Magnetic Carbon Nanotubes/Graphene Oxide Nanocomposites: One-Step Controllable Production, and Their Excellent Microwave Absorption Capabilities

Introduction

In the past decades, microwave absorbers (MAs) have drawn significant attention owing to the expanded electromagnetic (EM) radiation and interference problems (Novoselov et al., 2004; Zhang et al., 2014; Cao et al., 2019). It is well acknowledged that MAs with characteristics such as strong absorption ability, large absorption bandwidth, lightweight, low cost, and remarkable chemical stability are highly desirable because of their promising military and civil application prospects (Zhang et al., 2015; Fang et al., 2016). According to the EM energy conversion principle, the incident EM wave can be attenuated by dielectric and magnetic losses (Wei et al., 2017). Therefore, nanocomposites (NCs) consisting of dielectric loss materials and magnetic nanoparticles (NPs) are considered an effective way to achieve high-performance MAs (Liu et al., 2015, 2018; Quan et al., 2017). For example, CoNi@Air@TiO₂ (Liu et al., 2016), Co_0.6Fe_2.4O₄@MoS₂ (Long et al., 2019), Ni@SnO₂ (Zhao et al., 2016), Co₇Fe₃@SiO₂ (Chen et al., 2017) have been demonstrated to display outstanding microwave absorption properties (MAPs). Generally, owing to their excellent synergistic effect, the development of high-performance MAs mainly focused on core@shell structure magnetic NCs, in which dielectric substances are utilized as a shell and magnetic NPs as a core. Among them, different dielectric substances such as ZnO, TiO₂, and BaTiO₃ were often used as a shell (Liu et al., 2008; Jiang et al., 2014; Xu et al., 2018). However, the biggest drawback of these NCs is the high density, which hugely restricts their practical application.

In recent years, owing to the lightweight, unique tube structure and excellent dielectric loss, carbon nanotubes (CNTs) were used as substrate to construct the CNTs-based for designing the ideal MAs (Chen et al., 2015; Wang et al., 2018). Examples include Fe/CNTs (Che et al., 2004), ZnFe₂O₄/CNTs (Khabouri et al., 2015), and Fe/Co/Ni/CNTs (Wen et al., 2011), which were demonstrated to display very outstanding MAPs. Generally, the previously designed core@shell structure CNTs-based NCs were mainly composed of CNTs as a shell and different categories of magnetic NPs as a core (Lv et al., 2008; Weissker et al., 2010). However, the magnetic properties and magnetic loss abilities for these kinds of CNTs-based NCs are hugely limited and cannot be well modulated due to the magnetic NPs acting as the core, and the low encapsulation of magnetic NPs (Pawar et al., 2019; Long et al., 2020). Therefore, constructing the reverse core@shell structure magnetic CNTs-based NCs, in which magnetic NPs serve as the shell and CNTs as the core, is an effective way to overcome these problems (Wang et al., 2012; Li et al., 2017).

Furthermore, the recent results indicated that the outstanding properties of graphene (G) and the designed G-based could provide many more interfaces, which were conducive to improve MAPs (Qu et al., 2016; Wang et al., 2019). Considering these aspects, in this article, we designed and synthesized magnetic CNTs/graphene oxide (GO) NCs by a one-step hydrothermal method. By changing the Co:Fe molar ratio, different compositions of magnetic NPs/CNTs/GO NCs could be selectively produced. The obtained results showed that the as-prepared magnetic CNTs/GO NCs displayed very excellent MAPs.

