Xin Hao*
International College, Zhengzhou University, Zhengzhou, Henan Province 450000, P. R. China. E-mail: haoxinzzu@163.com
First published on 2nd August 2021
High-efficiency, porous and renewable magnetic microwave absorbing (MA) materials have been enthusiastically pursued due to their suitable impedance matching, light weight, strong multiple scattering and the synergy effect of dielectric and magnetic loss. Herein, a three-dimensional (3D) Co@C/ANF aerogel, composed of magnetic MOF derivatives embedded in biomass aramid nanofiber (ANF), was prepared for the first time through a directional-freezing method followed by an annealing process. To evaluate their MA attenuation performance, the electromagnetic parameters of Co@C/ANF composites with different component ratios were measured at 2–18 GHz. Profiting from the preserved porous structure of MOF derivatives, the construction of multiple heterogeneous interfaces and suitable electromagnetic parameters, Co@C/ANF 2:1 exhibited a good MA performance of RLmin = −64.3 dB (indicating more than 99.99996% microwaves were absorbed) and EABmax = 6.8 GHz. Considering the admirable overall performance, the Co@C/ANF aerogel is deemed to be a promising candidate for the next-generation of lightweight, reproducible, and high-performance MA materials.
Recently, 3D metal organic frameworks (MOFs) composed of metal ions/clusters and organic ligands, with large specific surface area and adjustable microstructure, has widely received attention in gas storage, supercapacitors, batteries, information storage and sensors.16–18 Typically, in MA materials field, porous magnetic MOFs derivatives (products of MOF after annealing or other treatments) can also play an obvious role. Especially, the shape of the polyhedron can cause multiple reflections, and the microwave injected into the hollow MOF hole can increase the transmission path and the probability of being fully absorbed, so as to obtain a strong absorbing performance. For example, Lü et al. prepared porous Co/C composite nanomaterials, through annealing ZIF-67 at different temperatures, with the RLmin of Co/C-500 is −35.3 dB and an effective absorption bandwidth (EAB) = 5.80 GHz.19 The excellent MA performance confirms the feasibility of MOF derivatives as a MA material. Subsequently, Wang et al. introduced an inorganic shell outside the MOF derivative, which reduced the incident resistance of microwaves, resulting SnO2/Co3Sn2@C hybrid can receive an optimal RLmin value of −56.2 dB.20 Nevertheless, the problem of high content (30 wt%) caused by the possible agglomeration of magnetic MOF derivative materials in matrix still needs to be further solved. Hopefully, Ji et al. used melamine foam as the skeleton of MOF derivatives to prepare a 3D porous network structure, and the obtained microwave absorption effect can be increased to the RLmin value of −59.82 dB.21 In addition, the hybrid aerogel also has excellent infrared invisibility and heat insulation, revealing the bright future of MOF derivatives/aerogel multifunctional MA materials. Therefore, choosing a key dielectric material as the 3D framework of the magnetic MOF derivative can rich the polarization site of the microwave, the scattering interface and the synergistic loss effect of aerogel, and it is an effective means for designing high-efficiency MA materials.
Aramid nanofibers (ANF) is a promising candidate to have great application potential for next-generation pollution-free materials with excellent thermal conductivity, renewable and biocompatible.22–24 Since uniformly dispersed ANF was first prepared by Kotov and co-workers, due to its high porosity, large specific surface area, high aspect ratio, unique nanoscale effects and higher mechanical strength than CNF, it has been widely used in many emerging fields such as thermal conductivity, EMI shielding and energy, etc. Theoretically, aerogels benefiting from the combination of porous and dielectric biomass cellulose and MOF derivatives can effectively introduce microwaves and gradually attenuate them through multiple reflections. However, as far as well know, there are few reports on the application of ANF in microwave absorption, especially MOF derivatives/ANF aerogel EM material.
In this work, Co@C/ANF aerogel was successfully fabricated through the gentle ammonia annealing process using ZIF-67/ANF composite as a precursor. Subsequently, by changing the ratio of ZIF-67 to ANF, the electromagnetic parameters of Co@C/ANF were well adjusted, which affected the overall absorbing performance of the aerogel. As expected, with multiple heterogeneous interfaces, hierarchical pore structure, dielectric and magnetic loss effects, the results indicate that Co@C/ANF 2:1 can possess outstanding MA performances of RLmin = −64.3 dB at 3.5 mm and an EABmax of 6.8 GHz. Taking the lightweight aerogel structure of Co@C/ANF, excellent environmental friendliness and strong wave absorbing performance into account, this work opened up a new journey in the design of ANF-based magnetic MA materials.
