilized for flexible shielding material due to its lightweight, extremely high conductivity and mechanical stability, and unique 3D microporous structure [80, 94]. The large number of internal pores and free space in the graphene aerogel ensure low density and multiple reflections between the 3D carbon material and air [95]. In addition, the high conductivity of graphene materials increases the relative complex permittivity and SE_R, thus enhancing the EMI shielding performance [96]. Marta et al. [97] prepared highly porous graphene aerogels via the improved hydrothermal treatment method. In a typical hydrothermal process, graphene oxide (GO) nanosheets are reduced and assembled around the hexane droplets. After two rounds of freeze-drying process, the hierarchical and porous structures with ~ 225 μm large pores and ∼5 μm small pores are obtained (Fig. 3a-d). The shielding SE of as-synthesized material is evaluated at 8–18 GHz. It is found that the transmittance is less than 5% of input EMW energy for all porous samples.

Fig. 3.

a-d SEM micrographs of graphene aerogels at different reduction temperatures: non-treated (a), 400 (b), 600 (c) and 1000 °C (d) under Ar/H₂ 1:0.15 atm. The scale bar denotes 200 μm [97];

Copyright © 2019 Elsevier Ltd

The microstructure of graphene aerogels can also be tailored to improve electromagnetic loss [98]. Li et al. [99] prepared graphene aerogel by compressing graphene hydrogel mechanically, accompanied by freeze-drying and annealing (Fig. 4a). It was found that the microstructure of the hydrogel transformed from cellular to layered configuration after compressing (Fig. 4b-e), which plays a key role in dissipation of EMWs. The study also illustrated that the compressed graphene aerogel presented excellent conductivity of 181.8 S/m and EMI SE of 43.29 dB in X-band at the thickness of 2.5 mm, meaning ≥ 99.99% of EMWs have been shielded. To study the effects of different porous molds on EMI shielding, Shen et al. [100] systematically studied the EMI SE of graphene film (G-film) and microporous graphene foam (G-foam) (Fig. 4f-g). It is notable that changing the layered G-film into porous G-foam improves the performance of EMI shielding because of the SE_M by microporous structure at the matrix interface (Fig. 4h). Besides, rather than reflection, the thickness of the G-foam is a key factor in improving electromagnetic absorption (Fig. 4i-k). It is found that the SE of G-foam increased along with the increase in sample thickness, but such increment is not proportional. Crespo et al. [101] reported flexible carbon nanotube (CNT) sponge with < 0.02 g cm^–3 density by CVD route for efficient shielding. Owing to its extremely lightweight, the specific SE (SSE) of it was found to be up to 1100 dB cm³ g^–1, with a SE_T ≥ 20 dB throughout 1–18 GHz range, and capable of realizing shielding by absorption. Their remarkable net absorption ability favors "green EMI shielding" when incorporated into a multilayer structure to inhibit EMW reflection at the input interface. Thus, graphene aerogel, graphene film, microporous graphene foam and CNT sponge could be regarded as friendly "green EMI shielding" materials.

Fig. 4.

a Schematic illustration of the TGA fabrication procedure; SEM images of b TGA-C100%, c TGA-C40%, d, e TGA-C5% [126];

Copyright © 2020 American Chemical Society; f schematic representation of the fabrication process of G-film and G-foam; g SEM images showing microcellular structure in the cross section of G-foam; h schematic representation of multiple reflections in the microcellular structure of G-foam; i-k SE_T, SE_A and SE_T of G-foam with different stacked layers in the frequency range of 8.2–12.5 GHz [100]. Copyright © 2016 Elsevier Ltd

2D MXene: Effective Assembly from Film to Foam

As a promising type of two-dimensional (2D) materials, MXene perfectly interprets the superior electrical conductivity of the layered structure and shows reliable mechanical stability along with adjustable surface, which make it capable for a number of applications such as portable and wearable electronics, especially in the fast-growing field of flexible EMI shielding materials [102–104]. Liu et al. [105] first developed hydrazine-induced foaming technology to prepare hydrophobic MXene foam by assembly of MXene nanosheets into film and further into foam (Fig. 5a). It is found that when MXene film was converted to foam, its conductivity decreased as its thickness is increased (Fig. 5b-e). It exhibited higher shielding SE of 70 dB than 53 dB of pristine MXene film, due to its highly efficient EMW attenuation in its well-existed porous structure. Qian et al. [106] fabricated the unique egg-box-structured carbonized MXene films (Fig. 5f). It was shown that such structure with abundant interior voids could contribute to interfacial polarization and multiple reflection of incident EMWs, and finally promote the EMW absorption (Fig. 5g). Specifically, in Fig. 5h, EMW reflection of the MXene film was drastically increased because of the enhanced conductivity coming from the large amount of free electrons.

Fig. 5.

a Schematic illustration of the fabrication of the hydrophobic and flexible MXene foam. Cross-sectional SEM images of b, c the MXene film and d, e the MXene foam [105].

Copyright © 2017 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim; f schematic illustration for the fabrication of CVMF; g comparison of average SE_A, SE_R and SE_T for CMF, pMF, CVMF and aMF in X-band; h schematic description of the EMWs propagating across CVMF [106]. Copyright © 2020 Elsevier Ltd

Non-Conductive Polymer Matrixes with Intrinsic Flexibility

Polymer-based materials with intrinsic flexibility have shown absorption-dominant EMI shielding capability, which is highly favorable in many application fields like military stealth [50]. In particular, conductive polymers possessing delocalized p-conjugated electrons display peculiar electronic properties, for example low ionizing potential and high electron affinity. The SE of conductive polymers roots in the moving charges as well as bound charges on the backbone [107]. Furthermore, conductive polymers possess easy preparation/processing, easy morphology/shape control, low density and tunable flexibility and conductivity. Nevertheless, for most of non-conducting polymers, they do not provide shielding effects. Therefore, the common approach is to introduce suitable conductive fillers to form polymer composites, which not only offer the possibility to adjust their physicochemical properties, but also afford the opportunity to modify the complex permeability and permittivity, and conductivity to optimize the shielding performance. Suitable filler or filler combinations are essential as well. These fillers would serve as the backbone to provide robust supports for ensuring the flexible structural integrity and effectively alleviating the structure destruction. Thus, the polymers without filler support are usually difficult for EMI shielding application directly. Oppositely, their composites could be more versatile with expanded application potential.