Experimental

Synthesis of Magnetic CNTs/GO NCs

Similarly to the previously reported experimental method shown in Figure 1 (Wu et al., 2020), 80 mg of GO was prepared by a modified Hummers method (Hummers and Offeman, 1958). The prepared GO was added in 40 mL deionized water and ultrasonicated for 30 min at room temperature (RT). Next, 40 mg of hydroxylated CNTs were ultrasonically dispersed into the GO solution for another 30 min to obtain the GO/CNTs substrate solution. Then, the solution of Co²⁺ and Fe³⁺ was obtained by ultrasonic dissolving C₄H₆CoO₄∙4H₂O (1 mmol) and FeCl₃∙6H₂O (1 mmol) into a 30 mL ethylene glycol solution. Subsequently, the resulting Co²⁺ and Fe³⁺ solution was dissolved into GO/CNTs substrate solution by stirred for ca. 60 min. Finally, urea (0.9 g) were thoroughly dispersed into the mixed solution for another 5 min. The final solution was transferred into a 100 mL Teflon-lined stainless steel autoclave and heated at 200°C for 24 h and left to cool to RT. The synthesized magnetic CNTs/GO NCs were washed several times and magnetically centrifuged. The obtained sample was left to dry. The experimental conditions were kept the same, with the exception of 2 and 3 mmol of FeCl₃∙6H₂O, which were used as the Fe source in the synthesis of magnetic NPs/CNTs/GO NCs to control compositions of the sample. The samples were denoted as S1, S2, and S3 for easy description, respectively.

FIGURE 1

Figure 1. Schematic illustration for the synthesis process of the as-prepared magnetic CNTs/GO NCs.

Characterization and Measurement

The phases and microstructures of the as-prepared magnetic CNTs/GO NCs were characterized by an X-ray powder diffractometer (XRD) (model Smart Lab, Rigaku), Raman spectroscopy (Jobin-Yvon Labram HR800), Thermal gravity analysis (TGA) (Netzsch Sta 449F3), transmission electron microscope (TEM) (model Tecnai-G20), and X-ray photoelectron spectroscopy (XPS) (model Escalab 250Xi, Thermo Fisher Scientific). 30 wt% of the obtained samples were mixed with wax and pressed into toroidal shaped samples (R_out: 7.0 mm, R_in: 3.0 mm), respectively, to investigate the EM properties and MAPs. The as-prepared composites were measured by a vector network analyzer (Agilent E8363B) in the frequency region of 2–18 GHz.

Results and Discussion

Figure 2 presents the XRD patterns and Raman spectra of the as-prepared magnetic CNTs/GO NCs. Figure 2A shows that all the as-prepared samples display similar XRD patterns, pointing to the same category of sample. The characteristic peaks at 30.08°, 35.44°, 43.06°, 53.44°, 56.97° and 62.59° corresponding to (220), (311), (400), (422), (511), and (440) crystal planes are consistent with the standard XRD patterns of spinel CoFe₂O₄ (JCPDS: 22-1086). In comparison, one peak at 32.6° can be observed clearly over S1 and S2, assigned to (104) crystal planes of CoCO₃ (JCPDS: 78-0209). However, this peak cannot be seen over sample S3. The comparison results reveal that the obtained samples evolve from CoCO₃ to Co_xFe_3–xO₄ when the amount of Fe source increases from 1 mmol to 3 mmol. In confirmation of the results, the experimental conditions were kept the same, with the exception of 5 mmol FeCl₃∙6H₂O, which was used as the Fe source to produce the sample, S4 for easy description. As shown in Figure 2A, the XRD pattern indicates that the phase of CoCO₃ cannot be observed over the as-prepared S4, which is consistent with our previous reported result (Wu et al., 2020). Moreover, consistent with the GO/CNT-Fe₃O₄ NCs reported elsewhere (Wang et al., 2014), the characteristic diffraction peaks for GO and CNTs cannot be seen, which should be attributed to the uniform dispersion of Co_xFe_3–xO₄ NPs on the surface of CNTs/GO. The existence of carbon materials can be confirmed by Raman spectra. As shown in Figure 2B, the obtained magnetic CNTs/GO NCs show three evident peaks located at 1347 cm^–1, 1586 cm^–1, and 2694 cm^–1, respectively. These peaks can correspond to the D band, G band and 2D band of carbon material, respectively. It is well-known that the D band originates from the sp³ defect/disorder in the graphitic structure, the G band is indicative of a high crystallinity graphitic layer, and the 2D band is excited by a double-resonant Raman process (Ritter et al., 2006; Popov and Lambin, 2013). Based on the obtained results, we can confirm the existence of GO and CNTs in the obtained NCs.

