Next Article in Journal
The Derivation of the Stability Bound of the Feedback ANC System That Has an Error in the Estimated Secondary Path Model
Next Article in Special Issue
Investigation of Physical Phenomena and Cutting Efficiency for Laser Cutting on Anode for Li-Ion Batteries
Previous Article in Journal
Gelatin-Enabled Microsensor for Pancreatic Trypsin Sensing
Previous Article in Special Issue
Investigation into the Fire Hazards of Lithium-Ion Batteries under Overcharging
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Applied Sciences
Volume 8
Issue 2
10.3390/app8020209
applsci-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Highly Graphitic Carbon Nanofibers Web as a Cathode Material for Lithium Oxygen Batteries

by
Hyungkyu Han
1,
Yeryung Jeon
2,
Zhiming Liu
2 and
Taeseup Song
2,*
1
Regional Centre of Advanced Technologies and Materials, Department of Physical Chemistry, Faculty of Science, Palacky University, Slechtitelu 11, 783 71 Olomouc, Czech Republic
2
Department of Energy Engineering, Hanyang University, Seoul 133-791, Korea
*
Author to whom correspondence should be addressed.
Appl. Sci. 2018, 8(2), 209; https://doi.org/10.3390/app8020209
Submission received: 20 December 2017 / Revised: 20 January 2018 / Accepted: 25 January 2018 / Published: 31 January 2018
(This article belongs to the Special Issue Advanced Materials for Rechargeable Lithium Batteries)
Browse Figures
Versions Notes

Abstract

:
The lithium oxygen battery is a promising energy storage system due to its high theoretical energy density and ability to use oxygen from air as a “fuel”. Although various carbonaceous materials have been widely used as a cathode material due to their high electronic conductivity and facial processability, previous studies mainly focused on the electrochemical properties associated with the materials (such as graphene and carbon nanotubes) and the electrode configuration. Recent reports demonstrated that the polarization associated with cycling could be significantly increased by lithium carbonates generated from the reaction between the carbon cathode and an electrolyte, which indicates that the physicochemical properties of the carbon cathode could play an important role on the electrochemical performances. However, there is no systematic study to understand these phenomena. Here, we systematically explore the electrochemical properties of carbon nanofibers (CNF) webs with different graphitization degree as a cathode for Li oxygen batteries. The physicochemical properties and electrochemical properties of CNF webs were carefully monitored before and after cycling. CNF webs are prepared at 1000, 1200 and 1400 °C. CNF web pyrolyzed at 1400 °C shows lowered polarization and improved cycle retention compared to those of CNF webs pyrolyzed at 1000 and 1200 °C.