In brief, in order to achieve great flexibility and EMI shielding capacity, the conductivity and special network, usually in the form of aerogel, sponge, film or foam structure, are vital for intrinsic flexible substrate/matrix EMI shielding materials. It is highly feasible to achieve highly efficient EMI shielding materials from MXene, CNT, graphene, as well as many other carbon-based materials, which provide inspirations for advanced design of more flexible EMI shielding composites.

Construction of Flexible Composite Architectures for Dielectric and Magnetic Synergy Effects

Nanocomplexing is regarded as a facile strategy to efficiently adjust conductivity and magnetic properties of the overall composites for superior EMI shielding performance. Also, it is popular strategy to construct flexible EMI shielding composites by combining intrinsically flexible bodies with mechanical supported fillers. Based on aforementioned flexible matrixes, reasonable dielectric or magnetic filling in these materials will greatly conduce to "green EMI shielding" by dielectric and magnetic synergy effects (Fig. 6).

Fig. 6.

Application of flexible nanocomposite in EMI shielding

Dilectric-type Complexing and Magnetic Filling for High SE_A Based on Flexible Nanocarbon Matrixes

As an alternative for conventional metal EMI shielding materials, carbon-based materials and their composite materials with high corrosion resistance, low density, suitable conductivity and easy processing feasibility have been intensively investigated. The nanocarbon-based materials including CNTs, graphene and other nanocarbons are widely applied to construct flexible EMI shielding composites [42, 108–113].

As typical one-dimensional (1D) material, CNT is regarded as a promising candidate for EMI shielding due to the high aspect ratio and conductivity. Moreover, the establishment of simple routes for constructing CNT-based 3D interconnected networks for mass production has attracted great interest [114–116]. Mei et al. [117] obtained CNT-based sponges with different compaction rates (0%, 30%, 50% and 70%) and studied their EMI SE in X-band (Fig. 7a). The microstructures of CNT sponges with different compaction ratios are displayed in Fig. 7b-e. With increased compaction degree, the pore size between the samples greatly decreases, showing a great impact on the sponge density, i.e., the higher compaction degree is, the higher density of CNT sponge is, ranging from 11.1 to 24.4 vol%. It was also demonstrated that 70% compaction rate was beneficial to the buildup of denser and tighter CNTs networks as an interconnected conducting network and finally enhanced the SE of such CNT sponge/EP composite. Similarly, Lu et al. [118] directly used the flexible sponge-like CNTs composed of self-assembled, interconnected CNT skeletons as shielding films with 10.0 mg cm⁻³ density (Fig. 7f-g). The SE and SSE of the freestanding film with 1.8 mm thickness in X-band reach as high as 54.8 dB and 5480 dB cm³ g⁻¹ (Fig. 7h-i). Further, these CNT sponges could also be combined with polymers for EMI shielding. Figure 7j presents the CNT/poly (dimethylsiloxane) (PDMS) nanocomposites as a typical case. Such CNT/PDMS film demonstrates satisfied SE of 46.3 dB at 2.0 mm of thickness with low CNT loading amount of < 1.0 wt%. After 1000 times of stretching or bending, the SE shows little change. These flexible, highly conductive and stable composites could be directly exploited for efficient EMI shielding coatings.

Fig. 7.

a Preparation process of composite CNT sponge with different compaction ratios. b-e SEM images of CNT sponges with varying compaction ratios [117].

Copyright © 2018 Elsevier Ltd. f Photograph of CNT sponges; g SEM image of the CNT sponge. h EMI SE of the CNT sponges in X-band. i Average SE_T, SE_R and SE_A of CNT sponge with different thicknesses. j Schematic illustration of the fabrication of the CNT/PDMS nanocomposites [118]. Copyright © 2018 Elsevier Ltd

The combination of CNTs and graphene foam can also achieve efficient shielding against EMWs while maintaining their flexibility. Sun et al. [119] combined PDMS, CNT and graphene foams (GF) with cellular structure to achieve great EMI shielding performance (Fig. 8a-f). Compared with GF/PDMS composite, the SE of GF/CNT/PDMS with the same porosity (90.8%) increases from 25 to 75 dB (Fig. 8g). However, it does not mean that the higher CNTs filling volume could result in the better EMI SE because there is no difference in the SE between GF/CNT/PDMS with 5 and 2 wt% CNT fillings. This is due to the synergistic effect of CNTs and GFs, which is manifested in the introduction of CNTs that greatly improves the EMW absorption capacity of the composites. On the one hand, the conductive network enabled by the GFs could provide the pathway for electromagnetic field-induced currents, while on the other hand, CNTs could add more interfaces for surface current attenuation. When the content of CNTs was further increased, the conductivity of the GF/CNT/PDMS composite could no longer be improved significantly due to the agglomeration effect. Therefore, the EMI shielding ability did not increase further. Similarly, Kong et al. [116] prepared porous CNTs/rGO foam composites for efficient EMI shielding (Fig. 8h). The introduction of CNTs increased SE_R and SE_A of the foam simultaneously and thus realized the enhanced EMW attenuation (Fig. 8i- j). The EMI SE of CNTs/rGO reached 31.2 dB at 2 mm thickness, and the SSE even reached 547 dB cm³ g⁻¹ with an ultralow density of 57 mg cm⁻³ (Fig. 8k-l). Sundararaj et al. [41] combined CNTs, carbon nanofibers (CNFs) and carbon black (CB) nanoparticles (NPs) with acrylonitrile–butadiene–styrene (ABS) polymer, and found that the CNT/ABS nanocomposites showed the best EMI shielding performance on account of their higher aspect ratio and electrical conductivity.

Fig. 8.

a-e SEM images of GF/PDMS composites with porosities of 9.3%; 28.9%; 51.5%; 73.2%; 90.8%. f SEM image of graphene layers after deposition on a Ni substrate. g Schematic illustration of effective EMI shielding by GF/CNT/PDMS hybrid composites through reflection and absorption [119].

