Article | Open Access | Published:

High nitrogen-containing cotton derived 3D porous carbon frameworks for high-performance supercapacitors

Scientific Reports volume 5, Article number: 15388 (2015) | Download Citation


Supercapacitors fabricated by 3D porous carbon frameworks, such as graphene- and carbon nanotube (CNT)-based aerogels, have been highly attractive due to their various advantages. However, their high cost along with insufficient yield has inhibited their large-scale applications. Here we have demonstrated a facile and easily scalable approach for large-scale preparing novel 3D nitrogen-containing porous carbon frameworks using ultralow-cost commercial cotton. Electrochemical performance suggests that the optimal nitrogen-containing cotton-derived carbon frameworks with a high nitrogen content (12.1 mol%) along with low surface area 285 m2 g−1 present high specific capacities of the 308 and 200 F g−1 in KOH electrolyte at current densities of 0.1 and 10 A g−1, respectively, with very limited capacitance loss upon 10,000 cycles in both aqueous and gel electrolytes. Moreover, the electrode exhibits the highest capacitance up to 220 F g−1 at 0.1 A g−1 and excellent flexibility (with negligible capacitance loss under different bending angles) in the polyvinyl alcohol/KOH gel electrolyte. The observed excellent performance competes well with that found in the electrodes of similar 3D frameworks formed by graphene or CNTs. Therefore, the ultralow-cost and simply strategy here demonstrates great potential for scalable producing high-performance carbon-based supercapacitors in the industry.


The depletion of fossil fuels and the increasingly environmental pollution has required the scientific community to develop new class of clean and sustainable energy sources. The fast-growing market for portable electronic devices and hybrid electronic vehicles has also demanded innovative energy storage materials of high power density and efficient energy conversion. Due to the large amount of energy stored in a very short time and long-cycle life, supercapacitors have been projected to be the most common energy storage devices1,2,3, with particular advancements achieved in flexible all-solid-state supercapacitors in recent years4,5,6,7,8.

Among the well-developed electrical double layer capacitors (EDLCs) and pseudo-capacitors, porous carbon nanostructure-based electrode materials have attracted increasing interests for supercapacitors owing to their high surface area, sufficient electrical conductivity, excellent chemical stability and low cost9. A remarkable variety of carbon sources with various nanostructures or unique morphologies have been widely explored, aiming to improve the electrochemical capacitance and power density. For such purpose, three-dimensional (3D) carbon porous nanostructures have been recently pursued because of the advantageous features of enhanced ion and electron transport, high specific capacities, superior electrochemical stability10,11,12. As typical 3D carbon nanostructures, carbon nanotube (CNT) aerogels and graphene aerogels (GAs) of high electrical conductivity, large surface area and interconnected porous structures have been largely studied13,14,15,16,17. For examples, Robert and coworkers have demonstrated two-electrode supercapacitor cells using 3D CNT-based materials, showing an area specific capacitance of 1 mF cm−2 in 1 M LiPF6 at a current of 10 μA18. On the other hand, Duan and coworkers have fabricated flexible GA-based solid-state supercapacitors, which demonstrated enhanced specific capacitance up to 186 F g−1 with area specific capacitance of 372 F cm−2 (current density of 1 A g−1) in two-electrode polyvinylalcohol (PVA)/H2SO4 gel system19. Further improvement includes simply employing heteroatoms into such 3D carbon frameworks, and thus additional pseudo-capacitance could be achieved in EDLCs. For instance, Müllen and coworkers have fabricated 3D nitrogen and boron co-doped graphene into all-solid-state supercapacitors, which showed high specific capacitance of 62 F g−1 at a scan rate of 5 mVs−1 in the two-electrode PVA/H2SO4 system20. Moreover, the nitrogen-doped 3D graphene framework fabricated by Qu and coworkers exhibited high specific capacitance, approaching 484 F g−1 at a current density of 1 A g−1 in 1 M LiClO4 aqueous solution (three-electrode system)21.

