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Carbon Nanofibers Propped Hierarchical Porous SiOC Ceramics Toward Efficient Microwave Absorption


The hierarchical porous SiOC ceramics (HPSCs) have been prepared by the pyrolysis of precursors (the mixture of dimethicone and KH-570) and polyacrylonitrile nanofibers (porous template). The HPSCs possess hierarchical porous structure with a BET surface area of 51.4 m2/g and have a good anti-oxidation property (only 5.1 wt.% weight loss). Owing to the porous structure, the HPSCs deliver an optimal reflection loss value of − 47.9 dB at 12.24 GHz and an effective absorption bandwidth of 4.56 GHz with a thickness of 2.3 mm. The amorphous SiOC, SiOx, and free carbon components within SiOC make contributions to enhancing dipolar polarization. Besides, the abundant interfaces between SiOC and carbon nanofibers (CNFs) are favorable for improving interfacial polarization. The conductive loss arisen from cross-linked CNFs can also boost the microwave absorption performance.


With the rapid development of wireless communication technology, the superfluous electromagnetic wave (EMW) has been regarded as new-type pollution, which is harmful for precise instruments, national security, and even human health [1,2,3]. It is urgent to develop high-performance microwave absorption materials (MAMs) to suppress the undesirable electromagnetic pollution. Recently, porous structures have been proven to be favorable for prolonging propagation paths and then improving microwave scattering, thus leading to a better microwave absorption performance. For instances, Yin et al. presented that the ultra-broad effective microwave band of cellular foam reached 29.7 GHz arising from the well-interconnected porous structure [4]. Li et al. reported that porous carbon delivered a minimum reflection loss (RLmin) value of − 56.4 dB, which was owing to the improvement of polarization abilities and multiple reflections [5]. Additionally, the porous materials can usually meet the requirement of lightweight for advanced MAMs. Thus, designing a porous structure is an efficient strategy to enhance the MA properties of MAMs.

Among these porous materials, the porous ceramics as rising stars have drawn extensive attention owing to their anti-oxidation, low thermal expansion, and chemical and physical durability characteristics [6, 7]. Therefore, they are strongly relevant for a series of applications, such as catalytic reactor, filtration, thermal energy storage, water treatment, and MAMs [8,9,10,11]. According to the previous studies, the SiOC ceramics are considered as promising candidates for MA applications because of their amorphous phases (the complex components of SiOC, SiOx, and free carbon), low cost, and lightweight features [12,13,14,15]. Benefiting from the existence of free carbon component, the electrical conductivity of SiOC material is much higher than that of SiC (a wide band gap semiconductor), resulting in a higher electronic dipole polarization loss. For example, Yin et al. reported that the RLmin value of SiOC ceramics could reach − 46 dB, and the good MA ability was mainly attributed to dipolar polarization occurring in SiC and free carbon phases [14]. However, there are little reports about designing porous SiOC structures for MA applications. Above all, it is expected to develop a facile method to prepare the porous SiOC ceramics as high-performance microwave absorbers.

Herein, the hierarchical porous SiOC ceramics (HPSCs) have been constructed through integrating a simple precursor and non-woven fiber fabric template. The XPS results reveal that the SiOC ceramics are composed of SiOC, SiOx, and free carbon. Based on the transmission line theory, the HPSCs deliver an optimal RL value of − 47.9 dB and an effective absorption bandwidth (EAB) of 4.56 GHz. The good MA performance is attributed to multiple reflections, diversified polarization, and conductive losses. This facile approach can open a new avenue toward the fabrication of polymer-derived porous ceramics for MA applications.

Experimental Methods

Synthesis of HPSCs

For HPSC preparation, the dimethicone (Sinopharm Chemical Reagent) and KH-570 (Sinopharm Chemical Reagent) were used as raw materials to prepare the precursor. Firstly, they were mixed with a weight ratio of 19:1 and then stirred at 80 °C for 6 h. Secondly, the non-woven fiber fabrics were used as templates via an electrospinning method. One gram of polyacrylonitrile (PAN; Macklin) powder was dissolved in 9.0 g N,N-dimethylformamide (DMF; Sinopharm Chemical Reagent) solvent with stirring for 5 h. Subsequently, the electrospinning was performed at a voltage of 18 kV and a feeding rate of 10 μL/min. To obtain the precursor/PAN hybrid, the as-prepared precursor was injected into PAN fabrics. Finally, the hybrid was heated to 1000 °C for 2 h at a heating rate of 2 °C/min under argon atmosphere. After cool down, the HPSCs were collected without any further treatment.