Copyright © 2016 Elsevier Ltd. h Schematic illustration of the EMI shielding mechanism of CNTs/RGO foam composite. i, j SE_T, SE_A and SE_R of the RGO and CNTs/RGO foam composites. k SE_T, conductivity and density of CNTs/RGO foam composite with different reaction time. l The mean values of SE_A and SE_R of RGO and CNTs/RGO foam composite with different reaction time [116]. Copyright © 2019 Elsevier Ltd

In spite of combination with each other among carbon materials to form composites, intrinsic carbon composition is usually limited by extremely high permittivity, resulting in the impedance mismatch. To promote the electromagnetic coupling of carbon materials and thus balance their impedance matching, magnetic particles or low permittivity of nanomaterials are exploited to be embedded or hybridized in the carbon materials. Cheng et al. [74] designed a lightweight and flexible composite aerogel, which was comprising of Co NPs anchored CNTs grown on cotton-derived micron-scale carbon fibers via a facile CVD method (Fig. 9a). It was revealed that the conductivity change of the sample could be controlled by adjusting the morphology of CNTs, i.e., longer and straight CNTs contributed to improved conductivity, resulting in considerable SE of 29.8 dB (Fig. 9b). In contrast, short and curled CNTs with optimized conductivity could facilitate the SE_A, resulting in a wide EAB of 5.08 GHz at 1.6 mm. Overall, when CNTs were filled at the amount of 25% and 30 wt% in matrix, the SE_T reached 20.6 and 29.8 dB, respectively, indicating their capability for shielding ≥ 99% incident EMWs (Fig. 9c). For obtaining "green EMI shielding," Zhang et al. [37] developed a novel dielectric-type WS₂-rGO self-assembly architecture (Fig. 9d). The unique WS₂-rGO gable structure also exhibited efficient and "green EMI shielding" within 2–18 GHz, with the SE > 20 dB, and the maximum shielding value of 32 dB (Fig. 9e). Endearingly, the green index (g_s) was evaluated to be near 1.0. It is revealed that their multilayer structure and inherent dielectric properties, including synergistic relaxation and conduction, and multiple scattering within abundant voids together contributed to the efficient and green EMI SE.

Fig. 9.

a Schematic graph of the formation process of CN-x composites. b The SE_T of all composites. c Shielding effective of SE_R, SE_A and SE_T values of CN-3.0 composite with different filler loadings of 20, 25 and 30 wt% [74].

Copyright © 2019 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim. d TEM images of WS₂ − rGO architecture. e SE of WS2 − rGO at and comparison with rGO [37]. Copyright © 2019 ACS Publications

Furthermore, Wan et al. [120] manufactured a flexible, lightweight and corrosion-resistant Ag nanowire-wrapped carbon (Ag@C) sponge (Fig. 10a), which exhibited ultrahigh EMI SE with superior mechanical stability and ultracompressibility. The Ag@C sponge with a low density of 0.00382 g cm⁻³ achieved 363.1 S m⁻¹ conductivity and an ultrahigh SE of 70.1 dB within 8.2–18 GHz. Besides, the SE of the Ag@C sponge was positively correlated with the thickness and annealing temperature, suggesting that the conductive nanocarbon played a key role in EMI shielding (Fig. 10b-c).

Fig. 10.

a Schematic illustration of fabrication of silver wire wrapped carbon core–shell (Ag@C) hybrid sponge and its application in EMI shielding. b, c EMI shielding performance of Ag@C-1000 sponge with different thicknesses and SE_T [120].

Copyright © 2018 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim

Nanoscale carbon materials are good EMW dissipation materials, regarding their great electrical conductivity. At the same time, their easy processability ensures that they can be combined with other mechanical support materials easily or can be produced into a variety of microstructures. Particularly, porous materials can trap EMWs within their pores, promoting multiple reflections to achieve improved SE_A. For flexible composite materials, the high-aspect-ratio conductive fillers and segregated structure are beneficial to the low percolation threshold; thus, high SE is achievable at relatively low filler loading levels than the randomly distributed systems. Moreover, the incorporation of dielectric materials can further increase the SE_T due to dielectric loss. Similarly, incorporation of magnetic materials can also increase the SE_T owing to interfacial polarization, eddy current loss and magnetic losses involving the magnetic domain movement, relaxation of the magnetization, etc.

Polymer Insertion and Ion Doped in Highly Conductive MXene

MXene is a distinguished 2D transition metal carbide and/or nitride (M_n+1X_nT_x) where M is an early transition metal and X stands for C or N [22]. The superior electrical conductivity and mechanical properties related to metal ions, and the facile insertion of organic molecules and ions, together make MXene good candidates for EMI shielding [121]. As a highly conductive filler, it has attracted tremendous attention in producing EMI shielding composites. In combination with polymers fiber or other fibers, MXene composites can achieve outstanding mechanical properties. MXene Ti₃C₂Tx is often incorporated into different polymer matrices to improve its tensile strength, while maintaining good electrical conductivity under low polymer loadings.

The EMI SE of freestanding MXene-based paper was studied by Ma et al. [99]. They prepared aramid nanofibers-Ti₃C₂T_x/Ag nanowire (AgNW) composite paper with a double-layer structure, super-flexibility and high mechanical strength, and found that higher content of MXene/AgNW led to stronger SE. The MXene/AgNW double-layer nanocomposite paper exhibited high conductivity as well as excellent electrical stability and even maintained excellent shielding performance (~ 80.0 dB, 91 mm, X-band) after repeated bending and stretching (Fig. 11a-b). Jiang et al. _ENREF_22 [122] explored an efficient EMI shielding composite paper based on cellulose /MXene (Ti₃C₂T_x) via a simple dip coating approach. It is found that with the increase in the number of coatings, the conductivity of the composite paper increases remarkably from 0 to 2756 S m⁻¹ attributed to the gradual formation of Ti₃C₂T_x conductive networks. After seven times of dip coating, the SE of the composite reaches 43 dB, which was much better than that of the composite paper without dip coating. Even after 2000 cycles, the EMI SE could still attain exceeding 90% (42.1 dB), indicating its broad application for next-generation flexible devices. Although MXene shows great potential for construction of conductive papers, it is still challenging to achieve satisfactory EMI SE with lowered amount of MXene. Feng et al. [123] systematically studied the influence of Mn²⁺ insertion on composite films and found that the introduction of Mn²⁺ significantly enhanced the shielding performance. Due to the ion bridging effect between MXene nanosheets, the overall electrical conductivity could be ultrahigh (4268 S m⁻¹) with less amount MXene by Mn ions, which is nearly three times than original Ti₃C₂T_x films (1894 S m⁻¹). The SE of Mn ion modified film could reach as high as 69 dB at 9.4 GHz.

Fig. 11.

a Schematic diagram for the fabrication of double-layered ANF-MXene/AgNW nanocomposite papers. b EMI shielding mechanism of the double-layered nanocomposite papers [99].