Graphical Abstract

1. Introduction

Development of new energy storage systems with a high energy density beyond Li ion batteries is essential to the critical applications such as large-scale storage for renewable power sources, electric vehicles, and plug-in hybrid electric vehicles [1,2]. Li-O2 batteries have received significant attention as a promising energy storage system due to their higher energy density (~3500 Wh·kg−1) than conventional Li ion batteries and simple concept [3,4]. However, their poor electrochemical properties, caused by the electrolyte instability, a large polarization upon both oxygen reduction reaction (ORR) and oxygen evolution reaction (OER) and pore clogging of cathode by the discharge product (Li2O2), limit their practical use [5,6].
Various materials and structures on the cathode have been intensively explored to overcome these problems [7,8,9,10,11]. Many kinds of carbonaceous materials, including carbon black, single/multi-walled carbon nanotubes, graphene and reduced graphene oxide, have been intensively explored as a cathode material due to their high electronic conductivity and facile processability [12,13,14,15]. The pore size and volume in the carbonaceous materials based cathode were engineered to provide a large tri-phase (solid–liquid–gas) regions for oxygen reduction and prevent the pore clogging associated with Li2O2 discharge product [16]. Recent reports demonstrated that the carbon cathode reacts with Li2O2 and this reaction results in the formation of lithium carbonates film on the surface of carbon cathode, which significantly increases the charge polarization [3,17,18,19,20,21]. To decrease polarization associated with formation/decomposition of Li2O2, various transition metal oxides and novel metals have been explored as a catalyst [5,22,23,24]. Although it is generally accepted that the electrocatalyst could enhance the kinetics associated with formation/decomposition of Li2O2, their catalytic activity should be investigated in the stable electrolyte system to understand their substantive effectiveness and underlying mechanism. Regarding the catalytic effect of carbonaceous materials itself during the cycling, it is certain that carbon materials play an important role in electrochemical performances. Therefore, it is expected that the physicochemical properties and geometry of carbon based cathode could significantly affect upon the electrochemical performances. However, there is no systematic study to understand the effect of physicochemical properties of carbon cathode on the electrochemical performances, which is critical to improve the performances of Li-oxygen batteries.
Here, we systematically study the electrochemical properties of carbon nanofibers (CNF) webs with different graphitization degree as a cathode for Li oxygen batteries. CNF webs are simply prepared using electrospinning method, and its graphitization degree was controlled by adjusting pyrolysis temperature [25,26]. The three dimensional network structure of CNF web enables an efficient electron transport along one dimensional geometry and provides uniform pore structure [27]. The geometrical advantages of CNF webs allow us to investigate the influence of graphitization degree on the electrochemical performances without its degradation caused by the pore clogging associated with Li2O2. The physicochemical properties and electrochemical properties of CNF webs were carefully monitored before and after cycling. The CNF web shows different electrochemical properties as a function of the graphitization degree. The CNF web with high graphitization degree exhibits the low polarization during OER/ORR reactions and improved cycle performance compared to those of the CNF webs with lower graphitization degree. These improvements could be attributed to the enhanced chemical stability came from the high graphitization degree.

2. Experimental Section

2.1. Preparation of Carbon Nanofibers Air Electrode

Carbon nanofibers were synthesized using electrospinning. Polyacrylonitrile (PAN, Mw ≈ 150,000, Sigma Aldrich, St. Louis, MO, USA) was dissolved in DMF to form a 10 wt % solution. The prepared solutions were mixed using a magnetic stirrer at 60 °C for 2 h. Then, the prepared solutions were transferred into a 20 mL syringe with an 18-gauge metal nozzle made of stainless steel. The solution was electrospun at a DC voltage of ~20 kV and a flow rate of 0.5 mL·h−1. The metallic current collector was placed ~10 cm below the tip of the nozzle to collect the nanofibers. The as-spun nanofibers were stabilized at 250 °C for 1 h in air atmosphere to induce dimensional stability of the carbon nanofibers. Then, carbon nanofibers were obtained by the calcination of as-spun nanofibers in argon atmosphere at 1000 °C, 1200 °C, and 1400 °C for 1 h.

2.2. Characterization

Carbon nanofibers electrodes were characterized using a field emission scanning electron microscope (FE-SEM, JEOL JSM-7600F, JEOL, Tokyo, Japan) and X-ray diffraction (XRD, Rigaku D/MAX RINT-2000, Rigaku, Tokyo, Japan).

2.3. Evaluation of Electrochemical Properties

A Swagelok-type Li air cell was assembled using the carbon nanofibers cathode together with a Li anode and glass fibre separator (GF/D, Whatman, Maidstone, UK). 1.0 M LiTFSi in TEGDME was used as the electrolyte. Assembling of the Swagelok-type cells was carried out in an argon glove box. After the sealed cells were removed from the argon glove box, the cathode side was exposed to a pressure balanced chamber filled with 1 atm dry O2 gas (<3 ppm H2O). The Swagelok-type cells were cycled between 2.5 V and 4.5 V using a battery cycle tester (TOSCAT 3000, Toyo Systems, Tokyo, Japan).

