# Amorphous/Nanocrystalline Carbonized Hydrochars with Isomeric Heterogeneous Interfacial Polarizations for High-performance Microwave Absorption

• 327 Accesses

## Abstract

Carbon allotropes and their derivatives have exhibited superior performances for microwave absorption ascribed to their dielectric attenuation capacity raised from the multiple dipolar configurations. Such characteristics could be achieved by constructing diverse micro/nanoscale architectures, incorporating vacancies and heteroatoms, and composing with heterogeneous components. Alternatively, we herein present a facile approach for the synthesis of carbonized hydrochars, which are composed of dispersed ultrafine nanocrystallines graphite and amorphous matrix. Such a isomeric construction has a high-density interfaces, accompanied with significant interfacial polarizations, leading to the improvement of microwave absorbing capabilities. For carbonized hydrochars, the RLmin value can reach −40.36 dB, and corresponding effective bandwidth is 2 GHz. This work provides a concept for designing microwave absorption materials based on isomeric heterogeneous interfacial polarizations in single-element systems.

## Introduction

In the present era of high-end technology, electronic devices and communication facilities have become an dispensable part of nearly every aspect of daily life. However, the accompanying electromagnetic pollution problem has turned to be increasingly serious due to its damages to human beings and environment. Microwave absorption materials have drawn attention of researchers in industrial, commercial and military fields1, which could absorb or dissipate electromagnetic energy effectively2. The ideal microwave wave absorbers with merits of thin thickness, broad effective bandwidth, high absorptive capacity, low filler loading ratio and light weight are highly desirable at present3,4. To date, various microwave absorption materials have been successfully prepared, including dielectric loss materials, such as ZnO5,6, magnetic loss materials, for example Ni7, ferrite8,9,10 and composites materials such as CoFe2O4/graphene oxide11, Fe3O4@C12, Ni@SnO213, Fe3O4/silica14, FeSn2/Sn/graphite15, CoNi@SiO2@TiO216, which exhibit attracting microwave absorption performance.

Carbon allotropes and their derivatives have been extensively developed in the field of energy conversion due to their various forms, tunable physical and chemical properties and chemical stability17,18,19,20,21,22,23. Carbon-based microwave absorption materials, such as, porous carbon24, carbon fibers25, polyaniline26, carbon nanotubes (CNTs)27,28, graphene5,29, reduced graphene oxide (RGO)30,31, and carbon microspheres3,32,33,34,35, exhibit superior microwave absorption properties due to their dielectric attenuation capacity raised from the multiple dipolar configurations. Most often, the conventional synthetic strategies for carbon-based microwave absorption materials are constructing diverse micro/nanoscale architectures27,29,32,33, incorporating vacancies and heteroatoms30,36 and composing with heterogeneous components24,25,26. However, the relative research on synthetic strategy based on constructing isomeric heterogeneous interfaces is rarely reported.

In this paper, carbonized hydrochars composed of dispersed ultrafine nanocrystallines graphite and amorphous matrix have been successfully prepared on the basis of synthetic strategy of constructing isomeric heterogeneous interfaces. This unique isomeric construction with high-density interfaces between amorphous matrix and nanocrystalline graphite, accompanied with significant interfacial polarizations, leading to the improvement of microwave absorbing capabilities. Moreover, a very thin thickness of absorber can be achieved (minimum thickness for reflection loss less than −10 dB), comparing with other carbon-based materials, which manifests total weight of microwave absorption composites can be substantially lower for practical applications.

## Results and Discussion

Initially, a series of experiments were conducted at 700 °C, 800 °C and 900 °C, while carbonized period was set to 30 min in this stage. The SEM images of hydrochars and carbonized products reacted at 700 °C, 800 °C, 900 °C for 30 min are shown in Fig. 1, the spherical morphologies of hydrochars and carbonized products could be clearly observed with some bonding particles, which are similar to each other. After carbonization, the mean diameters of products are around 700 nm, which are less than that of hydrochars, in accordance with size change trend of spherical activated carbons reported in previous literature37,38.