Copyright © 2020 American Chemical Society. c Illustration of the preparation process of Ti₂CT_x/PVA composite foam and film. d Proposed EMI shielding mechanism of MXene/PVA composites with a foam or film structure. e, f EMI shielding performances of Ti₂CT_x/PVA foam-1, film-1 and film-2 [60]. Copyright © 2019 American Chemical Society

As set forth, foaming is considered as an efficient technique to build up the shielding materials with high flexibility and lightweight. Xu et al. [60] produced porous Ti₂CT_x MXene/polyvinyl alcohol (PVA) composite foam (Fig. 11c). The calculated SSE reached 5136 dB cm² g⁻¹ with ultralow PVA filling of 0.15 vol% and ultralow SE_R of < 2 dB. After the foam was compressed into a thin film, the EMI shielding mechanism was changed from SE_A-dominated to SE_R-dominated mechanisms (Fig. 11d-f). Comparative experiments confirmed that internal multiple reflection, porous structure and dipole polarization show synergistic effects on improving SE_A toward excellent EMI SE. However, the introduced bubbles also easily destroyed the conductive networks in the composite, which leaded to the degradation of EMI SE. Zhao et al. prepared Ti₃C₂T_X-MXene/rGO aerogel with successive core–shell structures via hydrothermal assembly [124]. The porous structure and superior conductivity (1085 S m⁻¹) together enhanced the Ti₃C₂T_x composite aerogel an outstanding SE of 50 dB across X-band, which was a milestone record for the composites with similar MXene loading amount. Meanwhile, the composite aerogel also possessed stable EMI SE for EMWs from different directions attributed to the highly ordered lattice structure. Such assembly of three-dimensional (3D) porous structure can greatly promote the practical utilization of MXene-based composites for EMI shielding devices.

Although the EMI shielding performance is prominent for bare MXenes, their dielectric constants and conductivity are too high; thus, the resulted SE_R is too high while SE_A is low, which consequently cause undesired secondary pollution of EMWs. Incorporation of multiple components in the MXene-based composites could reduce the overall conductivity and EM reflection, resulting in moderate permittivity and increased dielectric loss. When the complex permeability and permittivity are close to each other, they could exhibit the best EMI SE_R and SE_A at the same time. In summary, combination of MXene with mechanical support materials such as polymers and carbon materials can take full advantages of the electromagnetic dissipation capability of MXene while achieving flexibility.

Reinforced Flexible Polymer Composites by Mechanical Supported Matrixes

Polymers are widely used for EMI shielding due to the satisfactory flexibility, corrosion resistance, lightweight and cheap price, while most polymers have poor mechanical property and inherently low electric conductivity, which limit their practical applications. Therefore, it is necessary to mix polymers with conductive and high-strength fillers to obtain desired EMI SE [125–128]. For non-conducting polymer, filling is usually employed to retain reinforced bulk polymer composite, which refers to the composite material consisting of polymer matrix and particle/fiber-type conductive fillers, and the combination of the two into it. Das et al. [129] reported a bulk polymer composite with short carbon fiber (SCF) and carbon black (CB) as filler, and vinyl acetate (EVA) as matrix. Correspondingly, the EMI shielding performance of SCF/EVA, CB/EVA and SCF/CB/EVA composite were studied. As a result, it is found that composites with SCF filler exhibited more superior EMI shielding performance than the composites with CB filler. The reason was also confirmed as SCF showed better dispersion in matrix, thus enhancing the SE. Notably, the shielding effect is inconsistent at Ku band (8–12 GHz) as the frequency increases. Oppositely, it increases slowly as the frequency increases in the lower-frequency range (100–2000 MHz). These carbon fillers could effectively promote the delocalization of the charge carriers and enhance the structural order of the polymer chains, thus facilitating the conductivity.

The composite of metal and non-conductive polymer is a feasible strategy for flexible EMI shielding [130]. Li et al. [131] prepared flexible Cu_xS/polyacrylonitrile (PAN) nanofiber mats (Fig. 12a). Such Cu_xS/PAN mats demonstrated excellent EMI shielding capability (29–31 dB) at low frequencies (500 -3000 MHz). Besides, Zeng et al. [132] designed membranes based on easy polydopamine (PDA)-assisted Cu or Ag deposition on electro-spun PDA polymer nanofibers. The PDA layer served as a substrate allowing the growth of ordered Cu NPs to form continuous layers, with the root mean square surface roughness of ≤ 9.2 nm, suggesting distinct core–shell structure in the membrane (Fig. 12b-d), which enabled the high conductivity and EMI SE of as-obtained membranes. Therefore, by effectively utilizing the interaction between cellular structure of metal and polymer nanofibers, excellent flexibility and conductivity as well as ultrahigh EMI SE could be achieved. The SE of membrane (2.5 µm of thickness, 1.6 g cm⁻³ of density) was up to 53 dB with a broad frequency range. The SE of 44.7 dB was achieved at the lowest thickness (1.2 µm) with normalized SSE as high as 232,860 dB cm² g⁻¹. In addition, Shen et al. have also exploited PDA functionalization to construct polymer films based on Ag@CNTs hybrids [133]. A flexible and highly conductive Ag@PDA@ carbon nanotube–polyvinyl alcohol (PVA) film was formed with the addition of well-dispersed carbon nanotubes and additional silver particles. Compared with the pure carbon nanotubes (21 dB), the shielding efficiency was significantly increased to 42.75 dB for the composite film. PDA polymerization time controls the size of silver particles, the formation of effective conductive network and conductive/interfacial polarization-induced loss mechanisms determine the shielding performance of the film.

Fig. 12.

a Schematic diagram for the preparation of Cu_xS/PAN nanofiber mat [131].