3. Results and Discussion

Figure 1 shows electron microscope images of CNFs webs synthesized at 1000 °C (CNF 1000), 1200 °C (CNF 1200) and 1400 °C (CNF 1400). The CNFs have uniform diameter ranging from 350 nm to 450 nm regardless of the pyrolysis temperature. However, their morphologies were significantly influenced by the processing temperature. The CNFs become wavy from straight morphology as increasing pyrolysis temperature. (Figure 1a,e,i) High magnification scanning electron microscope (SEM) images clearly reveal morphological changes in the surface as well as the junction between CNFs. (Figure 1b,f,j) The CNF 1200 and CNF 1400 have smooth surface while the CNF 1000 shows a rough surface, which indicates the rearrangement of carbon atoms by the increase of pyrolysis temperature [28,29]. The morphological change in the junction between CNFs is also significant. Physically touched interface changes to being merged as an increase of pyrolysis temperature. Figure 1j clearly shows fused cross junction for CNF 1400. The microstructure of CNF webs was further characterized using the transmission electron microscopy (TEM). Although the CNF 1000 shows a significant contrast in the brightness at the core and shell (Figure 1c), any noticeable difference in the brightness is not observed for both CNF 1200 and CNF 1400 (Figure 1g,k), which is associated with the rearrangement of carbon atoms at the surface. Figure 1d,h,i show the high resolution (HR) TEM images for CNF webs. An increase in pyrolysis temperature results in a transformation of the amorphous and disordered structure into the high ordered and large graphitic structure. These structural and morphological differences in the CNFs, such as graphitization degree and in junction interface, significantly affect the electrical property. The CNF 1000, 1200 and 1400 exhibit sheet resistances of 15.3, 9.6 and 5.0 ohm/sq (Figure S1).
X-ray diffraction (XRD), Raman spectroscopy and X-ray photoelectron spectroscopy (XPS) were employed to investigate the physicochemical properties of CNF webs. XRD patterns of CNF webs are shown in Figure 2a. The diffraction peak around the 2θ angle of 25°~26° is attributed to the (002) crystallographic plane of graphite crystallite. The intensity and sharpness of this peak gradually increased with the pyrolysis temperature. Figure 2b shows the Raman spectra for CNF webs. Two dominant peaks are observed at the ~1340 cm−1 and ~1580 cm−1, which are assigned to D-band and G-band, respectively. The intensity ratio of D band to G band (ID/IG) of the CNF webs decreases with an increase of the pyrolysis temperature, which clearly implies an enhancement in the graphitization degree. The high-resolution C1s spectra of XPS for CNF webs are shown in Figure 2c. Although all CNF webs have the highest intensities at 284.6 eV, the full width at half maximum (FWHM) for C1s spectra depends on their pyrolysis temperature. The CNF 1000, 1200 and 1400 have the FWHM values of 1.5, 1.4 and 1.2 eV, respectively, which indicates CNF 1400 has the highest graphitization degree among CNF webs. In O1s spectra (Figure 2d), both CNF 1200 and CNF 1400 exhibit more symmetric and narrow spectra towards higher binding energy than those of CNF 1000, which implies a decrease in the relative proportion of C=O and C-OH groups. The CNF 1200 and 1400 do not show any noticeable N1s related peak while the obvious N1s related peak is observed in CNF 1000 (Figure S2). The N1s related peak in CNF 1000 reveals the presence of nitrogen atom from polyacrylonitrile (PAN). The N atoms might be related to the high ID/IG intensity in the Raman result and low electronic conductivity [30,31].
Figure 3 shows the voltage profiles and cycle performances for CNF 1000, CNF 1200 and CNF 1400 electrodes. The electrochemical properties were evaluated with a limited capacity of 1000 mAh/g at a current density of 50 mA/gc using 1 M LiPF6/tetra(ethylene glycol)dimethyl ether (TEGDME) as an electrolyte. As shown in Figure 3a, the CNF electrodes show the different shape in the voltage profiles depending on the pyrolysis temperature. The CNF 1000 electrode has the discharge plateau at the voltage of ~2.63 V and the charge plateau at the voltage of ~4.19 V at 1st cycle, respectively, resulting in a large polarization of ~1.56 V. It is observed that the steep potential