The XRD spectra of original hydrochars (designated as “Original” in Fig. 2), carbonized hydrochars reacted at 700 °C, 800 °C and 900 °C for 30 min are presented in Fig. 2a. It is obvious that the original hydrochars group shows a broad hump at 21.2°, which can be ascribed to amorphous carbons. However, there are two broad diffraction peaks at around 22° and 44° for all three types of carbonized hydrochars. It has been reported that small domains of stacked crystalline graphite can be formed after high temperature carbonization, whose diffraction peaks locate at 24.3° and 44.8°39. For all three types of carbonized hydrochars mentioned above, the peaks at around 22° results from existence of nanocrystallines graphite and amorphous carbons after carbonization, while the peak at around 44° corresponds to the graphite (101) plane (JCPDS 26-1079). Besides, the peak at around 22° moves towards large angle with the increase of carbonized temperature (indicated by dashed lines in Fig. 2a), indicates an increase in amount of nanocrystalline graphite.

Figure 2b shows the Raman spectra of original hydrochars, carbonized hydrochars reacted at 700 °C, 800 °C and 900 °C for 30 min. All four spectra show two different peaks, the one located at around 1350 cm−1 (D band), while the other centered at 1590 cm−1 (G band). Herein, the ID/IG value increases with carbonized temperature from 0.815 (Original) to 0.981 (900 °C). As previously reported literature40,41,42, near K zone boundary, D band resulted from A1g symmetry breathing mode involving phonons is active with the existence of nanocrystalline graphite or disorder; G band resulted from E2g symmetry mode originates from in-plane bond-stretching motion of carbon sp2 atom pairs. Besides, Ferrari et al. brought forward a transition model from graphite to amorphous carbon (ta-C) based on changes of ID/IG, and the enlarged ID/IG value is derived from evolution of amorphous carbon to nanocrystalline graphite42. In other word, enlarged value of ID/IG at carbonized temperature indicates the amount of nanocrystalline graphite increases for carbonized hydrochars, which is exactly consistent with XRD results above.

Further details of the chemical structure of original hydrochars, carbonized hydrochars reacted at 700 °C, 800 °C and 900 °C were conducted, as shown in Fig. 2c,d. The C 1 s spectra are fitted with C-C, C-O, C=O and O-C=O functional groups, located at 284.6, 286.2, 287.8 and 289.0 eV, respectively3,5,43. For all three types of carbonized hydrochars, no signal of C=O functional group has been detected. Besides, their corresponding reducing signal areas of oxygen-containing functional groups (C-O, C=O, O-C=O), as well as enlarging signal area of C-C functional group indicate relative contents of oxygen-containing functional groups decrease, compared with signal areas of original hydrochars. And the O 1 s spectra could be deconvoluted into two individual component peaks at 533.1 and 531.7 eV, corresponding to the -C-O, -O-H bonds3,44. From Fig. 2d, we could also observe the obvious signal area changes of both -C-O and -O-H functional groups between original hydrochars and three types of carbonized hydrochars. More specifically, the relative content of -C-O functional groups drastically decreases after high temperature carbonization. These results above are closely interrelated with transition from amorphous carbon to nanocrystalline graphite.

It has been reported that small domains of stacked crystalline graphite are extremely difficult to be detected by TEM technique39. Herein, carbonized hydrochars reacted at at 800 °C for 20 min were selected for TEM characterization by means of ultrathin sections with the thickness of 40 nm. During process of TEM characterization, we found that nanocrystallines graphite were uniformly dispersed in carbonized hydrochars with sizes slightly varying from each other and that amorphous carbons without crystallization in large amount could be observed. The typical HRTEM images of carbonized hydrochars reacted at 800 °C for 20 min are shown in Fig. 3a,b. Figure 3a provides a clear view of nanocrystalline graphite particles with size of about 5 nm, which marked by red dotted line. And Fig. 3b, obtained from higher magnification, reveals that corrugated parallel fringes with basal spacing values of 0.196 nm and 0.208 nm depict the lattice-resolved (012) and (101) crystalline planes of graphite structure. Moreover, some small black regions with incomplete crystallization and lattice distortions resulted from atom dislocations could be clearly observed in Fig. 3a,b, respectively, indicating many defects existed in the domains of nanocrystalline graphite, which could be polarized centers. And the TEM results above are coincident with the XRD patterns of carbonized samples. More specifically, the broadening of (101) graphite diffraction peak has a strong relationship with defects in the domains of nanocrystalline graphite during the transition from amorphous carbons to crystalline graphites.