Although significant progresses have been made in the EDLCs based on 3D graphene- and CNT-based porous frameworks, the critical issues associated with high cost and low yield of such novel carbon-based materials still limit their applications in the industry of energy storage devices22. It is noticed that great challenges remain in the exploration of sufficient and simple procedures for scalable preparing CNTs and graphene23,24,25,26. As a consequence, the high price/cost of commercially available high-quality CNT and graphene-based materials (Table S1) only allows them to be used in the laboratories thus far.

In the present work, we demonstrate a simple strategy for large-scale preparing aerogel-like 3D carbon frameworks using ultralow-cost commercial cotton (0.01 USD/g, much lower than the commercially available CNTs and graphene shown in Table S1). Since the aerogel-like 3D porous framework of the cotton has been well preserved in the convenient thermal treatment, the as-prepared cotton-derived carbon frameworks (CCFs) have delivered excellent cycle stability with high specific capacities of 182 F g−1 at the current density of 0.1 A g−1 in 6 mol L−1 KOH aqueous solution. Further electrochemical improvements have been achieved by introducing low-cost N-doping sources (urea and melamine), and the resulting N-doped cotton-derived carbon frameworks with subsequent acid treatment (NCCFs) presented much enhanced specific capacities of 308, 240 and 200 F g−1 at current densities of 0.1, 1 and 10 A g−1, respectively. Moreover, the highest capacitance up to 220 F g−1 at 0.1 A g−1 and negligible capacitive loss were also observed in the flexible all-solid-state supercapacitors fabricated by NCCFs. Direct comparison indicates that such NCCFs of much lower cost offer very competitive electrochemical performance to the 3D graphene- and CNT-based frameworks in the literature. Implication of the results suggests that the use of extremely simple and easily scalable strategy with very cheap commercial cotton is highly promising for large-scale producing high-performance supercapacitors in the industry.


In the typical preparation (Fig. 1), certain amount of commercial cotton was used as the raw materials and the corresponding size and amount could be easily scale-up according to the chamber of furnace for carbonization. For preparing CCFs, the cotton was directly heated up for carbonization under N2 protection, and further treated under sonication in the mixed acid solution to improve the hydrophilicity via introducing carbonyl and hydroxyl groups27. NCCFs were obtained by the same conditions except for the presence of urea and melamine (N-doping sources) in the carbonization, allowing the nitrogen-containing radicals in the decomposition of melamine and urea to reacts with the carbon radicals upon high-temperature treatment.

Figure 1
Figure 1

Schemes of the 3D frameworks of the as-received commercial cotton (a), as-prepared 3D aerogel-like carbon framework (b) and fabricated all-solid-state supercapacitor in the PVA/KOH gel electrolyte (c).

Figure 2a shows a large piece of NCCFs prepared in this work, indicating the easy scalability of the approach. Similar to the observation in the recently reported graphene and CNT-based 3D frameworks28,29, the as-prepared NCCFs show light weight (Fig. 2b) and mechanical robust with excellent flexibility (Fig. 2c), which has also been confirmed by the stress-strain results of the static tensile tests (Figure S1). Figure 3 exhibits typical scanning electron microscopy (SEM) and transmission electron microscopy (TEM) images of raw cotton (Fig. 3a–d) and NCCFs (Fig. 3e–h). According to the direct comparison of the morphologies, the raw cotton and NCCFs both present similar 3D frameworks, indicating that the well-formed 3D frameworks in the raw cotton has been well reserved in the high-temperature carbonization. As the basic structure for the 3D frameworks, the carbon stripes in the NCCFs exhibit much curved and twisted (Fig. 3f) in comparison with those in the raw cotton (Fig. 3b,c). Such morphological changes should be associated with the mass loss upon the high-temperature carbonization, leading to shrinkages in the curved cotton stripes as well. Representative SEM and TEM images suggest the wrinkles along with rough and porous surface of the CCFs (Figure S2) and NCCFs (Fig. 3g,h). The elemental mapping results also suggest the uniform elemental distribution of N and O in the NCCFs, due to the N-doping and acid treatments (Figure S3). According to Fig. 4, further details of the microstructures have been observed in the CCFs and NCCFs, suggesting no meaningful difference has been found in these two samples. The observed mesopores and micropores in both of the CCFs and NCCFs would provide effective porosity and improved surface area for charge storage.