Copyright © 2019 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim; b-d SEM and AFM (the scale bar for height is 0–240 nm) images of the Cu-wrapped nanofibers in the cellular membranes; cross-sectional SEM image of the membranes; Schematic and microstructure of the cellular membranes composed of high-conjunction Cu-wrapped polymer (PDA precoated nylon) nanofibers [132]. Copyright © 2020 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim

In contrast, conductive polymers like polyaniline (PANI), polyfuran (PF), polythiophene (PTH), polypyrrole (PPy), poly(3,4-ethylenedioxythiophene) (PEDOT), polyparaphenylene (PPP), polyacetylene (PA) and poly(p-phenylene vinylene) (PPV), not only maintain decent mechanical properties, but also show outstanding electrical conductivity, making them suitable candidates as flexible EMI shielding agents. Combined with other electrically conductive materials, it is expected that EMWs can be dissipated effectively due to the synergistic effect. Wu et al. [134] reported ultralight EMI shielding composites utilizing the GF/poly(3,4-ethylenedioxythiophene):poly(styrenesulfonate) (PEDOT:PSS) (Fig. 13a). An ultralight porous composite structure with ultralow density of 0.0182 g/cm³ was gained when GF mass fraction is 58% (Fig. 13b-d). Owning to the good conductivity and porous structure, the composites delivered excellent EMI shielding performance (91.9 dB in SE, 3124 dB cm³ g⁻¹ in SSE). And as shown in Fig. 13e, the charge delocalization in highly conductive networks plays a key role by generating the local eddies under an alternating EM field.

Fig. 13.

a Schematic procedure of the preparation of GF/PEDOT:PSS composites. SEM and TEM images of GFs b, c before and d after PEDOT:PSS coating. e Schematic illustration of EMI shielding mechanisms [134].

Copyright © 2017 American Chemical Society. f-i SEM images of the PIPD-g-PDDA/Au6 composites; scheme of the gold network changes during the heating process; SEM images of the PIPD-g-PDDA/Au6 composites pressed at 3 MPa for 2 h; Scheme of the gold network changes during the pressing process [136]. Copyright © 2017 Royal Society of Chemistry

Although conductive carbon-based foams show lightweight and high EMI SE [135], their flexibility and conductivity seem insufficient as compared to those of metal. Alternatively, the combination of flexible skeleton of polymer and highly conductive networking species is expected to achieve high EMI shielding performance. Li et al. [136] constructed a porous polymer nanofiber material with a density of only 0.26 g cm⁻³ via assembly of Au NPs on a poly(pyridobisimidazole) grafted polydimethyl diallyl ammonium (PIPD-g-PDDA) backbone. It is revealed that the lower the Au content applied, the faster the conductivity declined. For high-Au-content PIPD-g-PDDA/Au film, the weight of the film decreases by about 0.8% after heating, with its surface morphology collapsed, as shown in Fig. 13f. The Au NPs were found to fuse together to form a solid gold network. Besides thermal treatment, compressing provides another possibility to promote the electrical conductivity of thin films. The electrical conductivity value of PIPD-g-PDDA/Au films rose to 22,240 ± 998 S cm⁻¹ at 3 MPa pressure. The compressed morphology of the composite material was shown in Fig. 13h. Under compression, as the cross-linked structure of PIPD-g-PDDA NFs changed from round to flat, the Au NPs were arranged more closely, which reduced the contact resistance of Au network (Fig. 13i). It was also found that the shielding effect exceeds 64.9 dB in the nanocomposite material with only 20 mm thick and in the band of 250 MHz-1.5 GHz. By comparing and analyzing SE_R, SE_A and SE_M, the related shielding mechanism is revealed, suggesting that the PIPD-g-PDDA/Au composite materials were both absorptive and reflective to EMW within a certain frequency band, where the SE_R was dominant for overall SE_T. As discussed above, conductive dielectrics-based fillers show satisfactory permittivity and conductivity, low density, as well as suitable physicochemical properties, contributing not only to reliable physical/mechanical properties, but also to high EMI SE of the corresponding composites. The shielding mechanism depends on balanced combination of SE_A and SE_R, rather than the SE_R-dominant mechanism of metals.

As a comparison, we summarize EMI shielding properties of representative flexible EMI shielding materials from intrinsically flexible substrate to composite flexible matrix (Table 1). It seems that the foam structure could be a promising choice for highly efficient shielding materials. Furthermore, it is also an effective approach to design the shielding materials with multiphase interfaces, which could extremely improve the multireflections and promote EMWs absorption. Nonetheless, an in-depth exploration on the materials that possess both ultralow thicknesses, low density and high SE as well as large SSE, and on the mechanisms of shielding in different bands or even broadband is still highly required.

Table 1.

Comparison of EMI SE of representative flexible EMI shielding materials

Materials	Thickness (mm)	Density (g cm−3)	EMI SE (dB)	EMI SSE (dB cm2 g−1)	Refs
PI	2.5	0.076	26.1–28.8	1373–1518	[80]
Graphene aerogel	2.5	–	43.29	–	[165]
Graphene aerogel	5	0.006	–	6743	[97]
Graphene foam	0.3	0.06	25.2	–	[100]
MXene foams	–	–	70	–	[105]
Microsphere@void@ MXene	0.01	–	46.51–59.76	18,637.14	[106]
CNTs/RGO foam	2	5.7	31.2	547	[117]
CNT sponge/epoxy	3	–	53.14	–	[118]
PIPD-g-PDDA/Au	0.02	–	66.9	15,890	[136]
GF/CNT/PDMS	–	–	75	833	[119]
CNTs aerogel	1.6	–	29.8	–	[74]
CNTs/RGO	2	–	31.2	547	[116]
Ag@C	3	0.00382	70.1	61,169	[120]
d-Ti3C2Tx/r-CNFs	0.015	–	42.7	–	[22]
MXene/AgNW	–	–	80	3725.6	[99]
rGO/epoxy	–	0.06	38	500	[125]
PVDF/MWCNT/GNPs/Ni	0.3	–	43.7	–	[128]
GF/PEDOT:PSS	–	0.0182	91.9	3124	[134]
Cu-wrapped polymer nanofiber	0.0025	1.6	53	232,860	[132]
PAN/CNT/Fe3O4	1.5	–	59.85	–	[147]
PPy/MXene	1.3	–	90	1000	[140]
CuxS/PAN	0.423	0.044	29–31	16,655.92	[131]
MCP-SiC composite paper	0.3	–	67	1–	[137]
AgNWs/cellulose films	0.0445	–	101	5571	[138]
PP/PDA/AgNPs/PDMS	–	0.263	71.2	270.7	[139]
AgNF	0.1	–	76	–	[143]
PEBAX/graphene	–	–	30.7	–	[145]
Fe3O4@Ti3C2Tx/GF/PDMS	–	–	77–80	–	[146]

Multifuctionality

Multifuctionality is inevitably a main direction for future development of EMI shielding materials. Particularly, the development of low-dimensional, nanoscale and functional EMI shielding agents could bring about advanced properties of materials. New functionalities related to EM properties in miniaturized EM devices occupy a lot of potential in the future development of various scientific and technological fields. Besides EMW absorbing and shielding, the new functionalities also include EMW filtering, sensing, optics and energy conversion and storage devices.