The microwave absorption performance of carbonized hydrochars reacted at 700 °C, 800 °C and 900 °C for 30 min were investigated by measuring relative complex permittivity (εr = ε′ − jε″) as well as relative complex permeability (μr = μ′ − jμ″). And corresponding real and imaginary permittivities are presented in Fig. 4a–c, ε′ values of three samples are in the range of 6.9–3.5, 24.4–9.8 and 53.0–22.4, respectively, indicating a decreased tendancy with increased frequency. Similarly, ε″ values of three samples decrease along with the increasing frequency, and they are in the range of 3.4–0.8, 26.7–4.0 and 106.1–16.6, respectively. And their corresponding dielectric dissipation factors (tanδe = ε″/ε′) are presented in Fig. 4d. In contrast to the features of complex permittivity, complex permeability for three samples show little change ranged from 1 to 18 GHz. And the complex permeability for all three types of carbonized hydrochars are close to unity (μ′ and μ″ at around 1 and 0), as shown in Fig. S1 (Supporting Information).

From the transmission line theory, the reflection loss (RL) values of microwave can be acquired by measuring the complex permittivity and complex permeability45,

$${Z}_{in}={Z}_{0}\sqrt{\frac{{\mu }_{r}}{{\varepsilon }_{r}}}tanh[j(\frac{2\pi fd}{c})\sqrt{{\mu }_{r}{\varepsilon }_{r}}]$$
(1)
$${\rm{RL}}\,(dB)=20log|\frac{{Z}_{in}-{Z}_{0}}{{Z}_{in}+{Z}_{0}}|$$
(2)

where Zin is the normalized input impedance, Z0 represents the impedance of free space, εr and μr refer to the complex permittivity and complex permeability, respectively, f is the frequency of microwave, d is the absorber thickness, and c is the velocity of light.

The 3D graphs of RL values for carbonized hydrochars with different thickness with paraffin loading ratio of 50 wt.% are displayed in Fig. 5a–c, and RL curves with different thicknesses are shown in Fig. S2 (Supporting Information). It can be found that the minimums of RL value for all three types of carbonized hydrochars shift toward lower frequency with increased thickness, which can be explained by quarter-wavelength cancellation model7,46,47. For the hydrochars carbonized at 700 °C for 30 min, the minimum RL value achieves −12.08 dB with the thickness of 4.12 mm (9.84 GHz). The RL values of carbonized hydrochars reacted at 900 °C with arbitrary thickness don’t exceed −10 dB with frequency range from 1 to 18 GHz (minimum: −6.17 dB at 16.30 GHz). It is noteworthy that the carbonized hydrochars reacted at 800 °C exhibits excellent absorption performance towards microwaves, especially at 10.35 GHz, the minimum RL value can achieve −28.20 dB with 2.02 mm thickness, and corresponding effective bandwidth (RL value <−10 dB, 90% microwave attenuation) reaches 2.1 GHz.

The ability of dielectric loss originated from polarization loss and conductivity loss has been widely accepted, and the loss of polarization includes interfacial polarization, dipole orientation polarization, ionic polarization and electronic polarization48. Usually electronic polarization and ionic polarization are found at high frequency range (103–106 GHz), so their effects could be easily eliminated48. Herein, isomeric heterogeneous interfacial polarizations as well as dipole polarizations resulted from incomplete crystallization and lattice distortions contribute enormously to microwave absorption. The specific isomeric structure guarantees induced charges accumulation on the interfaces between amorphous matrix and nanocrystalline graphite. Under alternating electromagnetic field, it is favorable for induced charges to migrate to response external electromagnetic field, which results in electromagnetic energy loss.

