Article | Open | Published:

N-Doped Carbon NanoWalls for Power Sources

Abstract

Cycling stability and specific capacitance are the most critical features of energy sources. Nitrogen incorporation in crystalline carbon lattice allows to increase the capacitance without increasing the mass of electrodes. Despite the fact that many studies demonstrate the increase in the capacitance of energy sources after nitrogen incorporation, the mechanism capacitance increase is still unclear. Herein, we demonstrate the simple approach of plasma treatment of carbon structures, which leads to incorporation of 3 at.% nitrogen into Carbon NanoWalls. These structures have huge specific surface area and can be used for supercapacitor fabrication. After plasma treatment, the specific capacitance of Carbon NanoWalls increased and reached 600 F g−1. Moreover, we made a novel DFT simulation which explains the mechanism of nitrogen incorporation into the carbon lattice. This work paves the way to develop flexible thin film supercapacitors based on carbon nanowalls.

Introduction

Carbon NanoWalls (CNWs) were discovered several decades ago and now they show a certain potential for fabrication of various-purpose devices. Despite the fact that many properties of these materials are already well-known, new areas of application keep emerging1,2. CNWs are characterized by high specific surface area and can be used in fabrication of supercapacitors, hydrophobic surface coatings, field emitters and other products. Earlier, our team published a paper on electrochemical activation of CNWs synthesized by Direct Current Plasma Enhanced Chemical Vapor Deposition (DC PECVD)3. The electrochemical activation led to an increase in electrode specific capacitance from 105 F g−1 to 120 F g−14. The composite electrode based on CNW@Si@CNW or CNW@Ge@CNW shows good stability and can be used to produce thin-film Li-ion batteries5,6, fabricate fuel cells7 or serve as a template for other catalytic materials8.

The most promising field of application for this material is electrodes for thin-film supercapacitors, which have become more popular recently due to ubiquitous adoption of wearable electronics and portable devices9,10. Crucial properties of CNWs are their high specific surface area, high electrical conductivity along graphite layers, and a total thickness of less than 5 µm. CNWs can be synthesized on the surface of different metals, semiconductors, carbon materials such as carbon paper and carbon fiber, thus allowing to fabricate flexible energy sources11. However, despite the fact that specific surface area of CNW amounts up to 1000 m2 g−15, its specific capacitance reaches values of ~120 F g−14. In order to increase specific capacitance of carbon materials, various metals oxide decoration methods are applied and, as a result, specific capacitance values of the structures are electrochemically enhanced by several times12,13. The decoration process requires additional technological procedures during or after the synthesis process. Recently, various nitrogen incorporation processes during the synthesis of graphene were demonstrated to have a positive effect on its specific capacitance due to an appearance of additional redox reactions14. One of these post-modification techniques, plasma treatment, was demonstrated to be able to produce a modified graphene with a specific capacitance of 855 F g−115,16. Due to the fact that carbon materials possess chemically and structurally tunable properties, various methods of modification during the material synthesis stage have been proposed. These techniques include chemical vapor deposition and chemical tuning17,18.

In this paper, we investigate the electrochemical performance of CNWs after plasma modification. We report an increase in specific capacitance by a factor of 4.5 after the plasma-enhanced DC glow-discharge modification. Since CNW morphology is easy to modify with extensive plasma-enhanced post treatment, the reported technique can be used to produce energy storage devices.

Experimental

Materials synthesis

Rectangular glassy carbon electrodes (A = 0.5 cm2) were used as substrates for carbon nanowalls growth. The synthesis was carried out using DC PECVD in CH4 and H2 atmosphere2,8. This method resulted in thin CNW films on glassy carbon. We estimated the areal loading of CNW on glassy carbon substrates by growing films on large substrates (A = 4 cm2) and weighing. Thickness of the film was estimated from SEM views to be 2 μm. CNWs modification was performed in DC glow discharge with cylindrical cathode. Discharge voltage and current were 2 kV and 80 mA, respectively. Nitrogen pressure during the CNW treatment was 0.02 Torr. Modifications took place during first 2 hours. After 2 hours, we noticed no further changes in Raman spectra.

Material characterization

Electrochemical studies were performed in 1 M H2SO4 solution on Advanced Electrochemical System Parstat 2273. Glassy carbon electrodes with CNW films were used as working electrodes in an asymmetric scheme with a large-area Au counter electrode and a standard hydrogen reference electrode. Structural analysis was performed with a use of Scanning Electron Microscope (SEM) Carl Zeiss Supra 40, Thermo Scientific DXR Raman Microscope spectrometer. X-ray photoelectron spectra (XPS) were recorded on an Axis Ultra DLD spectrometer (Kratos) using monochromatic Al Kα radiation.