Figure 2
Figure 2

Optical images showing the scable fabrication (a), light weight (b) and mechanical flexibility (c) of the NCCFs.

Figure 3
Figure 3

SEM images (a–c) and TEM image (d) of the commercial cotton; SEM images (e–g) and TEM image (h) of the NCCFs.

Figure 4
Figure 4

TEM images of CCFs (a,c) and NCCFs (b,d).

Figure 5 shows the N2 adsorption/desorption isotherms of cotton-derived carbon materials. The pore parameters calculated from N2 adsorption/desorption isotherms are summarized in Table 1. According to Fig. 5a, the N2 adsorption/desorption isotherms of both samples exhibit type I isotherms with H4 type hysteresis loops. The rapid increase of the adsorption isotherms in the low pressure region (P/P0 = 0 ~ 0.1) and the hysteresis loops indicates a large amount of micropores and presence of mesopores, respectively (Fig. 5a)30,31,32,33. The results of comparison show that CCFs possess slightly larger surface area (373 m2 g−1) than NCCFs (285 m2 g−1), which is attributed to the reduced micropores caused by the micropore collapse and merge during the acid treatment. The observed larger loops suggest increased meso/macropores surface area in the NCCFs (128 cm2 g−1), compared to 88 cm2 g−1 in the CCFs. These changes are mainly attributed to the surface functionalization during the carbonization process34. On the other hand, the distribution of average pore diameter was obtained by the density functional theory method. As exhibited in Fig. 5b, the pores size of CCFs was mainly around 0.5 nm, while decreased peaks of 0.5 nm coupled with pronounced peaks were observed around 1.4 nm, 1.7 nm and 2.7 nm in NCCFs. Such changes indicate that the surface functionalization has not only effectively enhanced the contents of heteroatoms, but also introduced pores in the 3D frameworks as well.

Figure 5
Figure 5

Nitrogen adsorption/desorption isortherms (a) and average pore diameter distributions of the CCFs and NCCFs (b).

Table 1: Pore parameters and chemical compositions (determined by XPS) of CCFs and NCCFs.

Raman spectra (Figure S4) illustrate two prominent bands around 1360 and 1600 cm−1, which are denoted as the D and G bands of carbon materials, respectively27. No significant difference was found in the ratios of Id/Ig for CCFs (0.94) and NCCFs (0.99). X-ray photoelectron spectroscopy (XPS) was carried out to investigate the chemical composition of carbon materials (Fig. 6). As expected, pronounced C peaks have been observed in both samples (Fig. 6a), showing dominant carbon-carbon species (284.6 eV) (Figure S5). Compared to CCFs, enhanced C-N (286.33 eV) and C = O (287.9 eV) peaks have been found in NCCFs, which is attributed to the doping of nitrogen and acid treatment. It is noticeable that the substantial increase of nitrogen content in NCCFs (~12.1 mol%) listed in Table 1 suggests the sufficient N-doping with the presence of urea and melamine in the carbonization process, where nitrogen-containing precursors would react with the carbon sources to form C-N bonding under an inert atmosphere35,36,37,38. As shown in Fig. 6b, the results exhibit different types of nitrogen-containing groups in the NCCFs, and the peaks at 400.6 eV (quaternary N (N-Q) species, 48.8%) and 398.1 eV (pyridine (N-6) species, 26.2%)38,39 were generated with the presence of melamine and urea, respectively. The peak associated with nitro-type complexes NO2 (5.5%) at 406.5 eV should be associated with acid treatment. It is well known that the positively charged N-Q and nitrogen oxide (N-X) (401.8 eV, 7.8%) could improve electron transfer, resulting in enhanced capacitive performance under larger current densities. The negatively charged pyrrole or pyridine (N-5) and N-6, on the other hand, could offer pseudo-capacitive interactions, leading to further enhancement in the specific capacitance40,41,42.

Figure 6
Figure 6

XPS spectra for CCFs and NCCFs (a) and N1s spectra of NCCFs (b).