According to the free electron theory49,50,51,52, the electrical conductivity of absorbers can be simply estimated based on the equation as below:

$$\varepsilon ^{\prime\prime} =\frac{\sigma }{\omega {\varepsilon }_{0}}=\frac{\sigma }{2\pi f{\varepsilon }_{0}}\to \sigma =2\pi f{\varepsilon }_{0}\varepsilon ^{\prime\prime}$$
(3)

where f is frequency, ε0 represents the permittivity of free space (ε0 = 8.854 × 10−12F·m−1), and ε″ is the imaginary permittivity. Figure 5d exhibits the calculated electrical conductivity of above three absorbers in alternating electromagnetic field. Apparently, the carbonized hydrochars reacted at 700 °C for 30 min presents the lowest electrical conductivity with no more than 1 S m−1, and the carbonized hydrochars reacted at 900 °C has relatively high conductivity (6–18 S m−1). Both two types of carbonized hydrochars above show relatively poor microwave absorption performance. This is because lower carbonized temperature or shorter carbonized period would reduce the degree of removal of oxygen-containing functional groups and decrease the amount of isomeric heterogeneous interfaces between amorphous matrix and nanocrystallines graphite, which have an adverse effect on isomeric heterogeneous interfacial polarizations and dipole polarizations, leading to poor microwave absorption property. And for higher carbonized temperature case, only high complex permittivity (ε′ and ε″) could not obtain outstanding microwave absorbing performance when considering the matched characteristic impedance. The matched characteristic impedance of absorbers should be equal to 377 Ω sq−1 for the achievement of zero-reflection at the materials front surface33,49. In general, the distinction of complex permeability and permittivity does harm to the matched characteristic impedance, which leads to a strong reflection of incident microwave33,43. The above results illustrate that electrical conductivity within an appropriate range is extremely crucial for absorbers in this work, high electrical conductivity would lead to impedance mismatch, and the weak isomeric heterogeneous interfacial polarizations and dipole polarizations are inevitable when corresponding electrical conductivity is relatively low.

In order to further optimize the experimental parameters, herein, four samples of hydrochars were selected in this experimental group under different carbonized periods (15, 20, 30 and 40 min), while carbonized temperature maintained at 800 °C. As mentioned above, all these four samples after carbonization show ε′ and ε″ at around 1 and 0 (not shown). Obviously, as shown in Fig. 6, complex permittivity curves for carbonized hydrochars reacted for 15, 20, 30 and 40 min vary from each other, and there are some fluctuations for ε′ and ε″ in high frequency range. The ε′ values of corresponding sample are 28.5–14.8, 24.8–12.3, 24.4–9.8 and 43.9–21.2, while their ε″ values are in the range of 25.4–6.5, 18.9–4.3, 26.7–4.0 and 128.6–15.4, respectively.

The 3D graphs of RL values and RL curves with different thicknesses for carbonized hydrochars reacted at 800 °C for 15, 20, 30 and 40 min are clearly shown in Figs 7 and S3 (Supporting Information), respectively. As observed, the minimum RL value of the hydrochars carbonized for 40 min could not reach −10 dB (90% microwave attenuation). Most noteworthy, carbonized hydrochars reacted for 20 min exhibits obviously enhanced microwave absorbing capability, especially at absorber thickness of 1.93 mm, the RLmin value can achieve −40.36 dB at 10.18 GHz, and their effective bandwidth is 2 GHz (9.3–11.3 GHz), as shown in Fig. S3b. As for carbonized hydrochars reacted for 15 min, their minimum RL value is −19.58 dB (9.50 GHz, thickness 1.91 mm), and their corresponding effective bandwidth is 1.7 GHz (8.6–10.3 GHz). Therefore, the hydrochars carbonized for 20 min exhibits outstanding microwave absorption performance among absorbers in this work, and its absorption properties could be modified by varying the thickness of absorbers in practical applications.