Computer modeling

DFT simulations were carried out with VASP (Vienna Ab initio Simulation Package) code19 and ORCA software20,21. GGA approximation with PBE exchange-correlation functional was applied for a larger model of graphene flake (72 and 120 atoms) to simulate potential chemical reactions, induced by N and O atoms, and hybrid B3LYP functional was used for a smaller model (~30 atoms) to estimate XPS shift for N-containing functional groups.

Results

A SEM image of CNWs is presented in Fig. 1.

Figure 1
figure1

SEM image of CNW film. Top right inset shows Raman spectra of raw CNWs and CNWs after plasma modification in DC glow-discharge. D, G and 2D bands are indicated.

For the raw materials, the I(D)/I(G) ratio is 0.78, while the I(2D)/I(G) is 0.90. After 2 hours of plasma treatment, these values changed to 1.32 and 0.60, respectively (Fig. 1 inset). The shift of the ratios implies that the CNW structure has changed.

To reveal the chemical state of carbon and nitrogen atoms, as-deposited CNWs, CNWs treated by the N2 plasma (further referred as NCNWs), and NCNWs after electrochemical cycling were analyzed by XPS (Fig. 2). XPS was preferred to CHNS in order to gain insight into atomic bonds and not only atomic content, and the penetration depth of XPS was sufficient for 2 μm thin films. The C1s XPS spectrum of CNWs contains the main contribution from sp2 carbon (284.5 eV) and a small peak at 284.9 eV that may be assigned to sp3 carbon. The oxygen content in this sample is ~2 at.%, while no nitrogen was detected by XPS. After plasma modification, the oxygen content sharply increases up to ~29.7 at.% and the nitrogen peak appears in the spectrum (Fig. 2b), corresponding to 2.4 at.% of nitrogen. This peak may be fitted by three components attributed to pyridinic nitrogen22 (N1, 0.3 at.%), pyrrolic or pyridonic nitrogen16,22 (N2, 2.4 at.%), and quaternary (graphitic) or oxidized pyridinic nitrogen species22 (N3, 0.5 at.%). In the C1s spectrum of this sample, the Cdef peak at a binding energy lower than that of sp2 carbon is observed (Fig. 2a). This peak corresponds to nitrogen bonding to defect sites in sp2 carbon22. After 100 electrochemical cycles, the pyridinic (N1) peak disappears from the N1s spectrum while the content of N2 and N3 nitrogen species changes to 1.3 and 1.2 at.%, respectively. At the same time, the total nitrogen content only slightly changes after cycling (2.5 at.%). Cycling also increases the contribution of C−O bonds in the C1s spectrum at about 286.5 eV.

Figure 2
figure2

High resolution C1s (a) and N1s (b) XPS spectra of CNWs, NCNWs and NCNWs after cycling voltammetry.

Electrochemical studies were performed in 1 M H2SO4 solution. Figure 3a shows cyclic voltammetry curves of CNWs for different scan rates. The same set of curves is presented for so-called NCNW samples. Specific capacitance was calculated as the area enclosed by the cyclic voltammetry curve, normalized by the potential range and the scan rate. A comparison of voltammetry curves is presented in Fig. 3c. Results show that glow-discharge plasma modification leads to an improvement in specific electrochemical capacitance from 104 F g−1 to 464 F g−1. These results are in a good agreement with work4. Thus, the plasma treatment process leads to an increase in specific capacitance of structures by a factor of 4.5. It can be assumed that such increase in capacitance correlates with oxygen content. However, according to another study, the increase of oxygen presence inside of the carbon structure doesn’t prominently affect the capacitance4,23. We attribute the increase in specific capacitance to nitrogen atom adsorption in bridge positions, as described below in the discussion section. N-doped CNWs demonstrate insignificant changes in specific capacitance with cycle number (Fig. 3d). We attribute this to slight changes in oxygen presence during cycling, despite a low potential range23.

Figure 3
figure3

Cyclic voltammetry in 1 М H2SO4 electrolyte. (a) Electrochemical properties of CNWs before treatment, (b) NCNWs properties after plasma treatment, (c) and (d) cyclic voltammetry and cyclic stability of CNWs and NCNWs at scan rate of 20 mV s−1.