The results of above characterizations imply that the as-prepared NCCFs present similar morphological and structural features to the typical 3D graphene- and CNT-based frameworks. Owing to such porous 3D carbon frameworks, they should be also ideal to serve as electrode materials for supercapacitors. First, the cotton-derived 3D carbon frameworks were fabricated into a three-electrode system (6 mol L−1 KOH aqueous electrolyte) for electrochemical measurements. Figure 7a shows the typical cyclic voltammetry (CV) curves of CCFs and NCCFs at 5 mV s−1. The curves demonstrate quasi-rectangular shape with slight distortion, which is mainly induced by the pseudo-capacitance due to the oxygen and nitrogen functional groups. The redox signals of nitrogen-doped carbon electrodes are unobvious especially in alkaline electrolyte, which is in accordance with many reported works39,42,43,44. Apparently, NCCFs show much larger area than CCFs. As illustrated in Fig. 7b, the electrical resistance and ion transfer of the as-prepared supercapacitors were characterized on the electrochemical impedance spectroscopy (EIS) over a frequency range from 10−2 to 105 Hz. According to the diameters of the semicircles at high frequency range, NCCFs exhibit lower resistance (~0.5 Ohm) than that of CCFs (~1.5 Ohm), which may be related to the promoted electron transfer with presence of N-Q and N-X. At lower frequency, all the samples present nearly vertical line, which suggests that the aerogel-like 3D porous frameworks facilitate the electrolyte transport in the cotton-derived carbon electrodes.

Figure 7
Figure 7

Electrochemical performance of CCFs and NCCFs measured in 6 mol L−1 KOH using three-electrode system: CV curves at 5 mV s−1 (a); Nyquist plots (b); Galvanostatic charge-discharge curves of NCCFs at different current densities (c); Rate performance of CCFs and NCCFs (d); Cycle stability of NCCFs at a current density of 5 A g−1 (e).

Figure 7c exhibits the galvanostatic charge-discharge curves of NCCFs at different current densities. The almost isosceles triangles indicate an excellent double-layer capacitance with no obvious voltage drop (IR drop) observed, which is in good agreement with the low resistance in Fig. 7b. The specific capacitance was acquired according to the equation of CS = I × t/V/m, where Cs (F g−1) is the specific capacitance, I (A g−1) the response current density, t (s) the discharge time, V (V) the potential and m (g) the mass of active material. As demonstrated in Fig. 7d, the specific capacities of the NCCFs present the highest capacities, approaching 308 F g−1 and 200 F g−1 at current densities of 0.1 A g−1 and 10 A g−1, respectively. As exhibited in Fig. 7e, NCCFs shows a high retention up to 97% after 10,000 cycles at a current density of 5 A g−1, suggesting excellent cycle stability. It is noticed that the NCCFs with surface area only up to 285 m2 g−1 show very high capacities and excellent retention in the cycles, which should be mainly due to the high-concentration doped nitrogen (12.1 mol%) that not only introduces sufficient pseudocapacitance but also improves the electronic structure of graphitic carbon as well45

A symmetrical flexible all-solid-state supercapacitor was further fabricated using the as-prepared electrodes coupled with PVA/KOH gel electrolyte (Fig. 1)46. The electrochemical properties of the all-solid-state supercapacitors are exhibited in Fig. 8. Figure 8a exhibits the CV curves at different current densities, and no pronounced redox peaks have been observed, suggesting typical double-layer capacitive behavior. The impedance in Fig. 8b shows only slight increase of impedance (~2 Ohm) in all-solid-state supercapacitors compared to the values in the three-electrode system. However, the vertical line in the low frequency region also indicates the fast ion transport in the PVA/KOH electrolyte (Fig. 8b). According to the galvanostatic charge/discharge curves in Fig. 8c, similar isosceles triangles were also observed except for the presence of limited IR drop. The specific capacitance of the electrodes in a two-electrode supercapacitor was achieved by the formula that Cs = 4I × t/V/m, where m is the mass of the active material in both electrodes. Figure 8d displays the rate stability of the all-solid-state supercapacitor, showing the highest capacitance up to 220 F g−1. After 10,000 cycles at a current density of 5 A g−1, the all-solid-state supercapacitor presented excellent cycle ability with 98% retention (Fig. 8e). In order to measure the capacitance retention under stress, the flexible supercapacitors were bent with different angles and the results show negligible effects on the capacitance upon bending (Fig. 8f).