Figure 8 exhibits the calculated electrical conductivity of carbonized hydrochars reacted at 800 °C for different periods in alternating electromagnetic field. Some absorbers in this work (carbonized hydrochars reacted for 20 min and 30 min) show better absorption performances, and their electrical conductivity curves show similar increasing trend in the measured frequency range with values ranging from 1 to 7 S m−1. As mentioned above, electrical conductivity within an appropriate range is extremely crucial for absorbers, which is closely associated with the amount of isomeric heterogeneous interfaces between nanocrystalline graphite and amorphous matrix.

An interesting result has been discovered that under the condition of low RL values (below −10 dB), the minimum thicknesses for absorber carbonized at 800 °C for 20 min are thinner than those of many absorbers in previous literature at X and Ku bands (8–18 GHz). The minimum thicknesses for different absorbers and that obtained in this work (RL values below −10 dB) are listed in Table 1, which are investigated by measuring the contours of RL values from these absorbers. The thinner thickness is conductive to reduce the structure weight of absorbers, which is favorable to practical application. Besides, the hydrochars as precursors can be synthesized from biomass (such as glucose, sucrose, starch, cellulose etc.)38,53,54, which are available in abundance with low cost. Additionally, only two simple and controllable steps including hydrothermal carbonization of biomass and high temperature carbonization are needed to prepare absorbers in this work. Undoubtedly, due to all the merits mentioned above, carbonized hydrochars are promising and appealing materials in the area of microwave absorption, especially for composing other dielectric or magnetic materials.

## Conclusions

In conclusion, we successfully prepared carbonized hydrochars composed of dispersed ultrafine nanocrystallines graphite and amorphous matrix on the basis of synthetic strategy of constructing isomeric heterogeneous interfaces. The isomeric heterogeneous interfacial polarizations as well as dipole polarizations resulted from incomplete crystallization and lattice distortions contribute enormously to microwave absorption. This study demonstrates a micro-interface scale insight to engineer microwave absorption materials and can be promised to have great potential for designing and manufacturing novel microwave-absorbing devices.

## Methods

### Synthesis of carbonized hydrochars

The synthetic procedure of hydrochars was carried out by the hydrothermal method53. Experimentally, 0.5 M sucrose solution (60 ml) was transferred to a Teflon-lined stainless steel autoclave with 80 ml and then heated for 12 h at 180 °C. The brown precipitates were collected by centrifugation and abstersion, followed by placed in vacuum oven at 80 °C overnight.

Subsequently, 5 g hydrochars were transferred to a lidded corundum crucible (30 ml), and then heated in a tube furnace with argon gas (Ar) protection. In the first set, tube furnace was respectively heated up to 700, 800, 900 °C for 30 min, the heating speed maintaining 5 °C min−1. And tube furnace was heated to 800 °C for 15, 20, 30 and 40 min in the second set of experiments. The argon gas protection were applied in both heating process and natural cooling process.

### Materials characterization

The morphologies of samples were observed by field emission scanning electron microscope (Zeiss Ultra 55), and the sizes of samples and statistic analysis were obtained by image processing software. X-ray diffraction (XRD) characterization were conducted on a diffractometer (Rigaku D/max-A) with Cu Kα radiation (λ = 1.5406 Å). Photoelectron spectrometer (Thermo ESCALAB 250) equiped with monochromatic Al Kα radiation at 1486.6 eV was used to collect the XPS spectra, and the C 1 s binding energy was calibrated at 284.6 eV for the high-resolution spectra. At the excitation wavelength of 532 nm, the Raman spectra were collected on a microscope (HORIBA XploRA PLUS). The ultrathin section was selected for carbonized hydrochars on a ultramicrotome (Leica EM UC 6), in order to conduct TEM characterizations. The microstructure of samples were characterized by a transmission electron microscope (JEOL JEM-ARM 200 F).