drop during the ORR and the significant increase in the OER potential after the first cycle. Although the CNF 1200 electrode shows the consistent voltage profile during the cycling, it exhibits also large polarization. On the other hand, the CNF 1400 electrode has small polarization of ~1.16 V with OER potential under 4 V, which leads to the improvement in cycle performance. The CNF electrodes exhibit markedly different cycle performances. (Figure 3d–f) The CNF 1000 electrode works only for 5 cycles. Even though the CNF 1200 electrode exhibits slightly enhanced cycle performance compared to that of the CNF 1000 electrode, it also shows fast degradation after 9 cycles. On the other hand, the CNF 1400 electrode exhibits the stable cyclability for 50 cycles. The enhanced cyclability of the CNF 1400 electrode is attributed to the high graphitization degree, confirmed by the TEM in Figure 1, and reduced defects on the surface. In Table 1, the Li-O2 batteries performances of various carbon electrodes are summarized. The charge and discharge voltage (V) difference of CNF webs pyrolyzed at 1000, 1200, and 1400 °C are lower than the other carbon electrodes [7,13,32,33,34,35,36,37,38,39].
The morphological changes of the CNF webs were carefully monitored after the discharging and charging within a limited capacity of 1000 mAh/g. As shown in Figure 4a,b,e,f,i,j, the discharging products were homogeneously formed on the surfaces of all CNF electrodes without any blocking and clogging. In the case of the CNF 1000 electrode, the diameter of discharging product is several tens of nanometer. However, it is observed that CNF 1200 and CNF 1400 electrodes have bigger discharging products (200–400 nm diameters) with a bead-like shape than that of CNF 1000 electrode. These results suggest that the formation mechanism of lithium peroxide could be greatly affected by the graphitization degree and surface defect of carbon cathode. After charging, the noticeable discharging product was not observed in all CNF electrodes, which indicates that discharge products Li2O2 were totally decomposed.
The morphological change of CNF electrodes after the fully discharging (cut-off voltage: 2.3 V) was further investigated (Figure S3). The toroidal shaped lithium peroxides formed on the surface of CNF electrodes without clogging even after full discharge, as shown in Figure S3. Interestingly, the CNF electrodes show the different Li2O2 morphology as a function of the pyrolysis temperature. The CNF 1000 electrode with low graphitization degree and many defects shows film like Li2O2 formation with small beads of ~200 nm. In contrast, CNF 1200 and 1400 electrodes with higher graphitization and lower defect amount compared to CNF 1000 favor large toroidal Li2O2 with 500 nm and 1 μm, respectively. These results imply that the graphitization degree and functional groups on the surface play important roles for the formation shape of Li2O2. Previous reports represented that the current density effects on the morphology evolution of the discharge product [21,40,41,42]. Our results suggest further study is required to understand the dominant factors governing the shape of discharge product, which is critical to improve the electrochemical properties of Li-O2 batteries including the rate capability, polarization and round-trip efficiency.
Figure 5 shows X-ray diffraction (XRD) of the CNF electrodes after discharging and the Raman results of the CNF electrode after 1 cycle. The XRD results of CNF electrodes in Figure 5a reveal the formation of lithium peroxide (Li2O2) without Li2O and LiOH [7,43]. The Li2Co3 of byproducts peak observed from XRD pattern [44,45]. In the Raman spectra (Figure 5b), the intensity ratios of the D-band to the G-band for CNF electrodes after 1 cycle increase significantly compared to those of pristine CNF electrodes. The ID/IG of CNF 1000 electrode after 1 cycle is 1.6, which is 64.9% and 55.3% higher than those of CNF 1200 (ID/IG ~ 1.03) and 1400 (ID/IG ~ 0.97) electrodes after 1 cycle. The intensity ratio of ID/IG of the CNF webs after 1 cycle show similar trend to those of the pristine CNF webs. And notably, the values of ID/IG of the CNF webs after 1 cycle are increased compared those of pristine CNF webs, which results from increasing defectivity after the electrochemical cycling [46].