Figure 8
Figure 8

Electrochemical performance of NCCFs all-solid-state supercapacitors using PVA/KOH gel electrolyte (two-electrode system): CV curves at different scan rates (a); Nyquist plot (b); Galvanostatic charge-discharge curves at different current densities (c); Specific capacities at various current densities (d); Cycle stability at a current density of 5 A g−1 (e); CV curves at a scan rate of 5 mV s−1 under different bending angles (f).


The results demonstrate that the cotton-derived 3D carbon frameworks present graphene aerogel-like morphologies and structures, which allow the electrolyte to deliver fast ion transport in the porous frameworks and meanwhile enable carbon interconnected networks to serve as the effective pathways for electron transport. On the basis of the sufficient surface area of the conductive porous carbon frameworks, further enhanced capacitance could be easily achieved by the introduced N-doped functional groups. In a typical work by Ruoff and coworkers, it is suggested that the increasing N content (0.7~2.3 wt% N) would contribute to greater enhancement in the capacitive capability of the N-doped graphite oxide (Table S2)42. Similar results in the work by Chen and coworkers also suggest the carbon with 11.89% N content substantially enhanced the specific capacitance43. Therefore, such NCCFs with highly concentrated N-containing groups (12.1 wt% N) are expected to exhibit promising electrochemical performance. In the three-electrode configuration, it is interesting to find that the capacitance in NCCFs is well competitive to that found in the graphene- and CNT-based 3D frameworks (Table S2). According to the price listed in Table S1 and direct comparison of typical performance of other carbon-based electrodes, the results suggest that such low-cost 3D carbon sources with the facile strategy provide sufficient capacitance similar to the fashion carbon materials of high expense. Unlike relatively high surface areas based on the presence of CNTs and graphene in the aerogel-like structures, NCCFs here based on simply doped with high-concentration N-functional groups, which are responsible for both enhancing pseudocapacitance and facilitating electron transfer in the NCCF frameworks, have exhibited the comparable charge storage to those based on large surface areas and sufficient pore sizes.

It may be argued that the NCCFs should be directly fabricated into the binder-free electrodes for taking their advantages. In comparison, the binder-free electrode was fabricated via directly compressing the NCCF onto the Ni foam. In the same three-electrode system of 6 M KOH aqueous electrolyte, the electrochemical performance of the binder-free electrode was 173, 124 and 52 F g−1 at current densities of 0.1, 1 and 5 A g−1, respectively (Figure S6). Apparently, the binder-free systems were far behind the binder systems (308 and 200 F g−1 at 0.1 and 10 A g−1, respectively). Therefore, the binder systems can deliver more promising performance for electrochemical storage. This observation is highly usual in the biomass-based active materials31,32,45, which are general required to be mixed up with binders and conductive agents to fully realize the optimal electrochemical performance. Furthermore, the mass loading of the binder electrode could reach ~9 mg/cm2, which is more close to the practical supercapacitors. However, the mass loading of the binder-free electrode was only up to 4 mg/cm2 due to the highly porous framework, which may not meet the practical applications. Although the mixing process with binder and conductive agent might change the framework morphology, it is believed to be the optimized approach to fully use the capacitive capability.

Apparently, there are more opportunities for further improving the device performance because related enhancements including optimization of cotton carbonization for tuning the sp2 carbon, enlargement of the surface area and porosity or adjustment of the heteroatomic doping (N- and B-doing for examples) could be performed on the current stage, by which the fundamental understanding of the impacts on the device performance would be also achieved. Compared to the mostly attractive graphene and CNT-based 3D frameworks, the cotton-derived configurations appear to be more promising in the large-scale applications because of the much lower cost and easier scalability. Therefore, the commercially available cotton coupled with simply strategies has shown a new stage for scalable fabrication of high-performance supercapacitors.


In conclusion, a facile and low-cost approach was demonstrated for scalable fabricating high-performance electrodes for supercapacitors. The commercially available cotton was used as the carbon source for preparing aerogel-like 3D nanostructures, which are favorable for both the ion and electron transport. Therefore, the resulting N-doped cotton-derived frameworks present effective capacitance, highly competitive to the performance observed in the other graphene- and CNT-based 3D frameworks. The strategy demonstrated here is very simply, low cost, easy scale-up and efficient, showing great potential for wide applications in the energy storage industry.