For preparation of microwave absorption test, the paraffins with 50 wt.% carbonized hydrochars powders were mixed in the samples. Then the mixture was pressed into a standard toroidal shape (Φin = 3.04 mm, Φout = 7.00 mm). The vector network analyzer (Agilent E5071C) in the frequency range of 1 to 18 GHz was used to acquire the complex permittivity as well as the complex permeability of samples with coaxial line.

## References

1. 1.

Lynch, D. Introduction to RF Stealth. SciTech Publishing Inc. (2004).

2. 2.

Chen, D. et al. Controllable fabrication of mono-dispersed RGO-hematite nanocomposites and their enhanced wave absorption properties. J. Mater. Chem. A 1, 5996–6003 (2013).

3. 3.

Xu, H. et al. Carbon Hollow Microspheres with a Designable Mesoporous Shell for High-Performance Electromagnetic Wave Absorption. ACS Appl. Mater. Interfaces 9, 6332–6341 (2017).

4. 4.

Wu, F. et al. Reduced graphene oxide (RGO) modified sponge like polypyrrole (PPy) aerogel for excellent electromagnetic absorption. J. Mater. Chem. A 3, 14358–14369 (2015).

5. 5.

Han, M. et al. Graphene-wrapped ZnO hollow spheres with enhanced electromagnetic wave absorption Properties. J. Mater. Chem. A 2, 16403–16409 (2014).

6. 6.

Wang, G. S. et al. Controllable synthesis of uniform ZnO nanorods and their enhanced dielectric and absorption properties. J. Mater. Chem. A 2, 8644–8651 (2014).

7. 7.

Lin, Z. J. et al. Improved microwave absorption properties of core–shell type Ni@SiC nanocomposites. J. Mater. Sci. -Mater. Electron. 28, 5887–5897 (2017).

8. 8.

Zhu, W. et al. Electromagnetic and microwave-absorbing properties of magnetic nickel ferrite nanocrystals. Nanoscale 3, 2862–2864 (2011).

9. 9.

Lv, H. et al. Interface Strategy To Achieve Tunable High Frequency Attenuation. ACS Appl. Mater. Interfaces 8, 6529–6538 (2016).

10. 10.

Liu, J. et al. Hierarchical magnetic yolk–shell microspheres with mixed barium silicate and barium titanium oxide shells for microwave absorption enhancement. J. Mater. Chem. 22, 9277–9284 (2012).

11. 11.

Li, X. et al. One-pot synthesis of CoFe2O4/graphene oxide hybrids and their conversion into FeCo/graphene hybrids for lightweight and highly efficient microwave absorber. J. Mater. Chem. A 3, 5535–5546 (2015).

12. 12.

Tian, C. et al. Synthesis and microwave absorption enhancement of yolk-shell Fe3O4@C microspheres. J. Mater. Sci. 52, 6349–6361 (2017).

13. 13.

Zhao, B. et al. Yolk−Shell Ni@SnO2 Composites with a Designable Interspace To Improve the Electromagnetic Wave Absorption Properties. ACS Appl. Mater. Interfaces 8, 28917–28925 (2016).

14. 14.

Zhang, X. et al. Assembled micro-nano particles with multiple interface polarizations for electromagnetic absorption at gigahertz. Appl. Phys. Lett. 104, 252404 (2014).

15. 15.

Zhang, X. et al. Multiple-phase carbon-coated FeSn2/Sn nanocomposites for high-frequency microwave absorption. Carbon 96, 972–979 (2016).

16. 16.

Liu, Q. et al. CoNi@SiO2@TiO2 and CoNi@Air@TiO2 Microspheres with Strong Wideband Microwave Absorption. Adv. Mater. 28, 486–490 (2016).

17. 17.

Zhang, Y. X. et al. MnO2@colloid carbon spheres nanocomposites with tunable interior architecture for supercapacitors. Mater. Res. Bull. 49, 448–453 (2014).

18. 18.

Zhu, S. J. et al. Flower-like MnO2 decorated activated multihole carbon as high-performance asymmetric supercapacitor electrodes. Mater. Lett. 135, 11–14 (2014).