Thermal Conductivity and Hydrophobicity

For modern flexible electronic devices, the effective heat dissipation during operation is essential, which ensures the reliability and service life of devices. Therefore, it opens an important direction for developing next-generation EMI shielding material with efficient heat conduction. Usually, the parameter thermal conductivity (TC) represents the ability of material to conduct heat, with its unit of W m⁻¹ K⁻¹, which means the capacity of material to transport a specific quantity of heat energy in 1 s via a plate of a specific area (1 m²) and thickness of (1 m) when its opposite face differs in temperature by 1 K. The development of EMI shielding materials should integrate the functionalities of high TC and high SE values. Chaudhary et al. [137] prepared multicomponent framework derived SiC composite paper with both strong EMI shielding effect (−67 dB at 10.3 GHz) and good TC of 6.5 W m⁻¹ K⁻¹, which were positively correlated with the amount of SiC. Similarly, Gu et al. [138] obtained AgNWs/cellulose films with outstanding mechanical strength and superior in-plane TC of 10.55 W m⁻¹ K⁻¹. Meanwhile, the SE was ultimately retained as ∼95 dB after bending for 1500 cycles. To further apply the AgNWs/cellulose films to thermal management, polyimide electrothermal films were pasted on AgNWs/cellulose films, and the variation in surface temperature was recorded (Fig. 14a). Unlike the sharp temperature increase when pure cellulose or air was used as heat sink, the maximum operating temperature fell to around 142 °C when 50 wt% AgNWs/cellulose film was utilized as heat sink, demonstrating its efficient heat dissipation during device operation. Additionally, the 50 wt% AgNWs/cellulose film also showed rapid response to Joule heating (Fig. 14b). When the input voltage is 1 V, the temperature did not increase greatly. However, the 1.5 and 2 V of input voltage caused rapid temperature increase of the AgNWs/cellulose film, which finally stabilized at 59.3 and 99.5 ℃, respectively.

Fig. 14.

a Schematic diagram of multifunctional flexible AgNWs/cellulose films; b Joule heating performances [138].

Copyright © 2020 American Chemical Society. c Water-contacting angle measurements of M-textiles without (right) and with the coated silicone (left); d I–V curve of silicone-coated M-textile; e Effects of water-resistant treatment on the stability of EMI shielding performance [140]. Copyright © 2018 WILEY‐VCH Verlag GmbH & Co. KGaA, Weinheim

Due to the requirement of water resistance for electronic devices, hydrophobicity becomes one of the emerging functions for EMI shielding materials. Gao et al. [139] prepared conductive polymer fabric composites (CPFCs) with high SE of 71.2 dB and an extremely high water-contacting angle (152.3°). More importantly, the super-hydrophobicity and EMI SE retained great stability after the abrasion/winding cycling tests. Zhang et al. [140] further designed and prepared a new fabric material, i.e., silicone-coated PPy-modified MXene sheets embedded on poly(ethylene terephthalate) (PET) textiles. Besides excellent joule heating and EMI SE performance, the thin silicone coating offered high hydrophilic property (Fig. 14c). The silicon-coated textiles occupied a contact angle up to ≈126°, which to a large degree protected MXene from water-induced oxidation and afforded valuable waterproofing performance. The experimental results also showed that the flexible and multifunctional textiles had low resistance from nearly linear I–V curve, which ensure voltage-driven heating favoring the safety of operators (Fig. 14d). The EMI shielding efficiency of resultant multifunctional textile at a thickness of 1.3 mm was up to 90 dB. What is more, it could maintain great EMI shielding ability even after washing (Fig. 14e). Therefore, such versatile textile holds great potential in smart clothing allowing both EMI shielding and personal heat management.

Transparency, Sensing and Multiple Functions

Transparency is also important for next-generation flexible shielding agents because of the demand for visualizations of electronic devices. Among the wide choice of materials, silver nanowires or nanofibers can well satisfy the industrial requirement of sheet resistance < 100 Ω sq⁻¹ and transmittance > 90% [141]. Moreover, AgNWs are more chemically stable than other metals like Cu. When compared to carbon-based NWs/NFs, AgNWs could create the networks with higher conductivity. The ferro-ferric oxide (Fe₃O₄)-modified AgNW films obtained by Jiao et al. [142] exhibited EMI SE of 24.9 dB and transparency of 90%. Due to the high permeability of Fe₃O₄, the absorption loss of electromagnetic radiation was improved. By improving the conductivity of silver nanowire film, the shielding effectiveness of silver nanowire EMI shielding film was enhanced. Subsequently, Lei et al. [143] prepared silver nanofiber film by a room-temperature roll-to-roll production method, exhibiting superior EMI shielding ability (76 dB, at 100 μm) and great light transmittance (89%, at 1 μm) (Fig. 15a-b). By controlling the fibers diameter and spinning time, the optical transmittance of silver nanofiber film can be varied (Fig. 15c). Furthermore, the film flexibility and bending stability was investigated. Figure 15d shows the test results for flexibility and durability of silver nanofibers and silver nanofiber film. No breaking was observed in silver nanofiber film despite the 180-degree bending.

Fig. 15.

a Schematic diagram of the fabrication of AgNF by continuous blow spinning and in situ UV irradiation. b Partially enlarged detail of needle module shows the principle of blow spinning. c A photograph of as-prepared fiber film after different spinning time (from left: 1, 2, 5, 10 and 20 min). d SEM image of a bended AgNF film and its partially enlarged areas, With scale bars of 300 and 50 μm, respectively [143].