Synthesis of CCFs and NCCFs

The commercial cotton was directly used as the starting material without any further pre-treatment. Typically, a piece of cotton was cut into a certain shape (determined by the furnace size) and mixed with melamine and urea with mass ratio of 1:2:2. Subsequently, the mixture was subjected to carbonization at 800 oC for 1 h with a heating rate of 5 oC min−1 under N2 atmosphere. The resulting samples were further treated under ultrasonication for 1h with the presence of mixture of HNO3/H2SO4 (v/v = 1/3, 70% HNO3 and 98% H2SO4). The resulted samples (NCCFs) were then washed with distilled water and dried at 90 oC overnight. For comparison, the reference samples (CCFs) were prepared under the same conditions except for the absence of melamine and urea.

Field-emission scanning electron microscopy (FESEM) was conducted on ZEISS supra 55 system. Transmission electron microscope (TEM) was performed on JEOL JEM-2010. Raman spectra were carried out on HR800 (Horiba JobinYvon) with a 514.5 nm Ar-ion laser. The nitrogen absorption/desorption isotherms associated with specific surface area and pore diameter distribution data were investigated on an Autosorb-iQ2-MP (Quantachrome) analyzer under 77k. X-ray photoelectron spectroscopy (XPS) was acquired on PHI-5300. Static tensile tests were performed with a mechanical analyzer (TA-XT Plus system, SMS).


The electrochemical performance of the carbon materials was determined in a three-electrode cell with basic aqueous solutions. The working electrode was prepared by mixing the carbon samples, acetylene black with polytetrafluoroethylene in a weight ratio of 80:15:5, and then the mixture was pressed onto a nickel foam. The typical mass and dimensions of the working electrodes are 10 mg and 1 cm2. For the three-electrode system, Pt and Hg/HgO electrode were used as the counter electrode and reference electrode, respectively, while the KOH solution (6 mol L−1) was employed as the electrolyte.

Electrochemical evaluation

The electrochemical performance of NCCFs was further determined in a gel electrolyte by using a two-electrode cell. Similar to the three-electrode system, the working electrode for two-electrode system was also fabricated with the carbon samples, acetylene black and polytetrafluoroethylene (80:15:5 in weight ratio), followed by being pressed onto a nickel foam. For the two-electrode system, an all-solid-state supercapacitor was fabricated as depicted in Fig. 1c. In a typical preparation, PVA powder (2 g) was dissolved in distilled water (20 mL) under vigorous stirring at 85 oC, followed by immersing two pieces of NCCFs electrodes in the PVA solution. Then, excessive KOH solution (6 M, 200 mL) was added and the mixture was kept for 24 h to form all-solid-state supercapacitors, where the PVA/KOH gel served as both electrolytes and separators.

Galvanostatic charge/discharge was tested at various current densities using LAND-CT2001A (Wuhan Jinnuo Electronics. Ltd.). Cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) were carried out using a CHI660C electrochemical workstation (CH Instruments, Inc.).

Additional Information

How to cite this article: Fan, L.-Z. et al. High nitrogen-containing cotton derived 3D porous carbon frameworks for high-performance supercapacitors. Sci. Rep. 5, 15388; doi: 10.1038/srep15388 (2015).


  1. 1.

    , , , & Activated graphene-based carbons as supercapacitor electrodes with macro- and mesopores. ACS Nano 7, 6899–6905 (2013).

  2. 2.

    , , & Chemical vapor deposition of mesoporous graphene nanoballs for supercapacitor. ACS Nano 7, 6047–6055 (2013).

  3. 3.

    et al. Flexible asymmetric supercapacitors based upon Co9S8 nanorod//Co3O4@RuO2 nanosheet arrays on carbon cloth ACS Nano 7, 5453–5462 (2013).

  4. 4.

    , , , & Highly flexible and all-solid-state paperlike polymer supercapacitors. Nano Lett. 10, 4025–4031 (2010).

  5. 5.

    , , , & Printable thin film supercapacitors using single-walled carbon nanotubes. Nano Lett. 9, 1872–1876 (2009).