19. 19.

Zhu, S. J. et al. Rational design of coaxial mesoporous birnessite manganese dioxide/amorphous-carbon nanotubes arrays for advanced asymmetric supercapacitors. J. Power Sources 278, 555–561 (2015).

20. 20.

Le, Q. J. et al. Biotemplate derived three dimensional nitrogen doped graphene@MnO2 as bifunctional material for supercapacitor and oxygen reduction reaction catalyst. J. Colloid Interface Sci. 544, 155–163 (2019).

21. 21.

Huang, M. et al. Highly oriented monolayer graphene grown on a Cu/Ni(111) alloy foil. ACS Nano 12, 6117–6127 (2018).

22. 22.

Huang, M. et al. Layered manganese oxides-decorated and nickel foam-supported carbon nanotubes as advanced binder-free supercapacitor electrodes. J. Power Sources 269, 760–767 (2014).

23. 23.

Wang, T. et al. Preparation of porous graphene@Mn3O4 and its application in the oxygen reduction reaction and supercapacitor. ACS Sustainable Chem. Eng. 7, 831–837 (2019).

24. 24.

Zhou, H. et al. A covalent route for efficient surface modification of ordered mesoporous carbon as high performance microwave absorbers. Nanoscale 5, 12502–12511 (2013).

25. 25.

Cao, M. S. et al. The effects of temperature and frequency on the dielectric properties, electromagnetic interference shielding and microwave-absorption of short carbon fiber/silica composites. Carbon 48, 788–796 (2010).

26. 26.

Yu, H. et al. Graphene/polyaniline nanorod arrays: synthesis and excellent electromagnetic absorption properties. J. Mater. Chem. 22, 21679–21685 (2012).

27. 27.

Sun, H. et al. Cross-Stacking Aligned Carbon-Nanotube Films to Tune Microwave Absorption Frequencies and Increase Absorption Intensities. Adv. Mater. 26, 8120–8125 (2014).

28. 28.

Gupta, T. K. et al. Improved nanoindentation and microwave shielding properties of modified MWCNT reinforced polyurethane Composites. J. Mater.Chem. A 1, 9138–9149 (2013).

29. 29.

Zhang, Y. et al. Broadband and Tunable High-Performance Microwave Absorption of an Ultralight and Highly Compressible Graphene Foam. Adv. Mater. 27, 2049–2053 (2015).

30. 30.

Wang, C. et al. The electromagnetic property of chemically reduced graphene oxide and its application as microwave absorbing material. Appl. Phys. Lett. 98 (2011).

31. 31.

Wen, B. et al. Reduced Graphene Oxides: Light-Weight and HighEfficiency Electromagnetic Interference Shielding at Elevated Temperatures. Adv. Mater. 26, 3484–3489 (2014).

32. 32.

Zhou, C. et al. Lightweight hollow carbon nanospheres with tunable sizes towards enhancement in microwave absorption. Carbon 108, 234–241 (2016).

33. 33.

Qiang, R. et al. Rational design of yolk-shell C@C microspheres for the effective enhancement in microwave absorption. Carbon 98, 599–606 (2016).

34. 34.

Wang, N. et al. One-pot synthesis of biomass-derived carbonaceous spheres for excellent microwave absorption at the Ku band. RSC Adv. 5, 40531–40535 (2015).

35. 35.

Qi, X. et al. Synthesis of high purity chain-like carbon nanospheres in ultrahigh yield, and their microwave absorption properties. RSC Adv. 5, 16010–16016 (2015).

36. 36.

Zhang, X. et al. Gigahertz dielectric polarization of substitutional single niobium atoms in defective graphitic layers. Phys. Rev. Lett. 115, 147601 (2015).

37. 37.

Li, M. et al. Hydrothermal synthesis, characterization, and KOH activation of carbon spheres from glucose. Carbohyd. Res. 346, 999–1004 (2011).

38. 38.