The morphologies of the samples were investigated by field-emission scanning electron microscopy (FESEM; FEI Apreo). The X-ray photoelectron spectroscopy (XPS, Thermo-VG Scientific, ESCALAB 250) was used with a monochromatic Al-Kα X-ray source (excitation energy = 1486 eV). The Raman spectra were tested through a microscopic confocal Raman spectrometer (Renishaw RM2000) with a wavelength of 514 nm at room temperature. The compositions of the sample were studied by X-ray diffraction (XRD) by a Rigaku D/max-RB12 X-ray diffractometer with Cu Kα radiation. The thermogravimetry analysis (TGA) was recorded on a TGA/Q5000IR analyzer under ambient atmosphere. The nitrogen adsorption and desorption isotherms were measured by ASAP 2020 Accelerated Surface Area and Porosimetry instrument.

Microwave Absorption Measurement

The electromagnetic parameters of samples mixed with wax (50 wt.%) were measured at 2~18 GHz using Vector network analyzer (N5245A, Agilent). The reflection loss (RL) values were calculated based on transmission line theory using the following equations [16, 17].

$$ {Z}_{\mathrm{in}}={Z}_0{\left({\mu}_r/{\varepsilon}_r\right)}^{1/2}\tanh \left[j\left(2\pi fd/c\right){\left({\mu}_r/{\varepsilon}_r\right)}^{1/2}\right] $$
$$ RL=20\log \mid \left({Z}_{\mathrm{in}}-{Z}_0\right)/\left({Z}_{\mathrm{in}}+{Z}_0\right)\mid $$

where εr and μr are the relative complex permittivity and permeability respectively, f is the frequency of microwave, d is the thickness of samples, c is the velocity of microwave in free space, Zin is the lumped input impedance at the absorber surface, and Z0 is the characteristic impedance of air [18].

Results and Discussion

Figure 1 shows the schematic illustration of fabrication of HPSCs. Step 1: the precursor was prepared by dimethicone and KH-570, and the PAN nanofiber fabric was obtained via an electrospinning method. Additional file 1: Figure S1 shows the optical image of PAN fabric (8 cm × 14 cm). Additional file 1: Figure S2 exhibits the cross-linked PAN nanofibers with a diameter of 378 nm. These cross-linked fibers form a large number of pores, which can be directly used as porous templates. Step 2: the as-prepared precursor was injected into PAN fabrics. Step 3: the HPSCs were obtained after a heat treatment. After pyrolysis and stabilization, the precursor and PAN nanofibers were transformed to SiOC ceramics and carbon nanofibers (CNFs), respectively. The CNFs were regarded as the backbone to prop porous structure, and the SiOC ceramics wrapped onto the surface of CNFs. Thus, the HPSCs were formed through a template/precursor pyrolysis method. As shown in Fig. 2a, the HPSCs exhibit a large number of pores with hierarchical porous structures. Figure 2b displays the irregular pores with a size of 1.2 μm, corresponding to the escape of gas (CH4, H2) in the precursor pyrolysis process. Figure 2 c and d exhibit much more uniform pores with a size of 200 nm, which are mainly constructed by the cross-linked carbon nanofibers.

Fig. 1
figure 1

The schematic illustration of fabrication of HPSCs

Fig. 2
figure 2

The SEM images of HPSCs at different magnification: a × 5.0 k, b × 10.0 k, c × 10.0 k, and d × 50.0 k

The XPS spectra (Fig. 3) are performed to verify the composition of HPSC samples. The survey spectrum (Fig. 3a) ascertains the existence of Si, C, and O elements within the HPSC sample. As shown in Fig. 3b, the broad peak of Si 2p exhibits three fitted bands around at 102.30, 103.15, and 103.90 eV, corresponding to C–Si–O, Si–O, and O–Si–O bonds, respectively [19]. The higher binding energy of 103.90 eV for O–Si–O bond is mainly attributed to the higher electronegativity of O atom (3.610) than those of C (2.544) and Si (1.916) atoms. As shown in Fig. 3c, the spectrum of C 1s displays the presence of different valence around C atom originating from bonding with other elements. It can be divided into three bands at 284.60, 285.00, and 285.90 eV, which are related to C–C, C–Si–O, and C–O bonds, respectively [20]. Figure 3d reveals that the fitted O 1s band suggests the presence of Si–O (532.50 eV) and O–Si–O (533.20 eV) bonds. The XPS results indicate that the SiOC component has been successfully obtained via this precursor pyrolysis method.