  6. 6.

    et al. Flexible supercapacitor made of carbon nanotube yarn with internal pores. Adv. Mater. 26, 2059–2065 (2013).

  7. 7.

    , , & Advances and challenges for flexible energy storage and conversion devices and systems. Energy Environ. Sci. 7, 2101–2122 (2014).

  8. 8.

    , , , & Flexible solid-state supercapacitors: design, fabrication and applications. Energy Environ. Sci. 7, 2160–2181 (2014).

  9. 9.

    , & Recent progress on nitrogen/carbon structures designed for use in energy and sustainability applications. Energy Environ. Sci. 7, 1212–1249 (2014).

  10. 10.

    , & 3D carbon based nanostructures for advanced supercapacitors. Energy Environ. Sci. 6, 41–53 (2013).

  11. 11.

    , , & Ideal three-dimensional electrode structures for electrochemical energy storage. Adv. Mater. 26, 2440–2445 (2014).

  12. 12.

    et al. High-performance multifunctional graphene yarns: toward searable all-carbon energy storage textiles. ACS Nano 8, 2456–2466 (2014).

  13. 13.

    & Carbonaceous hydrogels and aerogels for supercapacitors. J. Mater. Chem. A 2, 4852–4864 (2014).

  14. 14.

    , , & . Graphene with three-dimensional architecture for high performance supercapacitor. Carbon 67, 221–229 (2014).

  15. 15.

    , & Three-dimensional graphene materials: preparation, structures and application in supercapacitors. Energy Environ. Sci. 7, 1850–1865 (2014).

  16. 16.

    et al. Compact-designed supercapacitors using free-standing single-walled carbon nanotube films Energy Environ. Sci. 4, 1440–1446 (2011).

  17. 17.

    & Flexible supercapacitors based on carbon nanomaterials J. Mater. Chem. A 2, 10756–10775 (2014).

  18. 18.

    et al. Carbon nanotube−nanocup hybrid structures for high power supercapacitor applications Nano Lett. 12, 5616–5621 (2012).

  19. 19.

    et al. Flexible solid-state supercapacitors based on three-dimensional graphene hydrogel films ACS Nano 7, 4042–4049 (2013).

  20. 20.

    et al. Three-dimensional nitrogen and boron co-doped graphene for high-performance all-solid-state supercapacitors. Adv. Mater. 24, 5130–5135 (2012).

  21. 21.

    et al. A Versatile, ultralight, Nitrogen-doped graphene framework. Angew. Chem. 124, 11533–11537 (2012).

  22. 22.

    , & Graphene-based materials in electrochemistry Chem. Soc. Rev. 39, 3157–3180 (2010).

  23. 23.

    et al. Chemical vapor deposition of N-doped graphene and carbon films: the role of precursors and gas phase. ACS Nano 8, 3337–3346 (2014).

  24. 24.

    , , & Laser scribing of high-performance and flexible graphene-based electrochemical capacitors. Science 335, 1326–1330 (2012).

  25. 25.

    , , , & Lower-defect graphene oxide nanoribbons from multiwalled carbon nanotubes. ACS Nano 4, 2059–2069 (2010).

  26. 26.

    et al. Dynamic Electrosorption analysis as an effective means to characterise the structure of bulk graphene assemblies. Chem. Eur. J. 19, 3082–3089 (2013).

  27. 27.

    et al. Facile fabrication of ultrathin graphene papers for effective electromagnetic shielding. J. Mater. Chem. C 2, 5057–5064 (2014).

  28. 28.

    et al. Ultrastrong, foldable, and highly conductive carbon nanotube film. ACS Nano 6, 5457–5464 (2012).

  29. 29.

    , , & Strong, conductive, lightweight, neat graphene aerogel fibers with aligned pores. ACS Nano 6, 7103–7113 (2012).

  30. 30.

    et al. Large-area flexible core–shell graphene/porous carbon woven fabric films for fiber supercapacitor electrodes. Adv. Funct. Mater. 23, 4862–4869 (2013).

  31. 31.

    et al. Human hair-derived carbon flakes for electrochemical supercapacitors. Energy Environ. Sci. 7, 379–386 (2014).

  32. 32.