The TEM result further proves the internal microstructure of Co@C/ANF aerogel. As shown in Fig. 1g, the microframes retained the ZIF-67 shapes, confirmed the formation of core–shell structures of Co@C polyhedral particles and embedded onto ANF nanosheets. The high-resolution TEM images are shown in Fig. 1h and i. It can be found that the lattice fringe of 0.20 nm for encapsulated nanoparticles core corresponds to the well-resolved (111) lattice plane of Co nanoparticle, indicating a core–shell structure composed of cobalt nanoparticle cores and carbon nanosheet shells was successfully prepared, which is consistent with the SEM pattern results.
XRD analyses were used to confirm the crystalline structure and the constituents of the Co@C/ANF samples. As shown in Fig. 2a, the ZIF-67/ANF composite inherits the diffraction peaks of ZIF-67 and ANF (Fig. S3a, ESI†) completely. The ZIF-67 XRD pattern can be assigned to (011), (002) (112), and (222) crystal planes, which matches well with previous reports, proving the successful synthesis of ZIF-67.26,27 For the Co@C/ANF aerogel, the disappeared characteristic peak of ZIF-67 indicating the change in the crystal structure of ZIF-67 during calcination. The emerging four peaks in the Co@C/ANF composite at 44.2°, 51.5°, and 75.8° can be assigned to the (111), (200), and (220) crystal planes of cobalt metal (PDF# 15-0806), implies the formation of Co nanoparticles. Besides, the Co@C/ANF aerogel still retains the previous characteristic peaks of the calcined ANF, which can be speculated that the structure of ANF was reserved. To further confirm the changes in the composites, XPS analysis was used to analyze the chemical composition of ZIF-67/ANF and Co@C/ANF. The results confirmed the presence of C, N, C, O, and K elements in the samples (Fig. 2b). Interestingly, weak K 2p3 and N 1s peaks in ZIF-67/ANF can be observed at 293 eV and 401 eV, respectively, which is due to the use of KOH in the preparation of ANF and exist of N element in ANF. Precisely, Co@C/ANF shows the increasing N atom ratio, which implies a large amount of N atoms doping and defects are introduced during the annealing process. In Fig. S3 (ESI†), the prominent peaks at 398.5 and 400.5 in the N 1s spectrum reveal the formation of pyrrole nitrogen and pyridine nitrogen. Moreover, the C 1s signals at binding energies of 284.8 and 285.6 are attributed to CC and C–N.25 As for the specific chemical valence state of the element Co, the signals located at 778.3 eV and 793.5 eV can be attributed to 2p3/2 and 2p1/2 of Co, respectively, and the peaks at 781.5 eV and 796.4 eV correspond to the satellite peaks.28 The XPS spectrum of Co element once again shows the formation of Co metal crystal particles, which is consistent with the XRD results.
Fig. 2 (a) XRD patterns of Co@C/ANF and ZIF-67/ANF. (b) XPS spectra of Co@C/ANF and ZIF-67/ANF. (c) FT-IR spectra of Co@C/ANF. (d) Hysteresis loops of Co@C/ANF and ZIF-67/ANF. |
FT-IR analysis was performed to characterize the change of functional groups before and after transformation of aerogels. Evidently, there is a broad peak at 3437 cm−1 that corresponded to the –OH in the curve (Fig. 2c). In addition, the Co@C/ANF aerogel shows distinct bands at 1653, 1380, and 1129 cm−1, which are correspond to CO, N–H, and C–N, respectively, shows a similar peak to ZIF-67/ANF. The presence of oxygen/nitrogen-containing carbon bonds indicates that the annealed aerogel still retains some functional groups, which is conducive to the loss of dipolar polarization in the alternating electromagnetic field. Fig. 2d shows the magnetization hysteresis lines of ZIF-67/ANF and Co@C/ANF aerogels, where ZIF-67/ANF composite shows an almost flat line, indicating its non-magnetism property. On the contrary, the hysteresis curve of the ANF/MOF composite shows a typical ferromagnetic behavior, giving the hybrid material magnetic loss capability. Intriguingly, the Co@C/ANF composite exhibits a higher Hc (830 Oe), which can facilitate the natural resonance and enhance the magnetic loss of MA performance.