Copyright © 2019, Springer Nature. e Schematic diagram of the fabrication procedure for Fe₃O₄@Ti₃C₂TX/GF/PDMS composite. f Images of the equipment used for pressure sensing measurement (left), GF-based composite with two electrode lines (right up) and bending/stretching features of GF-based composite (right down). g Plots of relative resistance variation versus applied pressure for GF/PDMS and Fe₃O₄@Ti₃C₂TX/GF/PDMS composites [146] Copyright © 2020 Elsevier B.V

The rapid developing industry of flexible electronics requires various sensors with high sensitivity and a wide range of responses [144]. Zhao et al. [145] prepared the poly(ether-block-amide)/graphene films. With 8.91 vol% graphene, the composite film could reach 30.7 dB of average EMI SE. More interestingly, the poly(ether-block-amide)/graphene film exhibited an almost linear pressure sensing behavior as the external pressure stimulation increased owing to the formation of more conductive paths via decreased distance between adjacent graphene. Also, Nguyen et al. [146] demonstrated a multifunctional EMI shielding skin containing freestanding graphene-reinforced PDMS foam decorated by Fe₃O₄ NPs-interbedded Ti₃C₂T_X nanosheets (Fig. 15e), exhibiting remarkable EMI SE of 80 dB in X-band and 77 dB in Ka-band because of high SE_A. Besides, it also played a part as a pressure sensor owing to the high electrical conductivity, good elasticity and rapid recovery. It is distinct in Fig. 15f that the sensing material is highly bendable and stretchable. The relative resistance variation (R − R₀)/R₀ for the composites is shown in Fig. 15g under varied pressure from 62.4 to 998.9 kPa. The lightweight, highly conductive and flexible composite with favorable response to external pressure is holding great potential for multifunctional EMI shielding skin toward wearable electronics.

Many studies have also shown that flexible EMI shielding materials can demonstrate multiple functions simultaneously. Wang et al. [147] recently reported a multifunctional nylon/graphene nanoplatelet (GNP) paper material made of commercial nylon gauze and GNP, via a feasible and scaled method combing vacuum filtration and compression molding. It is investigated that the as-prepared composite paper possesses the advantages of good flexibility and multifunctional properties. When adding 11.8 wt% GNPs, the three-layer composite nylon/GNP paper with a thickness of ~ 180 μm demonstrates both high electrical conductivity and high thermal conductivity of 24.3 S cm⁻¹ and15.8 W m⁻¹ K⁻¹, respectively. In particular, it shows a large EMI SE of 58.1 dB in x-band (8.2–12.4 GHz). Remarkably, the hydrophobicity and flame retardancy of the composites are improved obviously, and the mechanical properties are also satisfactory. For future electronic equipment, the electromagnetic pollution is not the only concern, while flame retardant, heat insulation, water resistance and other features may also be required. Besides, the flexible EMI shielding materials may be required to become optically transparent, electrically conductive, thermally conductive or even sensitive. Therefore, multifunctional integration will be one of the directions in developing flexible EMI shielding materials in the future.

Conclusions and Prospect

Given the rapid advancement of 5G-related microelectronics and flexible electronics industries, the overwhelmingly generated electromagnetic radiation has definitely become a serious pollution source. Great advances have been achieved in exploration of reliable EMI shielding agents which could reduce or even eliminate detrimental electromagnetic radiation. In this regard, this review describes recent developments of flexible shielding agents based on a comprehensive elaboration of EMI shielding mechanisms, the correlation between absorption and shielding, and lays a specific emphasis on flexible EMI shielding materials with excellent structural integrity and various functional construction. Through literature survey, generally, flexible EMI shielding materials could be obtained via either direct or indirect constructing routes. In terms of the direct route, conductive foam, sponge or aerogel 3D structure present some representative merits and is regarded as excellent contenders. In addition to contributing low weight, the pores in foam, sponge or aerogel promote absorption of EMW energy by multiple scattering at the interfaces within pores. Therefore, foam, sponge or aerogel-structured materials are specialized in flexible portable electronics and defense wearable devices. The indirectly constructed flexible EMI shielding composite materials could show not only great EMI shielding performance but also various excellent properties by introducing nanofillers. On the one hand, the abundant heterogeneous interfaces enhance the interface polarization/relaxation, resulting in magnified interface polarization and multiple reflection-induced SE_A. On the other hand, introducing magnetic species into dielectric system could achieve greatly enhanced magnetic loss [148–151]. Meanwhile, the composite materials integrating both magnetic and dielectric components could display both high magnetic loss and dielectric loss [152–155], along with the improved impedance matching [156–159]. From the perspective of flexible materials, carbon-based materials, MXenes and polymers are three mainstream matrixes for constructing the intrinsically flexible substrates or their composites based on nearly most of reported literature.

For carbon-based materials, 1D CNTs and CNFs, and 2D graphene nanosheets could show highly efficient EMW absorption and EMI shielding performance, but their excellent flexibility and mechanical properties can no longer meet the current development of devices. As mentioned previously, various 3D carbon structures including foam, sponge, aerogel are encouraging. Besides the large surface area and highly porous structure, which are conducive to enhanced multiple reflections, the electromagnetic parameters can be adapted by mechanical compression of the foam or sponge. Despite that carbon-based porous microstructures and their composites have been verified to be beneficial toward improved multiple reflections, the underlying mechanism remains unclear. What is the optimal pore size range for EMI shielding? What is the relation between wavelength of incident EMW and aperture? How to evaluate the contribution from multiple reflections and scattering? All these questions need systematic study and urgent breakthrough.

The research on MXene-related materials has been deepened with extensive in-depth investigation from all over the world. MXene exhibits great potential in EMI shielding owing to its laminated structure and high conductivity. By atomic layer clipping and hybridization, the interior conductive networks of MXenes could be regulated to afford high SE and SSE. Nonetheless, the irreversible oxidation of MXene may destroy its microstructure and restrict its EMI SE. Next, it is essential to optimize the hybridization approach to avoid undesired damage of the microstructure for efficient regulation of the network structure. Furthermore, even though the manufacturing method for MXene-based material is coming-of-age at present, in order to achieve large-scale production of MXene, more reliable, safer and economical manufacturing process is admirable.

Polymers are favorable for constructing flexible shielding agents because of excellent elastic–plastic properties. Through addition of nanofillers with high conductivity (CNTs/graphene/CNFs/metal and other fillers) into the polymers, the electrical conductivity and mechanical strength of the resultant composites are further improved. However, dispersion of nanofillers in polymers is a challenging work as van der Waals attraction among carbonaceous fillers would cause agglomerations in the polymers. Therefore, addressing the interface interaction issue between these fillers and polymer matrix is crucial. Besides, some fibrous fillers, such as CNTs and CNFs, present a long structure, but they may transform into curved ones because of ductility during the mixing process, which further increases viscosity. To alleviate these problems, appropriate blending process is also needed along with surface treatment. To sum up, surface treatment and better mixing method of filler are very important to obtain a good EMI shielding for polymer-based composites. The improved wettability of the filler reduces the matrix viscosity, requiring smaller shear stress for filler decentralization in the matrix. This creates multiple contacts between the entangled structure, and the filler in the matrix creates more paths that facilitate electrons to move efficiently through the insulating polymer. Nevertheless, appropriate mixing mechanisms and equipment is challenging in order to achieve such a dispersion in mass production. As described in the literature, it is a challenging to improve structure performance with superior EMI shielding effect under the premise of low quality and low cost.