Discussion

CNW films placed on the anode of the dc discharge are subject to radical fluxes (N atoms), electrons and plasma radiation (no ion fluxes on the samples). Discharge current density at the cathode (j~0.4 mA cm−2) and measured cathode temperature Tc = 310 K hints at an abnormal regime of the discharge operation. Based on plasma-chemical and electron kinetics calculations of N2 plasma24 we estimate the electron and ion concentration ne ≈ ni~108 cm−3, reduced electric field E/N~55 Td and respective electron temperature Te~1 eV in positive column between the cathode and sample surfaces. In these conditions, N atoms in ground N(4S) and lowest metastable N(2D) and N(2P) states are effectively produced in N2 dissociation by electron impacts. Cathode beam electrons also contribute to N2 dissociation. Monte Carlo calculations of the beam electrons energy dissipation show that ~1/3 of the gained energy goes into N2 dissociation and the remaining part is mostly due to N2 ionization3.

Negative oxygen ions (e.g. O as a main ion in our conditions) and other NxOy species are also produced in air dc discharge plasma and, in lesser degree, in nitrogen plasma (due to air admixture). Negative ions in anode sheath could gain the hyperthermal energies (of about and lower than typical anode sheath potentials ~15–20 eV) and induce only slow erosion of the CNW surface (removal or substitution of surface C atoms). The created C-vacancies and surface could be occupied by impinging N and O atoms to produce various N and O containing surface sites observed in the XPS spectra, e.g. pyridinic N (N bonded to two carbon atoms), graphitic N (N bonded to three carbon atoms, also called substituted N or quaternary N) where surface C atoms are substituted by N atoms, pyrrole N and nitrogen oxide sites16. Pyridinic N sites and some O sites could be responsible for alteration of the CNW specific capacitance and catalytic activity15,16. In recent study16, it was revealed that pyridinic N in nitrogen-doped graphitic carbons creates the active sites for the oxygen reduction reaction (ORR). Carbon atoms next to pyridinic N are suggested to be the active sites at which O2 molecules are adsorbed as the initial step of the ORR16. We cannot exclude that the additional surface oxidization could be related with these active sites. It should be also noted that these stable N and O contained sites could be also removed by energetic O ions.

In our N2 (with air admixture) and air plasmas, O ions are mainly produced in dissociative attachment reaction

$${{\rm{O}}}_{2}+{\rm{e}}\to {{\rm{O}}}^{-}+{\rm{O}}$$
(1)

Here O2 molecules in ground (O2(X3Σg)) and lowest singlet (O2(a1Δ)) states will contribute in O production. O ions are destructed at the anode and associative attachment reactions

$${{\rm{O}}}^{-}+{\rm{O}}\to {{\rm{O}}}_{2}+{\rm{e}}$$
(2)
$${{\rm{O}}}^{-}+{{\rm{O}}}_{2}({{\rm{a}}}^{1}{\rm{\Delta }})\to {{\rm{O}}}_{3}+{\rm{e}}$$
(3)
$${{\rm{O}}}^{-}+{\rm{N}}\to {\rm{NO}}+{\rm{e}}$$
(4)
$${{\rm{O}}}^{-}+{\rm{NO}}\to {{\rm{NO}}}_{2}+{\rm{e}}$$
(5)

The concentrations of O ions in positive column and anode layer will be determined by a balance of all these processes.

Possible reactions of N and O atoms on the created N and O sites of CNW surface were studied by density functional theory (DFT) method (the details of similar DFT modeling of N atoms interactions with low-k SiOCH films are described25). N(4S) atoms do not induce chemical reactions on regular graphene sheets, DFT calculations show only physical adsorption of an N(4S) atom above the graphene plane without chemical bonding with C atoms. In contrast to (N4S), metastable (N(2D) and N(2P)) atoms produce C-N-C bridge groups (Fig. 4a). However, these bridge N-states can be easily removed by oxygen or nitrogen atoms/ions (Fig. 4b):

$${{\rm{N}}}_{{\rm{bridge}}}+{{\rm{O}}}_{{\rm{gas}}}\to {{\rm{NO}}}_{{\rm{gas}}}$$
(6)
$${{\rm{N}}}_{{\rm{bridge}}}+{{\rm{N}}}_{{\rm{gas}}}\to {{\rm{N}}}_{2{\rm{gas}}}$$
(7)
Figure 4
figure4

(a) N atom adsorbed in bridge position in the center of graphene flake; (b) the formation of a volatile NO species due to the O atom interaction with the bridge N site; (c) an N atom embedded into the carbon network; (d) an N atom adsorbed at the C-vacancy. C, H, N and O atoms are shown as grey, white, blue and red circles, respectively.