Fig. 3
figure 3

The XPS spectra of HPSCs. a The survey spectrum. b The fitted Si 2p peak. c The fitted C 1s peak. d The fitted O 1s peak

The Raman spectrum (Figure 4a) was carried out to ascertain the existence of free carbon phase within SiOC ceramics. The Raman spectrum can be fitted into D, G, T, and D” bands. The typical D and G bands are located at 1328 and 1598 cm−1, indicating the amorphous carbon structure. The D and T bands are ascribed to electron–hole relaxation originating from disordered graphitic carbon, while the D” band is associated with amorphous carbon soot. And the G band is corresponding to E2g mode arising from in-plane stretching vibration of sp2 hybridized bonds [21]. The XRD pattern of HPSCs is plotted in Additional file 1: Figure S3. A broad peak around at 24.5° is mainly attributed to the amorphous carbon phase within SiOC ceramics and PAN-derived carbon nanofibers [22, 23]. The TGA characterization was carried out to measure the anti-oxidation property of HPSCs. Figure 4b shows the TGA curve in the temperature of 20~1000 °C under flowing air atmosphere. A weak weight loss is about 5.1 wt.% in the range of 450~800 °C, which is attributed to the oxidation of free carbon component within SiOC ceramics. Based on the TGA result, it can be concluded that HPSCs show good thermal stability and anti-oxidation properties, and carbon fibers as template have been totally wrapped and protected by SiOC ceramics. The N2 adsorption–desorption isotherms are performed to investigate Brunauer–Emmet–Teller (BET) surface area of HPSCs. Figure 4c shows a typical type IV behavior, revealing the presence of mesopores in HPSC samples. And the HPSCs deliver a BET surface area of 51.4 m2/g. The pore size distribution is studied by the Barrett–Joyner–Halenda (BJH) model. Figure 4d shows that HPSCs also possess a lot of mesopores with a diameter of 20 nm.

Fig. 4
figure 4

a The Raman spectrum. b TGA curve under air atmosphere. c N2 adsorption–desorption curves. d Pore size distribution of HPSC samples

As shown in Fig. 5a, the MA performance of HPSCs is illustrated by the RL curves versus frequency at different layer thickness. The HPSCs deliver an optimal RLmin value of − 47.9 dB at 12.24 GHz, and an EAB of 4.56 GHz in the range of 10.24~14.8 GHz with a matching thickness of 2.3 mm. The RLmin values can reach − 23.8 dB at 14.56 GHz, − 47.9 at 12.24 GHz, − 45.5 at 10.8 GHz, − 26.6 at 8.72 GHz, − 23.5 at 7.28 GHz, and − 20.3 dB at 6.32 GHz with the thicknesses of 2.0, 2.3, 2.5, 3.0, 3.5, and 4.0 mm, respectively. This phenomenon can be interpreted by the quarter-wavelength cancelation model, which illustrates the relationship between matching thickness (tm) and corresponding matching frequency (fm) by the following equation [24, 25].

$$ {t}_{\mathrm{m}}= n\lambda /4= n c/\left(4\ {f}_{\mathrm{m}}\ \sqrt{\left|{\varepsilon}_r\right|\left|{\mu}_r\right|}\right)\kern1.25em n=\left(1,3,5,\dots \right) $$
Fig. 5
figure 5

The MA properties of HPSCs. a The RL curves. b The complex permittivity and tangent loss curves. c RLmin versus thickness of similar Si-based ceramics absorbers. d The schematic illustration of MA mechanism