Generally, the MA property can be estimated from the reflection loss curve. According to transmission line theory, the value of RL can be calculated by the following equation.29–31
(1) |
RL (dB) = 20log|(Zin − Z0)/(Zin + Z0)| | (2) |
The MA behavior of the Co@C/ANF aerogel was investigated in the frequency range of 2–18 GHz. Fig. 3 shows the RL curves of ANF and Co@C/ANF aerogels with different thicknesses. Overall, it is first observed that the peak frequency of the RL curves shifts to the lower frequency region with an increased thickness of the absorber, which can be explained by the quarter-wavelength (λ/4) cancelation theory.32,35 Simultaneously, it can be found that the synthesized Co@C/ANF aerogels have significant performance advantages over pure ANF MA materials in Fig. 3a (RLmin = −22.37 dB). With the content of MOF derivatives increased, according to Fig. 3b, it can be observed that the RLmin value of Co@C/ANF 1:2 was −37.9 dB with EAB of 4.7 GHz. For the Co@C/ANF 1:1, the RLmin value is −30.4 dB at 2.5 mm (Fig. 3c). Particularly, Fig. 3d shows that Co@C/ANF 1:2 exhibits an excellent MA characteristic and the RLmin value can reach −64.3 dB at 3.5 mm. Intuitively, the 3D and 2D absorbing effects of the Co@C/ANF 2:1 are shown in Fig. 3e and f, respectively. By changing the thickness, the RLmin of Co@C/ANF 2:1 can achieve an EABmax of 6.8 GHz at 2.5 mm. Through the comparison with the materials in the literature (Table 1), the advantages of Co@C/ANF 2:1 are further highlighted. Considering the overall MA capacity, it can be concluded that Co@C/ANF 2:1 exhibits the best MA performance with small RLmin, thin thickness, and wide EAB.
Fig. 3 Reflection loss curve of (a) ANF (b) Co@C/ANF 1:2 and (c) Co@C/ANF 1:1 at 2–18 GHz. (d) 2D, (e) 3D and (f) flat reflection loss graph of Co@C/ANF 2:1. |
Material name | Matrix | Filler loading (wt%) | Thickness (mm) | RLmin (dB) | EAB (GHz) | Ref. |
---|---|---|---|---|---|---|
Fe–Co/NC/RGO | Wax | 25 | 2.5 | −33.26 | 9.12 | 2 |
ZIF-67@CoNi | Wax | 30 | 2.5 | −58.2 | 4.03 | 13 |
Fe–Co/NPC | Wax | 50 | 1.2 | −21.7 | 5.8 | 15 |
Ni@C-ZIF | Wax | 40 | 2.7 | −86.8 | 7.4 | 17 |
FeCoNi@C | Wax | 38 | 2.1 | −64.75 | 8.08 | 18 |
Co/C | Wax | 40 | 2.5 | −35.3 | 5.80 | 19 |
Co1.29Ni1.71O4 | Wax | 50 | 1.6 | −50.7 | 4.84 | 30 |
Fe3O4/CNT | Wax | 30 | 8.3 | −28.7 | 1.75 | 32 |
CS/MoS2 | Wax | 30 | 1.4 | −52.6 | 4.9 | 33 |
Co@C/ANF 2:1 | PVDF | 10 | 3.5 | −64.3 | 4.5 | This work |
Co@C/ANF 1:2 | PVDF | 10 | 2.5 | −46.3 | 6.8 | This work |
Co@C/ANF 1:1 | PVDF | 10 | 3 | −37.9 | 4.8 | This work |
According to the energy conversion principle, the MA property is strongly related to relative complex permittivity (εr = ε′ − jε′′) and the complex permeability (μr = μ′ − jμ′′).36 Specifically, the ε′ and μ′ are mainly associated with the storage capacity of microwave energy, and the ε′′ and μ′′ are connected with the dissipation capability of electrical and magnetic energy.33,37 From Fig. 4a, it can be found that ε′ values gradually decrease from 11.5 to 4.2 for different samples. In an alternating electromagnetic field, the existence of a heterogeneous interface will cause electrons to shift and polarization will occur. However, as the frequency increases, when the polarization cannot keep up with the frequency, the real part of the dielectric constant will decrease, which explains the change in the dielectric constant. Besides, as shown in Fig. 4b, the Co@C/ANF composites present a lower value of ε′′ compared to ANF. Due to the addition of ZIF-67, the conductive path of ANF is isolated, then the resistivity of Co@C/ANF composite is higher compared to ANF and this phenomenon can be explained by the free-electron theory (ε′′ ≈ 1/2πε0ρ). Moreover, several resonance peaks can be observed on the ε′′ curve (Fig. 4b), proving the presence of multiple polarization relaxation in the composite. Based on the free-electron theory and the Debye theory, the relationship between ε′ and ε′′ can be expressed by the following equation.38,39
(3) |
Fig. S4† shows the curves of ε′' and ε′′, where a single semicircle is denoted as a Cole–Cole semicircle, and if the curves form a semicircle it represents that a relaxation process may occur.40 It can be seen that various multiple semicircles and small tail appear in the ε′–ε′′ curves of Co@C/ANF samples, indicating that polarization relaxation contributed to their MA absorption performance, and conductance loss mechanism is exist. In addition, the Cole–Cole semicircles in these samples overlap and are distorted, which indicating that other mechanisms, such as Maxwell–Wagner relaxation and electron polarization, also contribute to the dielectric properties in addition to the Debye relaxation.41,42
For the complex permeability, the μ′ and μ′′ values for samples exhibit a similar trend in 2–18 GHz. Fig. 4c and d show the magnetic permeability of different samples, although more ZIF-67 (Co@C/ANF 2:1) achieve a high magnetic permeability, the magnitude of the magnetic permeability between different samples is not large. As we know, for the magnetic materials, magnetic losses are mainly attributed to natural resonance, eddy current effect, and domain wall resonance. The eddy current loss caused by the eddy current effect can be expressed as C0.43,44 If the value of C0 is the dominant factor causing the magnetic loss, then C0 remains constant over the entire frequency range. However, significant fluctuations were detected in the C0 curves for all samples, suggesting that the magnetic losses are mainly caused by exchange resonance and natural resonance effects (Fig. S5a, ESI†).