FIGURE 2

Figure 2. (A) XRD patterns, and (B) Raman spectra of the as-prepared samples.

Figure 3 shows the typical TGA curves and XPS spectra of as-prepared samples. As shown in Figure 3A, it can be seen that the obtained S2 and S4 samples present the evident weight loss under air atmosphere in the temperature range of 240–620°C. Based on the XRD results, the mass loss can mainly be ascribed to the thermal decomposition of GO and CNTs, and the residual substances should be assigned to Co_xFe_3–xO₄ NPs. The TGA results indicate that the Co_xFe_3–xO₄ content in the obtained S2 and S4 samples is 18.4% and 30.4%, respectively. To confirm the composition of the obtained samples, Figure 3B provides their XPS spectra. It can be deduced that all the obtained NCs have four peaks located at 284, 530, 712, and 781 eV, respectively. Further, these peaks can be assigned to C 1s, O 1s, Fe 2p, and Co 2p.

FIGURE 3

Figure 3. (A) TGA curves, and (B) XPS spectra of the obtained samples.

To obtain the chemical valence states of Fe and Co, Figure 4A provides the high-resolution XPS spectra of Fe 2p. Four peaks, which are at ca. 711.2, 719.3, 724.6, and 731.4 eV, respectively, can be observed. Among these peaks, 711.2 and 724.6 eV can be assigned to the Fe 2p_3/2 and Fe 2p_1/2, while the other peaks correspond to the satellite peaks of Fe 2p_3/2 and Fe 2p_1/2. Similarly to the previous result (Yamashita and Hayes, 2008), the obtained result suggests the presence of Fe³⁺ in the obtained samples. As indicated in Figure 4B, the Co 2p high-resolution spectra also display four evident peaks. The peaks located at 780.9 and 796.6 eV originate from Co 2p_3/2 and Co 2p_1/2, and the peaks at 786.8 and 803.3 eV are the satellite peaks of Co 2p_3/2 and Co 2p_1/2, which indicate the existence of Co²⁺ ions (Bennet et al., 2016). In general, the obtained XPS results are consistent with their XRD patterns.

FIGURE 4

Figure 4. High resolution XPS spectra of (A) Fe 2p, and (B) Co 2p peaks for the as-prepared samples.

Figure 5 provides the morphologies of the as-prepared S1 and S2. As shown in Figure 5a,b it can be observed that larger quantities of Co_xFe_3–xO₄ and CoCO₃ NPs attached on the surface of GO and CNTs, similarly to the reported GO/CNT-Fe₃O₄ NCs (Wang et al., 2014). A closer TEM observation indicates that the NPs, CNTs, and GO nanosheets are well connected with each other to form a good three dimensional (3D) hierarchical networks structure. In the same manner as S1, as displayed in Figures 5c,d, the obtained S2 consists of large numbers of NPs, CNTs and paper-like GO, which presents a typical structure of 3D hierarchical networks. Combined with the XRD and XPS results, the conclusion suggests that the as-prepared S1 and S2 are 3D hierarchical networks structure of CoCO₃-Co_xFe_3–xO₄/CNTs/GO quaternary NCs. Equally, the TEM investigation of S3 and S4 (as presented in Figure 6) shows that they are composed of Co_xFe_3–xO₄ NPs with a relatively uniform size, CNTs and GO nanosheets, which bind together to establish the structure of 3D hierarchical networks. Unlike S1 and S2, the XRD, XPS and TEM results demonstrate that the as-prepared S3 and S4 are 3D hierarchical networks structure of Co_xFe_3–xO₄/CNTs/GO ternary NCs. Generally, with the Co:Fe increasing from 1:1 to 1:5, it is discovered that the prepared samples gradually undergo the transition from CoCO₃-Co_xFe_3–xO₄/CNTs/GO quaternary NCs to Co_xFe_3–xO₄/CNTs/GO ternary NCs, which is in agreement with our reported results (Wu et al., 2020). Compared to the binary NCs such as Co_xFe_3–xO₄/CNTs and Co_xFe_3–xO₄/GO, it is well recognized that the formed CoCO₃-Co_xFe_3–xO₄/CNTs/GO quaternary NCs and Co_xFe_3–xO₄/CNTs/GO ternary NCs can provide many more interface contacts. Further, the generated 3D hierarchical networks structure of our designed magnetic CNTs/GO NCs can provide a double loss mechanism and synergy effect among them, which is conducive to the attenuation of the EM wave. Generally, based on the previously reported papers and our obtained results (Lu et al., 2018; Shi et al., 2018), one can find that CoCO₃ will easily form under the condition of the existence of urea and a small quantity of Fe source. With the increasing amounts of Fe source, much more Co²⁺ will couple with Fe³⁺ to generate the Co_xFe_3–xO₄. Therefore, the obtained S2 should display a much higher content of CNTs/GO compared to S1. Moreover, with the formation of Co_xFe_3–xO₄ with large quantities, the obtained S3 has a larger Co_xFe_3–xO₄ content compared to S2.