Based on the above discussion, some prospects concerning the flexible EMI shielding materials are proposed and summarized as follows:

• (i)Exploring more novel materials for flexible EMI shielding. Besides the materials discussed above, there are some other emerging materials which are promising for flexible shielding applications. For example, the atomic sheets of boron, called borophene, have shown even more favorable electrical and mechanical properties than graphene [160]. Calculations reveal that corrugated borophene could conduct electricity more easily along the ridge direction than across them, and is also stiffer in this direction than graphene, which suggest its great promise as a new EMI shielding material. What is more, phosphorene, liquid metallic/ionic foams are also holding great promise as future flexible EMI shielding [161].
• (ii) Controllable fabrication. The adjustable fabrication and optimization of EMI shielding constituent with designed structure are fundamental for developing the flexible and efficient shielding material. Currently, it is difficult to obtain stable and reproducible materials with precisely controlled morphology, porous structure and multiple interfaces, especially for those sophisticated multilayer or 3D structures such as hydrogels, aerogels and foams that hold great potential for next-generation SE_A-dominant shielding materials and devices. More importantly, from an industrial viewpoint, the fabrication of typical shielding materials such as MXene is not environmentally friendly and cost-effective because it usually requires longtime hydrofluoric acid etching, which is quite energy-consuming, time-consuming and dangerous to workers. Meanwhile, the complicated fabrication details, along with unclear synthetic mechanisms have also hindered the scaling up of production of current EMI shielding materials toward practical applications and commercial usage.
• (iii) In-depth understanding of shielding mechanisms for "green EMI shielding." The fundamental insights of the composition–structure–property relationship are vital for further optimization of SE. This is the prerequisite for developing highly efficient flexible shielding materials. Currently, the mechanisms of EMI shielding still need to be further studied. Particularly, the future trend of EMI shielding materials is low SE_R and high SE_A, i.e., "green EMI shielding." Most of the current EMI shielding materials are dominated by reflection, which comes from high electrical conductivity, while such high reflection will result in secondary pollution of electromagnetic radiation. However, it is still an arduous task to search for more high-absorption and low-reflection materials and develop absorption-dominated EMI shielding mechanisms. In this regard, some advanced techniques such as electron holography could be helpful for revealing the magnetism-related interfacial phenomena toward enhanced "green EMI shielding" performance [162, 163]. On the other hand, it is difficult to implement the absorption, conversion and storage of electromagnetic energy simultaneously to realize the energy recycling. To date, there are still few reports on this meaningful topic. Thus, MXene as an emerging type of materials which presents amazing performance as a variety of catalysts and supercapacitor electrodes [164], may bring about some breakthroughs in the near future.
• (iv)Toward multifunctional and practical applications. Till now, highly efficient flexible shielding materials have been extensively studied. The multifunctional level has also been constantly extended from TC and hydrophobicity to transparency, sensing even multiple functions. However, these materials were mostly tested at the laboratory level, while there is still a large gap to practical production. In this regard, the cost control and standardization are two most important prerequisites for scale-up of the production. For cost control, both the selection of EMI flexible shielding material and the consequent processing, including design, fabrication and optimization of multifunctional properties need to be considered more economically. For example, as reported high-performance material for flexible EMI shielding, MXenes are quite expensive, and their fabrication processes are usually quite complicated, which need to be fulfilled at extremely harsh, energy-consuming and time-consuming conditions. One possible way to solve the problems is to reduce the concentration of electrical or magnetic conductive filler in a well-designed 3D scaffold. It could significantly reduce the using amount of MXene, bringing about more cost-effective, low-density flexible shielding materials. Moreover, the controlled porosity can help disperse the conductive species selectively and thereby optimize the generation of conductive network at a lower MXene amount to achieve superior shielding performance. In another concerned respect, for standardization, it is of great significance as well for multifunctional and practical usage of the current laboratory-level shielding materials because it can ensure the stability and reliability with regard to both the production and usage of the materials and devices.

We believe that there is huge space for further development of flexible EMI shielding materials, and this review offers some guidelines for future research on construction of next-generation flexible and multifunctional EMI shielding materials with high performance.

Abbreviations

g_s

Green shielding index

EMI

Electromagnetic interference

WLAN

Wireless local area network

IARC

International Agency for Research on Cancer

WHO

World Health Organization

3GPP

3Rd Generation Partnership Project

EMW

Electromagnetic wave

SE

Shielding efficiency

SE_A

Absorption loss

SE_R

Reflection loss

SE_M

Multiple reflection loss

SE_T

The total SE of EMI

3D

Three-dimensional

CNT

Carbon nanotube

GO

Graphene oxide

rGO

Reduced graphene oxide

G-film

Graphene film

G-foam

Graphene foam

CVD

Chemical vapor deposition

SSE

Specific shielding efficiency

2D

Two-dimensional

1D

One-dimensional

PDMS

POLYDIMETHYLSILOXANE

CNFs

Carbon nanofibers

CB

Carbon black

NPs

Nanoparticles

ABS

Acrylonitrile–butadiene–styrene

AgNW

Silver nanowire

PVA

Polyvinyl alcohol

SCF

Short carbon fiber

EVA

Vinyl acetate

PAN

Polyacrylonitrile

PDA

Polydopamine

PANI

Polyaniline

PF

Polyfuran

PTH

Polythiophene

PPy

Polypyrrole

PEDOT

Poly(3,4-ethylenedioxythiophene)

PPP

Polyparaphenylene

PA

Polyacetylene

PPV

Poly(p-phenylene vinylene)

PSS

Poly(styrenesulfonate)

PIPD

Poly(pyridobisimidazole)

PDDA

Polydimethyl diallyl ammonium

TC

Thermal conductivity

CPFCs

Conductive polymer fabric composites

PET

Poly(ethylene terephthalate

Funding

Open access funding provided by Shanghai Jiao Tong University.