The potential erosion of CNW surfaces by energetic O ions facilitates the insertion of N atoms into C-vacancies leading to the formation of pyridinic (N1), pyrrolic (N2) and graphitic (N3) states. These states are tightly bound with neighboring carbon atoms and are very stable as compared with bridge C–N–C states. Our static DFT calculations revealed that only excited N atoms are able to embed into a C-vacancy substituting a missing C atom and restoring the hexagonal network (Fig. 4c). The similar mechanism can be responsible for the formation of pyridinic and pyrrol sites. A ground-state N(4S) atom can be adsorbed on the C atom with a dangling bond (Fig. 4d). The energy of this state is 7.2 eV higher, and a substantial reconstruction of the graphene flake is observed and indicated that the formation of such C–N bonding is not probable for a flat graphene surface. However, additional pathways for N(4S) incorporation should be studied with dynamic DFT calculations since we cannot exclude potential intersystem crossing and graphene surface reconstruction.

The obtained results can explain the observed difference in nitrogen and oxygen content in the experimental XPS spectra as it was stated above (after N2 plasma exposure 2.4 at.% vs. 29.7 at. % for nitrogen and oxygen, respectively). In literature, 10–35 wt % of nitrogen contents (and similar surface N/C ratios) in nitrogen-doped carbon materials are reported in dependence on the carbonization temperature (e.g. ~500–1000 C) and relative independence on “the carbonaceous precursor, preparation conditions, and carbon type (porous carbon or graphene)”26. In our experiments, a rather different process of carbon surface enrichment by N atoms results in much lower percentage of surface N/C in CNWs at near room temperatures. The DFT calculations show the following principal problems of nitrogen (and oxygen) incorporation into CNWs under fluxes of thermal atoms. Even the most probable radical-radical addition reactions are not always feasible for ground states atoms N(4S). Excited atoms (e.g. metastable N(2D)) of lower concentrations are required for such reactions. In addition, the created single bond sites C-N or N bridge sites over regular graphene surface are easily destroyed under further impacts of atoms N and O resulting in volatile products N2 and NO, respectively. The production of stable nitrogen sites (N atoms binding with two or three surface C atoms) requires special and rare surface configurations (sites) e.g. C vacancies, two adjacent C vacancies at the CNW edges. The limited number of these appropriate sites (presented in as-deposited CNW films or created by hyperthermal O ions and O atoms) implies low percentage of stably incorporated nitrogen.

Diverse reactions of O atoms with various surface sites (including nitrogen sites) will be reported in a separate paper. In general, O atoms are more reactive with CNW surface than N atoms, and O atoms/ions are able to form more stable ether-like C–O–C bridge groups and initiate chemical reactions leading to the formation of defects (vacances) and volatile CO and CO2 molecules27,28. However, the observed high uptakes of oxygen (much higher than the fractions of incorporated nitrogen) are mainly related to ex-situ oxygen adsorption in ambient air. 7.4% ± 0.3% fractions of surface oxygen after N-implantation of HOPG at ion’s dosages of 1015–1017 ions/cm229. The authors29 have explained this effect by “reactive surface defects (i.e., dangling bonds, step edges, radicals, etc.) created by the implantation process are immediately passivated and/or oxidized by oxygen species upon exposure to atmosphere”. In our DFT calculations, we have also observed the dissociation of O2 molecules on C-vacancies. Moreover, atmospheric molecular oxygen can dissociate at C-vacancies30, forming strong C–O and C=O bonds and thus increasing the oxygen content.

DFT calculations were also carried out to explain the obtained XPS spectra. We have calculated the thresholds of X-ray absorption spectra with B3LYP exchange-correlation functional; these thresholds are closely related to the shift in the XPS spectrum due to chemical bonding31. The difference between calculated shifts for pyridinic (N1) and graphitic (N3) groups is ~3.2 eV which coincides quite well with the experimental data (401.8–398.2 = 3.6 eV, see Fig. 2). When H atom interacts with pyridinic N site, an N–H bond forms, and the N atom becomes bound with three atoms. The calculated shift for such a configuration is ~2.6 eV higher than for the initial pyridinic N site indicating that H adsorption on this site leads to its conversion from pyridinic-N to graphitic-N or to pyrrolic-N in the XPS spectra. Such an effect was observed in32, when the exposure to hydrogen caused the disappearance of N1 peak and the enhancement of graphitic N3 peak. The similar shift could be induced by OH radical adsorption near a pyridinic site and its transformation into a pyridonic site16.