FIGURE 5

Figure 5. TEM images of (a,b) S1, and (c,d) S2, respectively.

FIGURE 6

Figure 6. TEM images of (a,b) S3, and (c,d) S4, respectively.

It is well known that the value of minimum reflection loss (RL_min) and its corresponding frequency bandwidth (FB_cor), with the reflection loss (RL) values lower than −10 dB (90% EM wave absorption) are the important characteristic for measuring high performance MAs (Ye et al., 2018). Further, it is very desirable that MAs can simultaneously have a low RL_min and large FB_cor values. To investigate their MAPs, the values of RL were calculated based on the measured EM parameters and transmission line theory (Yusoff et al., 2002):

$$Z_{in}=Z_0\sqrt{\frac{\mathrm{\mu }}{\mathrm{\epsilon }}}\tanh \left(j\frac{2\mathrm{\pi }fd\sqrt{\mathrm{\mu }\mathrm{\epsilon }}}{c}\right)(1)$$

$$RL=20\log \left|\frac{Z_{in}-Z_0}{Z_{in}+Z_0}\right|(2)$$

Where f is the frequency of the EM wave, d is the thickness of absorber, c is the velocity of light, Z₀ is the impedance of air, and Z_in is the input impedance of absorber. Figure 7 provides the RL curves of S1, S2, and S3. As shown in Figures 7A,B, the RL_min and large FB_cor values for S1 are −54.69 dB at 11.08 GHz with the matching thickness (d_m) value of 8.57 mm and 2.36 GHz. The as-prepared S2 presents the RL_min value of −63.99 dB at 14.96 GHz with the d_m value of 6.60 mm (Figure 7C), and the FB_cor value of 2.48 GHz (Figure 7D), respectively. Equally, as shown in Figures 7E,F, one can find that the RL_min value for S3 is ca. −63.36 dB at 13.12 GHz with the d_m value of 7.95 mm, and its FB_cor value is 2.68 GHz. Moreover, the corresponding maximum absorption bandwidths (AB_max) with RL < −10 dB for S1, S2, and S3 (as provided in Figure 8) are 2.60 GHz with the d_m value of 7.69 mm, 2.72 GHz with the d_m value of 6.00 mm, and 3.08 GHz with the d_m value of 6.33 mm, respectively. In general, the designed magnetic CNTs/GO NCs display very outstanding MAPs. The as-prepared S3 exhibits the superior comprehensive MAPs compared to S1 and S2. As summarized in Figure 9, the proposed magnetic CNTs/GO NCs present excellent comprehensive MAPs compared to the representative related NCs reported previously (Li et al., 2015; Yang et al., 2016; Zhang et al., 2016; Zhang K.C. et al., 2017; Zhang S. et al., 2017; Ren et al., 2018; Shu et al., 2018a, b; Hu et al., 2019; Lu et al., 2019; Xu et al., 2019).