When the tm and fm meet Eq. (3) well, the phase difference between the incident wave and the reflective wave is 180°, which means that the RLmin can be obtained owing to the dissipation of electromagnetic energy at the air-absorber interface [26]. Additional file 1: Figure S4 shows the tm versus fm curves of 1λ/4 for HPSCs; it is apparent that \( {t}_{\mathrm{m}}^{\mathrm{exp}} \) dots are located at the \( {t}_{\mathrm{m}}^{\mathrm{cal}} \) lines, revealing that this model can expound the relationship between tm and fm well. The complex permittivity is tightly relevant to MA performance, and the tangent loss (tanδε = ε″/ε′) is generally used to evaluate the attenuating ability of MAMs [27]. The real part (ε′) represents the storage ability of EM energy, while the imaginary part (ε″) is corresponding to the loss ability of EM energy [28]. Figure 5b displays the complex permittivity and tanδε curves of HPSCs. The ε′ declines in the whole range, and the ε″ delivers a peak in the range of 9.2~13.6 GHz. Therefore, the tanδε exhibits a relaxation peak around at 12.0 GHz, which is close to that (12.24 GHz) of the optimal RLmin. As shown in Additional file 1: Figure S5, the real and imaginary parts of complex permeability are nearly equal to 1 and 0, respectively, which is ascribed to the non-magnetism of HPSCs. Figure 5c shows a comparison of RLmin value versus thickness of similar Si-based ceramics materials in recent studies [12,13,14, 29,30,31,32,33,34,35]. Additional file 1: Table S1 lists the detailed MA data of all related references. It can be found that the HPSCs not only deliver an optimal RL value but also possess a thin thickness.

$$ \alpha =\frac{\sqrt{2}\pi f}{c}\times \sqrt{\left({\mu}^{\prime \prime }{\varepsilon}^{\prime \prime }-\mu^{\prime}\varepsilon^{\prime}\right)+\sqrt{\left({\mu}^{\prime \prime }{\varepsilon}^{\prime \prime }-\mu^{\prime}\varepsilon^{\prime}\right)+\left({\mu}^{\prime \prime }{\varepsilon}^{\prime }+\mu^{\prime}\varepsilon^{\prime\prime}\right)}} $$

Generally, the EM attenuation constant (α) is regarded as an important factor to assess the dissipation capability, and it can be expressed by Eq. (4) [36]. As shown in Additional file 1: Figure S6, the HPSCs show an increasing trend and strong attenuation ability in the range of 2~18 GHz. These values are much larger than those of similar Si-based materials [31, 33]. On the other hand, a proper impedance matching is favorable to make more microwave propagate into materials. When the value of |Zin/Z0| is equal to 1, it means that there is no any reflection of an incident wave at the air-absorber surface [37]. As shown in Additional file 1: Figure S7, the |Zin/Z0| values of HPSCs are close to 1 in the most range of 2~18 GHz. And the optimal RLmin value of − 47.9 dB is obtained at 12.24 GHz, and the corresponding |Zin/Z0| value (0.994) is nearly equal to 1. Figure 5d demonstrates a possible MA mechanism of HPSCs. Firstly, the porous structure can make contributions to extend the scattering of EMW, enhancing the attenuation of electromagnetic energy [5]. Secondly, the dipolar polarization is arisen from SiOC owing to the existence of SiOC, SiOx, and free carbon [38]. And there are a large amount of grain boundaries within the amorphous SiOC structure; it is a benefit to enhancing interfacial polarization. Thirdly, the abundant interfaces between CNFs and SiOC play a vital role in boosting the interfacial polarization [39]. Fourthly, the cross-linked CNFs can provide a continuous transport path for free electrons, which is favorable for enhancing the conductive loss [26, 40]. The proper impedance matching of HPSCs reveals that more microwave can propagate into absorbers, and thus, more electromagnetic energy can be dissipated and converted into heat or other energy. Based on these aspects, the HPSCs exhibit an impressive MA performance. And the MA properties can be optimized by tuning the chemical compositions of SiOC and porous structure (pore size, pore volume).


In summary, the HPSCs have been successfully obtained via a CNF template method. The SEM images and BET results reveal the hierarchical porous structure of SiOC sample. The XPS results indicate that SiOC is formed by SiOC, SiOx, and free carbon components. The HPSCs show good anti-oxidation property according to the result of TGA. The optimal RL value and EAB of HPSCs can reach − 47.9 dB and 4.56 GHz at the thickness of 2.3 mm, which is advanced among these similar MAMs. The excellent MA property is originated from multiple reflection, polarization, conductive losses, and favorable impedance matching effect. The HPSCs can be prospective candidates for high-temperature MA application owing to its good anti-oxidation and MA properties.

Availability of Data and Materials

The data supporting the conclusions of this article are included within the article and its additional files.