Conclusion

In this study, we demonstrate a simple and efficient approach for surface modification of carbon materials. In particular, we used graphene derivative called Carbon NanoWalls, which are known for high specific surface area and can be used as active materials to produce electrochemical energy sources. As-deposited CNWs posses no nitrogen content. After CNWs treatment by N2 DC discharge plasma (CNWs were placed on anode and exposed to N atoms, electrons and negative ions), three forms of the incorporated nitrogen are detected by XPS: pyridinic, pyrrolic and graphitic sites. After electrochemical study of cyclic voltammetry in 1 M H2SO4 solution, we have detected the disappearance of pyridinic sites, minor changes in pyrrolic sites fraction and doubling of graphitic sites. DFT calculations were used to study possible production mechanisms for these nitrogen sites. Our research demonstrates the incorporation of nitrogen up to ~3 at.%, which leads to an increase in electrochemical specific capacitance by a factor of 4.5–6. The specific capacitance of Carbon NanoWalls at a scan rate of 20 mV s−1 reached ~600 F g−1, while that of non-modified structures was only 105 F g−1. We assume that the proposed technique can be used for effective post-treatment surface modification of carbonaceous materials.

References

  1. 1.

    Evlashin, S. et al. Optical and IR absorption of multilayer carbon nanowalls. Carbon N. Y. 70, 111–118 (2014).

  2. 2.

    Dyakonov, P. et al. Carbon nanowalls as a platform for biological SERS studies. Sci. Rep. 7, 13352 (2017).

  3. 3.

    Mironovich, K. V., Mankelevich, Y. A., Voloshin, D. G., Dagesyan, S. A. & Krivchenko, V. A. Simulation and optical spectroscopy of a DC discharge in a CH4/H2/N2 mixture during deposition of nanostructured carbon films. Plasma Phys. Reports 43, 844–857 (2017).

  4. 4.

    Krivchenko, V. A. et al. Electrochemical activation of carbon nanowalls. Mendeleev Commun. 21, 264–265 (2011).

  5. 5.

    Krivchenko, V. A. et al. Carbon nanowalls decorated with silicon for lithium-ion batteries. Carbon N. Y. 50, 1438–1442 (2012).

  6. 6.

    Mironovich, K. V. et al. Gaining cycling stability of Si- and Ge-based negative Li-ion high areal capacity electrodes by using carbon nanowall scaffolds. J. Mater. Chem. A 5, 18095–18100 (2017).

  7. 7.

    Chul Shin, S. et al. Carbon nanowalls as platinum support for fuel cells. J. Appl. Phys. 110, 104308 (2011).

  8. 8.

    Maksimov, Y. M. et al. Galvanic displacement of silver deposited on carbon nanowalls by palladium and the electrocatalytic behavior of the resulting composite. Mendeleev Commun. 27, 382–384 (2017).

  9. 9.

    Yi, F. et al. Wearable energy sources based on 2D materials. Chem. Soc. Rev. 47, 3152–3188 (2018).

  10. 10.

    Zamarayeva, A. M. et al. Flexible and stretchable power sources for wearable electronics. Sci. Adv. 3, e1602051 (2017).

  11. 11.

    Tomatsu, M. et al. Hydrogen peroxide sensor based on carbon nanowalls grown by plasma-enhanced chemical vapor deposition. Jpn. J. Appl. Phys. 56, 06HF03 (2017).

  12. 12.

    Hassan, S., Suzuki, M., Mori, S. & El-Moneim, A. A. MnO2/carbon nanowalls composite electrode for supercapacitor application. J. Power Sources 249, 21–27 (2014).

  13. 13.

    Dinh, T. M. et al. Hydrous RuO2/carbon nanowalls hierarchical structures for all-solid-state ultrahigh-energy-density micro-supercapacitors. Nano Energy 10, 288–294 (2014).

  14. 14.

    Yen, H. F. et al. Vertically aligned epitaxial graphene nanowalls with dominated nitrogen doping for superior supercapacitors. Carbon N. Y. 82, 124–134 (2015).

  15. 15.

    Lin, T. et al. Nitrogen-doped mesoporous carbon of extraordinary capacitance for electrochemical energy storage. Science (80-.). 350, 1508–1513 (2015).

  16. 16.

    Guo, D. et al. Active sites of nitrogen-doped carbon materials for oxygen reduction reaction clarified using model catalysts. Science (80-.) 351, 361–365 (2016).