FIGURE 7

Figure 7. 3D color RL curves and their corresponding RL_min plots of (A,B) S1, (C,D) S2, and (E,F) S3.

FIGURE 8

Figure 8. Typical RL curves versus frequency plots for (A) S1, (B) S2, and (C) S3, respectively.

FIGURE 9

Figure 9. Comparison results of MAPs with the representative NCs reported in recent papers.

To effectively understand their MAPs, Figure 10 gives their complex permittivity (ε = ε′−jε″) and complex permeability (μ = μ′−jμ″). As shown in Figures 10A,B, besides the shift of peak at ca. 13 GHz, the as-prepared samples present the similar ε′ and ε″ variation tendency in the frequency region owing to the same categories of samples. The complex permittivity exhibits several resonant peaks in the whole frequency range, indicating the multiple relaxation processes (Huang et al., 2019). Furthermore, the ε′ and ε″ values of samples present the decreased tendency with the frequency increasing from 2 to 18 GHz, which can be explained by the Debye theory (Wang et al., 2015). Overall, the obtained S2 has larger values of ε′ and ε″ compared to S1 and S3, which can be ascribed to the highest content of CNTs/GO in the as-prepared S2. According to the previous result (Li et al., 2017), the ε′ and ε″ values could be effectively enhanced by increasing the content of CNTs. The obtained S3 presents the lowest values of ε′ and ε″, which should be ascribed to the gradual formation of Co_xFe_3–xO₄ with large quantities in NCs resulting in the decreasing content of CNTs/GO. Figures 10C,D present the μ′ and μ″ values of the obtained samples. Generally, it can be observed that the obtained samples exhibit the gradually growing μ′ and μ″ values with increased addition of Fe sources, which can be related to the enhanced content of Co_xFe_3–xO₄ NPs in the NCs. Figure 11 provides the dielectric loss (tan⁡δ_E = ε″/ε′) and magnetic capabilities (tan⁡δ_m = μ″/μ′). Overall, the as-prepared magnetic CNTs/GO NCs display much higher tan⁡δ_Evalues than those of tan⁡δ_m, which indicates that the attenuation of wave EM mainly originates from dielectric loss (Feng et al., 2020; Li et al., 2020). Moreover, the obtained S2 displays larger values of tan⁡δ_E compared to S1 and S3. Further, the large tan⁡δ_m values of S3 are higher than those of S1 and S2. The difference in dielectric loss and magnetic loss abilities should be related to the different CNTs/GO and magnetic Co_xFe_3–xO₄ NPs contents.

FIGURE 10

Figure 10. EM parameters for the as-prepared samples: (A,B) complex permittivity, and (C,D) complex permeability.

FIGURE 11

Figure 11. Frequency dependence (A) dielectric loss tangent, and (B) magnetic loss tangent of the as-prepared samples.

Based on the obtained EM parameters, RL curves and the previously reported mechanisms for the interpretation of the good MAPs (Liu et al., 2012, 2020), the excellent MAPs of the as-prepared magnetic CNTs/GO NCs can be explained by the geometrical effect. For this model, the values of d_m and peak frequency (f_m) should satisfy the 1/4 wavelength equation (Liu et al., 2020):

$${\text{d}}_m=nc\mathrm{/}4f_m\sqrt{\left|\mathrm{\mu }\right|\left|\mathrm{\epsilon }\right|}\begin{array}{}\end{array}(n=1,3,5\mathrm{\cdots })(3)$$

Figure 12 provides their comparison results between the experimental value of $d_m^{\exp }$ (obtaining directly from their RL curves) and their theoretical curves of ${\text{d}}_m^{sim}$ [plotting by the formula (3)]. One can find that the scattered dots of $d_m^{\exp }$ land on the theoretical curves of ${\text{d}}_m^{sim}$. Consistent with the CoNi@PRM-NC, ZnFe₂O₄@C, and CNTs@MoS₂ reported elsewhere (Gao et al., 2019; Yan et al., 2019; Wang et al., 2020), the agreement between the experimental and theoretical values suggests the cancelation effect of reflected EM waves and a strong EM wave attenuation.