Carbon nanofibers




Effective absorption bandwidth


Electromagnetic wave


Field-emission scanning electron microscopy


Hierarchical porous SiOC ceramics


Microwave absorption materials



RLmin :

Minimum reflection loss


Thermogravimetry analysis


X-ray photoelectron spectroscopy


  1. Hu Q, Yang R, Mo Z, Lu D, Yang L, He Z, Zhu H, Tang Z, Gui X (2019) Nitrogen-doped and Fe-filled CNTs/NiCo2O4 porous sponge with tunable microwave absorption performance. Carbon 153:737–744

    Article  CAS  Google Scholar 

  2. Deng Z, Li Y, Zhang H-B, Zhang Y, Luo J-Q, Liu L-X, Yu Z-Z (2019) Lightweight Fe@C hollow microspheres with tunable cavity for broadband microwave absorption. Compos Part B 177

  3. Luo H, Feng W, Liao C, Deng L, Liu S, Zhang H, Xiao P (2018) Peaked dielectric responses in Ti3C2 MXene nanosheets enabled composites with efficient microwave absorption. J Appl Phys 123

  4. Xu H, Yin X, Li M, Li X, Li X, Dang X, Zhang L, Cheng L (2019) Ultralight cellular foam from cellulose nanofiber/carbon nanotube self-assemblies for ultrabroad-band microwave absorption. ACS Appl Mater Interfaces 11:22628–22636

    Article  CAS  Google Scholar 

  5. Wu Z, Hu W, Huang T, Lan P, Tian K, Xie F, Li L (2018) Hierarchically porous carbons with controlled structures for efficient microwave absorption. J Mater Chem C 6:8839–8845

    Article  CAS  Google Scholar 

  6. Liu R, Xu T, Wang, C. (2016) A review of fabrication strategies and applications of porous ceramics prepared by freeze-casting method. Ceram Int 42:2907–2925

    Article  CAS  Google Scholar 

  7. Sun YS, Yang ZH, Cai DL, Li Q, Li HL, Wang SJ, Jia DC, Zhou Y (2017) Mechanical, dielectric and thermal properties of porous boron nitride/silicon oxynitride ceramic composites prepared by pressureless sintering. Ceram Int 43:8230–8235

    Article  CAS  Google Scholar 

  8. Minas C, Carnelli D, Tervoort E, Studart AR (2016) 3D Printing of emulsions and foams into hierarchical porous ceramics. Adv Mater 28:9993–9999

    Article  CAS  Google Scholar 

  9. Gröttrup J, Schütt F, Smazna D, Lupan O, Adelung R, Mishra YK (2017) Porous ceramics based on hybrid inorganic tetrapodal networks for efficient photocatalysis and water purification. Ceram Int 43:14915–14922

    Article  Google Scholar 

  10. Maurath J, Willenbacher N (2017) 3D printing of open-porous cellular ceramics with high specific strength. J Eur Ceram Soc 37:4833–4842

    Article  CAS  Google Scholar 

  11. Liu JJ, Ren B, Wang YL, Lu YJ, Wang L, Chen YG, Yang JL, Huang Y (2019) Hierarchical porous ceramics with 3D reticular architecture and efficient flow-through filtration towards high-temperature particulate matter capture. Chem Eng J 362:504–512

    Article  CAS  Google Scholar 

  12. Du B, He C, Shui A, Zhang X, Hong C (2019) Microwave-absorption properties of heterostructural SiC nanowires/SiOC ceramic derived from polysiloxane. Ceram Int 45:1208–1214

    Article  CAS  Google Scholar 

  13. Duan WY, Yin XW, Li Q, Liu XM, Cheng LF, Zhang LT (2014) Synthesis and microwave absorption properties of SiC nanowires reinforced SiOC ceramic. J Eur Ceram Soc 34:257–266

    Article  CAS  Google Scholar 

  14. Duan WY, Yin XW, Luo CJ, Kong J, Ye F, Pan HX (2017) Microwave-absorption properties of SiOC ceramics derived from novel hyperbranched ferrocene-containing polysiloxane. J Eur Ceram Soc 37:2021–2030

    Article  CAS  Google Scholar 

  15. Chen L, Zhao J, Wang L, Peng F, Liu H, Zhang J, Gu J, Guo Z (2019) In-situ pyrolyzed polymethylsilsesquioxane multi-walled carbon nanotubes derived ceramic nanocomposites for electromagnetic wave absorption. Ceram Int 45:11756–11764

    Article  CAS  Google Scholar 

  16. Feng WL, Luo H, Wang Y, Zeng SF, Deng LW, Zhou XS, Zhang HB, Peng SM (2018) Ti3C2 MXene: a promising microwave absorbing material. RSC Adv 8:2398–2403