Romero-Anaya, A. J. et al. Spherical carbons: Synthesis, characterization and activation process. Carbon 68, 296–307 (2014).

39. 39.

Wang, K. et al. Mesoporous Carbon Nanofibers for Supercapacitor Application. J. Phys. Chem. C 113, 1093–1097 (2009).

40. 40.

Dillon, R. O. et al. Use of Raman scattering to investigate disorder and crystallite formation in as-deposited and annealed carbon films. Phys. Rev. B 29, 3482–3489 (1984).

41. 41.

Nemanich, R. J. First- and second-order Raman scattering from finite-size crystals of graphite. Phys. Rev. B 20, 392–401 (1979).

42. 42.

Ferrari, A. C. et al. Interpretation of Raman spectra of disordered and amorphous carbon. Phys. Rev. B 61, 14095–14107 (2000).

43. 43.

Song, W. L. et al. Highly ordered porous carbon/wax composites for effective electromagnetic attenuation and Shielding. Carbon 77, 130–142 (2014).

44. 44.

Clark, D. T. et al. Applications of ESCA to Polymer Chemistry. XVII. Systematic Investigation of the Core Levels of Simple Homopolymers. J. Polym. Sci. Plo. Chem. 16, 791–820 (1978).

45. 45.

Naito, Y. et al. Application of Ferrite to Electromagnetic Wave Absorber and Its Characteristics. IEEE Trans. Microw. Theory Tech. 19, 65–72 (1971).

46. 46.

Wang, C. et al. Controlled Synthesis and Morphology-Dependent Electromagnetic Properties of Hierarchical Cobalt Assemblies. J. Phys. Chem. C 114, 14826–14830 (2010).

47. 47.

Li, R. et al. Microwave absorption properties of oriented Pr2Fe17N3-δ particles/paraffin composite with planar anisotropy. J. Alloy. Compd. 586, 239–243 (2014).

48. 48.

Tian, C. et al. Constructing Uniform Core-Shell PPy@PANI Composites with Tunable Shell Thickness toward Enhancement in Microwave Absorption. ACS Appl. Mater. Interfaces 7, 20090–20099 (2015).

49. 49.

Cui, C. et al. Synthesis of Electromagnetic Functionalized Fe3O4 Microspheres/Polyaniline Composites by Two-Step Oxidative Polymerization. J. Phys. Chem. B 116, 9523–9531 (2012).

50. 50.

Micheli, D. et al. X-Band microwave characterization of carbon-based nanocomposite material, absorption capability comparison and RAS design simulation. Compos. Sci. Technol. 70, 400–409 (2010).

51. 51.

Micheli, D. et al. Broadband Electromagnetic Absorbers Using Carbon Nanostructure-Based Composites. IEEE Trans. Microw. Theory Tech. 59, 2633–2646 (2011).

52. 52.

Zhang, X. F. et al. Microwave absorption properties of the carbon-coated nickel nanocapsules. Appl. Phys. Lett. 89, 053115 (2006).

53. 53.

Qi, Y. et al. Mechanism for the formation and growth of carbonaceous spheres from sucrose by hydrothermal carbonization. RSC Adv. 6, 20814–20823 (2016).

54. 54.

Sevilla, M. et al. The production of carbon materials by hydrothermal carbonization of cellulose. Carbon 47, 2281–2289 (2009).

## Acknowledgements

The authors acknowledge financial support from the National Natural Science Foundation of China (grant No. 51172040) and the Fundamental Research Funds for the Central Universities (grant No. N130105001). The authors sincerely appreciate the significant discussion with Prof. Xuefeng Zhang.

## Author information

Yujie Qi completed the most of experiment and wrote the draft paper under Yang Qi’s guidance. Dongchao Wei helped Yujie Qi to perform experimental work. Gui-Mei Shi and Mu Zhang gave valuable suggestion and revised the draft paper.

Correspondence to Gui-Mei Shi or Yang Qi.

## Ethics declarations

### Competing Interests

The authors declare no competing interests.

Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

## Rights and permissions

Reprints and Permissions