FIGURE 12

Figure 12. Comparison results between the calculated and experimental matching thicknesses for (A) S1, (B) S2, and (C) S3.

Based on the previous models and our obtained results (Wang et al., 2014; Shu et al., 2018a), as depicted in Figure 13, as for our designed magnetic CNTs/GO NCs, the possible paths for the EM wave attenuation are mainly attributed to the following facts: (i) the 3D hierarchical networks structure results in the multiple reflections and/or scattering of the EM wave (Figure 13A), which plays a significant role in the EM wave attenuation; (ii) many more interface contacts among magnetic NPs, CNTs, and GO nanosheets (Figure 13B) induce the formation of interface polarization with large quantities, which can effectively dissipate the energy of the incident EM wave; (iii) the designed NCs consisted of dielectric substances and magnetic NPs (Figure 13C), which can simultaneously provide the dielectric and magnetic loss mechanism. The excellent synergistic effect between them further improves the attenuation of the EM wave; (iv) the high conductivity of GO/CNT and a large number of defects and functional groups existing on CNTs (Figure 13B) and GO (Figure 13D) can generate massive electrons, defect dipoles and interface polarizations, which are also conducive of the dissipation of the EM wave.

FIGURE 13

Figure 13. Schematic illustration of possible EM wave absorption avenues of magnetic CNTs/GO NCs. (A,B) Multiple reflections, (C) dielectric and magnetic loss, and (D) defect dipole and interface polarization.

Conclusion

In summary, we proposed a one-step hydrothermal method to selectively synthesize different compositions of magnetic CNTs/GO NCs such as CoCO₃-Co_xFe_3–xO₄/CNTs/GO quaternary NCs and Co_xFe_3–xO₄/CNTs/GO ternary NCs. The TEM investigation indicated that the designed NC consisted of CoCO₃-Co_xFe_3–xO₄ NPs, CNTs, and GO nanosheets, which were well bound together to form the good 3D hierarchical networks structure. Owing to the construction of many more interface contacts among magnetic NPs, CNTs, and GO nanosheets, an excellent synergistic effect between dielectric and magnetic loss substances, the as-prepared magnetic CNTs/GO NCs presented very extraordinary MAPs. The RL_min and FB_cor values for the as-prepared samples were ca. −54.69 dB and 2.36 GHz, −63.99 dB and 2.48 GHz, −63.36 dB and 2.68 GHz, respectively. Moreover, owing to their low cost, lightweight and high stability, the proposed 3D hierarchical networks structures of magnetic GO/CNTs NCs exhibit very outstanding comprehensive MAPs, which may be used as promising candidates for high performance MAs and are very much worth further study.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation, to any qualified researcher.

Author Contributions

MW contributed to the conceptualization, methodology, investigation and provided resources. XQ contributed to the conceptualization, methodology and writing of the original draft of the manuscript. RX contributed to the investigation. SQ provided supervision, and contributed to the writing, review and editing of the manuscript. CD provided formal analysis and resources. WZ contributed to the methodology, and the writing, review and editing of the manuscript.

Funding

This work was supported by the Fund of Fok Ying Tung Education Foundation, the Platform of Science and Technology and Talent Team Plan of Guizhou Province (2017-5610 and 2017-5788), the Major Research Project of Innovative Group of Guizhou Province (2018-013), the National Science Foundation of Guizhou Province (2017-1034), and the National Natural Science Foundation of China (Grant Nos. 11474151, 11604060, and 11964006) for financial support.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

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