    Article  CAS  Google Scholar 

  17. Mo ZC, Yang RL, Lu DW, Yang LL, Hu QM, Li HB, Zhu H, Tang ZK, Gui XC (2019) Lightweight, three-dimensional carbon Nanotube@TiO2 sponge with enhanced microwave absorption performance. Carbon 144:433–439

    Article  CAS  Google Scholar 

  18. Zhao HB, Cheng JB, Zhu JY, Wang YZ (2019) Ultralight CoNi/rGO aerogels toward excellent microwave absorption at ultrathin thickness. J Mater Chem C 7:441–448

    Article  CAS  Google Scholar 

  19. Yu S, Tub R, Goto T (2016) Preparation of SiOC nanocomposite films by laser chemical vapor deposition. J Eur Ceram Soc 36:403–409

    Article  CAS  Google Scholar 

  20. Wu Z, Cheng XQ, Tian D, Gao TT, He WD, Yang CH (2019) SiOC nanolayers directly-embedded in graphite as stable anode for high-rate lithium ion batteries. Chem Eng J 375

  21. Okuda H, Young RJ, Wolverson D, Tanaka F, Yamamoto G, Okabe T (2018) Investigating nanostructures in carbon fibres using Raman spectroscopy. Carbon 130:178–184

    Article  CAS  Google Scholar 

  22. Zhang T, Xiao B, Zhou PY, Xia L, Wen GW, Zhang HB (2017) Porous-carbon-nanotube decorated carbon nanofibers with effective microwave absorption properties. Nanotechnology 28

  23. Cheng P, Li T, Yu H, Zhi L, Liu ZH, Lei ZB (2016) Biomass-derived carbon fiber aerogel as a binder-free electrode for high-rate supercapacitors. J Phys Chem C 120:2079–2086

    Article  CAS  Google Scholar 

  24. Wang M, Lin Y, Liu Y, Yang H (2019) Core–shell structure BaFe12O19@ PANI composites with thin matching thickness and effective microwave absorption properties. J Mater Sci Mater Electron 30:14344–14354

    Article  CAS  Google Scholar 

  25. Zeng S, Wang M, Feng W, Zhu L, Teng Z, Zhang H, Peng S (2019) Cobalt nanoparticles encapsulated in a nitrogen and oxygen dual-doped carbon matrix as high-performance microwave absorbers. Inorganic Chemistry Frontiers 6:2472–2480

    Article  CAS  Google Scholar 

  26. Qiao M, Lei X, Ma Y, Tian L, He X, Su K, Zhang Q (2018) Application of yolk–shell Fe3O4@N-doped carbon nanochains as highly effective microwave-absorption material. Nano Res 11:1500–1519

    Article  CAS  Google Scholar 

  27. Dai B, Zhao B, Xie X, Su T, Fan B, Zhang R, Yang R (2018) Novel two-dimensional Ti3C2Tx MXenes/nano-carbon sphere hybrids for high-performance microwave absorption. J Mater Chem C 6:5690–5697

    Article  CAS  Google Scholar 

  28. Ding D, Wang Y, Li XD, Qiang R, Xu P, Chu WL, Han XJ, Du YC (2017) Rational design of core-shell Co@C microspheres for high-performance microwave absorption. Carbon 111:722–732

    Article  CAS  Google Scholar 

  29. Hong W, Dong S, Hu P, Luo X, Du S (2017) In situ growth of one-dimensional nanowires on porous PDC-SiC/Si3N4 ceramics with excellent microwave absorption properties. Ceram Int 43:14301–14308

    Article  CAS  Google Scholar 

  30. Dong S, Hu P, Zhang X, Han J, Zhang Y, Luo X (2018) Carbon foams modified with in-situ formation of Si3N4 and SiC for enhanced electromagnetic microwave absorption property and thermostability. Ceram Int 44:7141–7150

    Article  CAS  Google Scholar 

  31. Ye X, Chen Z, Ai S, Hou B, Zhang J, Liang X, Zhou Q, Liu H, Cui S (2019) Effects of SiC coating on microwave absorption of novel three-dimensional reticulated SiC/porous carbon foam. Ceram Int 45:8660–8668