Dielectric loss angle tangent and magnetic loss angle tangent are two important factors to evaluate the absorbing performance of MA materials. According to ε′ ε′′ μ′ and μ′′, the curves of dielectric loss angle tangent and magnetic loss angle tangent can be obtained by using the following equations tanδε = ε′′/ε′ and tanδμ = μ′′/μ′. As displayed in Fig. 5, it is obvious that the tanδε values of all composites are far larger than the tanδμ values, showing that dielectric loss plays a dominant role in the composite absorber. In general, the higher the value of dielectric loss angle tangent, the more electric energy of incident microwave can be dissipated. Compared to other samples, Co@C/ANF 2:1 shows a higher tanδε values. This should originate from its high ε′′ value at 8–12 GHz, confirming that the Co@C/ANF 2:1 has a more outstanding dielectric loss performance at 8–12 GHz. However, Fig. S5b (ESI†) exhibits that tanδε + tanδμ of pure ANF is larger than that of the Co@C/ANF composites, which means that the combined microwave loss capability of the composite is lower than that of ANF.
Fig. 5 The loss angle tangent and the magnetic loss angle tangent of (a) ANF, (b) Co@C/ANF 1:2, (c) Co@C/ANF 1:1 and (d) Co@C/ANF 2:1. |
To further investigate the MA mechanism of Co@C/ANF, the attenuation coefficient and impedance matching should be introduced. Attenuation coefficient (α) and impedance matching are the key factors affecting the absorbing performance of composite materials, which determine the entry capacity and inherent attenuation capacity in the microwave wave absorber.45 As shown in Fig. 6a, within a certain range, ANF shows the highest α value in almost the entire frequency. This may be because of its high values of ε′′. Although the loss capability of pure ANF is stronger than the Co@C/ANF composite, on the whole, they both have high tanδε + tanδμ values and attenuation constants and maintain a strong MA capability.
Generally, as the ratio of the input impedance of the absorber to the free space impedance (|Zin/Z0|) is equal to 1, most of the microwaves can easily enter the absorber, which helps to improve the MA performance.46 The impedance matching of the Co@C/ANF 2:1 sample vs. frequency is presented in Fig. 6b, and it can be found that the impedance matching of Co@C/ANF 1:2 is close to 1. Therefore, for the Co@C/ANF 2:1, microwave can be easily incident into the absorber then attenuated rather than reflected at the absorber surface. Interestingly, in the left point (around 10 GHz) of the impedance in Co@C/ANF 2:1 is equal to 1, but the optimal RL value cannot be obtained due to the weak attenuation capabilities. Therefore, it can be concluded that the appropriate impedance matching and strong attenuation capability are two important factors for obtaining excellent absorbing properties. Fig. S6 (ESI†) shows the impedance matching of the four samples at different thicknesses. These results demonstrate that excellent impedance matching is the first element for their excellent MA performance.
Based on the above discussions, the MA characteristics of Co@C/ANF composite are mainly determined by the following factors (Fig. 7): (i) the introduction of MOF derivative particles implies a higher resistance in the Co@C/ANF aerogel, leading to excellent impedance matching and resulting in more microwaves reaching the material.47 (ii) The hollow-porous structure of Co@C/ANF composite extends the propagation range of incident waves, producing various reflection and scattering events that benefit the conversion of microwaves into other forms of energy.48,49 (iii) The addition of a large amount of MOF derivative particles can bring more interfaces, leading to interfacial polarization and dipole polarization between MOF derivative and ANF, resulting in microwave energy attenuation.50 For magnetic losses, eddy current effects and natural resonance play a major role in enhancing microwave absorption. Therefore, considering the excellent over all microwave attenuation capacity, Co@C/ANF 2:1 can be a promising and attractive absorber for application in the MA field.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/d1ra04725f |
This journal is © The Royal Society of Chemistry 2021 |