  17. 17.

    Zhang, J., Xia, Z. & Dai, L. Carbon-based electrocatalysts for advanced energy conversion and storage. Sci. Adv. 1, e1500564–e1500564 (2015).

  18. 18.

    Chen, P. et al. Hydrothermal synthesis of macroscopic nitrogen-doped graphene hydrogels for ultrafast supercapacitor. Nano Energy 2, 249–256 (2013).

  19. 19.

    Kresse, G. & Furthmüller, J. Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set. Comput. Mater. Sci. 6, 15–50 (1996).

  20. 20.

    Neese, F. The ORCA program system. Wiley Interdiscip. Rev. Comput. Mol. Sci. 2, 73–78 (2012).

  21. 21.

    Rees, J. A., Martin-Diaconescu, V., Kovacs, J. A. & DeBeer, S. X-ray Absorption and Emission Study of Dioxygen Activation by a Small-Molecule Manganese Complex. Inorg. Chem. 54, 6410–6422 (2015).

  22. 22.

    van Dommele, S., Romero-Izquirdo, A., Brydson, R., de Jong, K. P. & Bitter, J. H. Tuning nitrogen functionalities in catalytically grown nitrogen-containing carbon nanotubes. Carbon N. Y. 46, 138–148 (2008).

  23. 23.

    Choo, H.-S. et al. Mechanism for Electrochemical Oxidation of Highly Oriented Pyrolytic Graphite in Sulfuric Acid Solution. J. Electrochem. Soc. 154, B1017 (2007).

  24. 24.

    Volynets, A. V. et al. N2 dissociation and kinetics of N(4S) atoms in nitrogen DC glow discharge. J. Phys. D. Appl. Phys. 51, 364002 (2018).

  25. 25.

    Voronina, E. N. et al. Experimental and DFT study of nitrogen atoms interactions with SiOCH low-κ films. Eur. Phys. J. D 71, 111 (2017).

  26. 26.

    Zhang, S., Tsuzuki, S., Ueno, K., Dokko, K. & Watanabe, M. Upper Limit of Nitrogen Content in Carbon Materials. Angew. Chemie Int. Ed. 54, 1302–1306 (2015).

  27. 27.

    Sun, T. & Fabris, S. Mechanisms for Oxidative Unzipping and Cutting of Graphene. Nano Lett. 12, 17–21 (2012).

  28. 28.

    Voronina, E. N. & Novikov, L. S. Ab initio study of unzipping processes in carbon and boron nitride nanotubes under atomic oxygen impact. RSC Adv. 3, 15362 (2013).

  29. 29.

    Pylypenko, S. et al. Tuning Carbon-Based Fuel Cell Catalyst Support Structures via Nitrogen Functionalization. I. Investigation of Structural and Compositional Modification of Highly Oriented Pyrolytic Graphite Model Catalyst Supports as a Function of Nitrogen Implantation Dose. J. Phys. Chem. C 115, 13667–13675 (2011).

  30. 30.

    Carlsson, J. M., Hanke, F., Linic, S. & Scheffler, M. Two-Step Mechanism for Low-Temperature Oxidation of Vacancies in Graphene. Phys. Rev. Lett. 102, 166104 (2009).

  31. 31.

    Nilsson, A. Applications of core level spectroscopy to adsorbates. J. Electron Spectros. Relat. Phenomena 126, 3–42 (2002).

  32. 32.

    Liu, G., Li, X., Ganesan, P. & Popov, B. N. Studies of oxygen reduction reaction active sites and stability of nitrogen-modified carbon composite catalysts for PEM fuel cells. Electrochim. Acta 55, 2853–2858 (2010).

Download references

Acknowledgements

This work was supported by Russian Foundation for Basic Research 17-08-01414 A. The calculations were performed using the equipment of the shared research facilities of HPC computing resources at Lomonosov Moscow State University.

Author information

S.A.E. fabricated samples and analysed results, N.V.S. and I.S.A. supervised the project, Y.A.M. and E.N.V. made the DFT simulation, K.I.M. measured the XPS spectra, E.V.Z. and A.A.P. made SEM and Raman analysis, S.V.V. and Y.M.M. measured the electrochemistry, A.A.P. and P.V.D. made the syntheses of the samples and their modification.

Correspondence to Stanislav A. Evlashin.

Ethics declarations

Competing Interests

The authors declare no competing interests.

Additional information

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

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/.

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Further reading

Comments

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.