    , , & From dead leaves to high energy density supercapacitors. Energy Environ. Sci. 6, 1249–1259 (2013).

  33. 33.

    , & Carbon Microfibers with Hierarchical Porous Structure from Electrospun Fiber-Like Natural Biopolymer. Sci. Rep. 3, 1119 (2013).

  34. 34.

    et al. Effects of the functional groups on the electrochemical properties of ordered porous carbon for supercapacitors Electrochim. Acta 105, 299–304 (2013).

  35. 35.

    et al. Supercapacitors Prepared from Melamine-Based Carbon. Chem. Mater. 17, 1241–1247 (2005).

  36. 36.

    et al. Easy preparation of nitrogen-enriched carbon materials from peptides of silk fibroins and their use to produce a high volumetric energy density in supercapacitors. Carbon 45 2116–2125 (2007).

  37. 37.

    et al. The Large Electrochemical Capacitance of Microporous Doped Carbon Obtained by Using a Zeolite Template. Adv. Funct. Mater. 17, 1828–1836 (2007).

  38. 38.

    et al. Nitrogen-doped graphene with high nitrogen level via a one-step hydrothermal reaction of graphene oxide with urea for superior capacitive energy storage. RSC Adv. 2, 4498–4506 (2012).

  39. 39.

    , , , & Nitrogen-doped graphene nanosheets from bulk graphite using microwave irradiation. ACS Appl. Mater. Interfaces 6, 6361−6368 (2014).

  40. 40.

    , , & Combined effect of Nitrogen- and Oxygen-containing functional groups of microporous activated carbon on its electrochemical performance in supercapacitors Adv. Funct. Mater. 19, 438–447 (2009).

  41. 41.

    , & Differentiate the pseudocapacitance and double-layer capacitance contributions for nitrogen-doped reduced graphene oxide in acidic and alkaline electrolytes J. Power Sources 227, 300–308 (2013).

  42. 42.

    et al. Nitrogen doping of graphene and its effect on quantum capacitance, and a new insight on the enhanced capacitance of N-doped carbon. Energy Environ. Sci. 5, 9618–9625 (2012).

  43. 43.

    et al. Nitrogen-doped carbon monolith for slkaline supercapacitors and understanding Nitrogen-induced redox transitions. Chem. Eur. J. 18, 5345–5351 (2012).

  44. 44.

    , & Electrochemical performance of Nitrogen-enriched carbons in aqueous and non-aqueous supercapacitors. Chem. Mater. 18, 2318–2326 (2006).

  45. 45.

    et al. Nitrogen-containing hydrothermal carbons with superior performance in supercapacitors Adv. Mater. 22, 5202–5206 (2010).

  46. 46.

    , & Rational design of graphene/porous carbon aerogels for high-performance flexible all-solidstate supercapacitors J. Mater. Chem. A 2, 10895–10903 (2014).

Download references


The authors gratefully acknowledge financial support from National Basic Research Program of China (973 program) (No. 2013CB934001), NSF of China (51532002, 51172024, 51372022, and 51575030), and Ministry of Education (20130006110019).

Author information


  1. Key Laboratory of New Energy Materials and Technologies, Institute of Advanced Materials and Technology, University of Science and Technology Beijing, Beijing 100083, P. R. China.

    • Li-Zhen Fan
    • , Tian-Tian Chen
    • , Wei-Li Song
    •  & Xiaogang Li
  2. School of Materials Science and Engineering, Beihang University, Beijing 100191, China

    • Shichao Zhang


  1. Search for Li-Zhen Fan in:

  2. Search for Tian-Tian Chen in:

  3. Search for Wei-Li Song in:

  4. Search for Xiaogang Li in:

  5. Search for Shichao Zhang in:


L.Z.F., X.G.L. and S.C.Z. devised the original concept, designed the experiments, discussed the interpretation of results and co-wrote the paper. T.T.C. prepared the samples and W.L.S. performed the electrochemical experiments. All authors discussed the results and participated in manuscript revision.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Li-Zhen Fan or Xiaogang Li or Shichao Zhang.

Supplementary information

Word documents

  1. 1.

    Supporting Information

About this article

Publication history





Further reading


By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.