    Article  CAS  Google Scholar 

  32. Dong Y, Yin X, Wei H, Li M, Hou Z, Xu H, Cheng L, Zhang L (2019) Carbon nanowires reinforced porous SiO2/3Al2O3·2SiO2 ceramics with tunable electromagnetic absorption properties. Ceram Int 45:11316–11324

    Article  CAS  Google Scholar 

  33. Ye X, Chen Z, Ai S, Hou B, Zhang J, Liang X, Zhou Q, Liu H, Cui S (2019) Synthesis and microwave absorption properties of novel reticulation SiC/Porous melamine-derived carbon foam. J Alloys Compd 791:883–891

    Article  CAS  Google Scholar 

  34. Zhao WY, Shao G, Jiang MJ, Zhao B, Wang HL, Chen DL, Xu HL, Li XJ, Zhang R, An LA (2017) Ultralight polymer-derived ceramic aerogels with wide bandwidth and effective electromagnetic absorption properties. J Eur Ceram Soc 37:3973–3980

    Article  CAS  Google Scholar 

  35. Du B, He C, Qian J, Cai M, Wang X, Shui A (2019) Electromagnetic wave absorbing properties of glucose-derived carbon-rich SiOC ceramics annealed at different temperatures. J Am Ceram Soc 102:7015–7025

    Article  CAS  Google Scholar 

  36. Luo JH, Zhang K, Cheng ML, Gu MM, Sun XK (2020) MoS2 spheres decorated on hollow porous ZnO microspheres with strong wideband microwave absorption. Chem Eng J 380

  37. Xu HL, Yin XW, Zhu M, Li MH, Zhang H, Wei HJ, Zhang LT, Cheng LF (2019) Constructing hollow graphene nano-spheres confined in porous amorphous carbon particles for achieving full X band microwave absorption. Carbon 142:346–353

    Article  CAS  Google Scholar 

  38. Li X, Wang L, You WB, Xing LS, Yang LT, Yu XF, Zhang J, Li YS, Che RC (2019) Enhanced polarization from flexible hierarchical MnO2 arrays on cotton cloth with excellent microwave absorption. Nanoscale 11:13269–13281

    Article  CAS  Google Scholar 

  39. Gou GJ, Meng FB, Wang HG, Jiang M, Wei W, Zhou ZW (2019) Wheat straw-derived magnetic carbon foams: in-situ preparation and tunable high-performance microwave absorption. Nano Res 12:1423–1429

    Article  CAS  Google Scholar 

  40. Li Y, Liu XF, Nie XY, Yang WW, Wang YD, Yu RH, Shui JL (2019) Multifunctional organic-inorganic hybrid aerogel for self-cleaning, heat-insulating, and highly efficient microwave absorbing material. Adv Funct Mater 29

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This work is supported by the National Natural Science Foundation of China (Grant No. 91326102), the Science and Technology Development Foundation of China Academy of Engineering Physics (Grant No. 2013A0301012), and the Science and Technology Innovation Research Foundation of Institute of Nuclear Physics and Chemistry. Haibin Zhang is grateful to the Foundation by the Recruitment Program of Global Youth Experts and the Youth Hundred Talents Project of Sichuan Province.


National Natural Science Foundation of China (Grant No. 91326102) and Science and Technology Development Foundation of China Academy of Engineering Physics (Grant No. 2013A0301012).

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YNL designed this study and wrote this manuscript. SFZ designed this study. ZT and WLF contributed to figure modifying and language checking. HBZ and SMP provided many critical suggestions for this paper. All authors have read and approved the final manuscript.

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Correspondence to Haibin Zhang or Shuming Peng.

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Additional file 1: Figure S1.

The optical image of PAN fabric. Figure S2. The SEM images of electrospinning derived PAN fibers. Figure S3. The XRD pattern of HPSCs. Figure S4. The reflection loss curves (upper region) and the dependence of matching thickness (tm) on matching frequency (fm) at the wavelength of 1/4λ (lower region) of HPSCs. Figure S5. The complex permeability curves of HPSCs. Figure S6. The attenuation constant of HPSCs. Figure S7. The |Zin/Z0| curve of HPSCs. Table S1. The MA properties of similar Si-based materials

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Liu, Y., Zeng, S., Teng, Z. et al. Carbon Nanofibers Propped Hierarchical Porous SiOC Ceramics Toward Efficient Microwave Absorption. Nanoscale Res Lett 15, 28 (2020).

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  • SiOC
  • Carbon nanofibers
  • Porous ceramics
  • Microwave absorption