4. Conclusions

We have explored the graphitization effect of the carbon based electrode on the performances of Li-O2 batteries through the systematic approach using CNFs prepared by different pyrolysis temperature. The CNFs electrode with high graphitization degree and low surface defects shows lower polarization and improved cyclability compared to those of CNFs electrode with low graphitization degree and high surface defect. Electrochemical properties and analysis results imply that the graphitization degree and surface defect of carbon based air electrode play an important role on the electrochemical properties. We plan to synthesize the highly graphitic carbon nanofibers with metal oxide catalyst, including Co3O4, MnO2, NiO, RuO2, etc., as a cathode electrode for Li-O2 batteries and evaluate their electrochemical properties in future research. Further study on the relationship between physicochemical properties of carbon electrode and its electrochemical properties should be carried out to understand the fundamental insight.

Supplementary Materials

The following are available online at https://www.mdpi.com/2076-3417/8/2/209/s1, Table S1: Some typical achievements for lithium oxygen cells in cathode materials, electrolytes, difference of charge and discharge voltage, and current density, Figure S1: Sheet resistance of CNF 1000, CNF 1200 and CNF 1400, Figure S2: XPS analysis N1s of CNF 1000, 1200 and 1400, Figure S3. Voltage profile and SEM images of (a, b and c) CNF 1000, (d, e and f) CNF 1200 and (g, h and i) CNF 1400 after fully discharging.

Acknowledgments

This work was supported by the Korea Institute of Energy Technology Evaluation and Planning (KETEP) and the Ministry of Trade, Industry & Energy (MOTIE) of the Korea (20174010201240) and by Basic Science Research Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Science, ICT (2016R1C1B2007299).

Author Contributions

H.H. and T.S. designed and performed experiments, analyzed data and wrote the paper; Y.J. and Z.L. designed and performed experiments.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Lu, Y.C.; Gallant, B.M.; Kwabi, D.G.; Harding, J.R.; Mitchell, R.R.; Whittingham, M.S.; Shao-Horn, Y. Lithium-oxygen batteries: Bridging mechanistic understanding and battery performance. Energy Environ. Sci. 2013, 6, 750–768. [Google Scholar] [CrossRef]
  2. Li, F.J.; Zhang, T.; Zhou, H.S. Challenges of non-aqueous Li-O2 batteries: Electrolytes, catalysts, and anodes. Energy Environ. Sci. 2013, 6, 1125–1141. [Google Scholar] [CrossRef]
  3. Jung, H.G.; Kim, H.S.; Park, J.B.; Oh, I.H.; Hassoun, J.; Yoon, C.S.; Scrosati, B.; Sun, Y.K. A Transmission Electron Microscopy Study of the Electrochemical Process of Lithium-Oxygen Cells. Nano Lett. 2012, 12, 4333–4335. [Google Scholar] [CrossRef] [PubMed]
  4. Lim, H.K.; Lim, H.D.; Park, K.Y.; Seo, D.H.; Gwon, H.; Hong, J.; Goddard, W.A.; Kim, H.; Kang, K. Toward a Lithium-“Air” Battery: The Effect of CO2 on the Chemistry of a Lithium-Oxygen Cell. J. Am. Chem. Soc. 2013, 135, 9733–9742. [Google Scholar] [CrossRef] [PubMed]
  5. Black, R.; Lee, J.H.; Adams, B.; Mims, C.A.; Nazar, L.F. The Role of Catalysts and Peroxide Oxidation in Lithium-Oxygen Batteries. Angew. Chem.-Int. Ed. 2013, 52, 392–396. [Google Scholar] [CrossRef] [PubMed]
  6. Armand, M.; Tarascon, J.M. Building better batteries. Nature 2008, 451, 652–657. [Google Scholar] [CrossRef] [PubMed]
  7. Mitchell, R.R.; Gallant, B.M.; Thompson, C.V.; Shao-Horn, Y. All-carbon-nanofiber electrodes for high-energy rechargeable Li-O2 batteries. Energy Environ. Sci. 2011, 4, 2952–2958. [Google Scholar] [CrossRef]
  8. Xiao, J.; Mei, D.H.; Li, X.L.; Xu, W.; Wang, D.Y.; Graff, G.L.; Bennett, W.D.; Nie, Z.M.; Saraf, L.V.; Aksay, I.A.; et al. Hierarchically Porous Graphene as a Lithium-Air Battery Electrode. Nano Lett. 2011, 11, 5071–5078. [Google Scholar] [CrossRef] [PubMed]
  9. Itkis, D.M.; Semenenko, D.A.; Kataev, E.Y.; Belova, A.I.; Neudachina, V.S.; Sirotina, A.P.; Havecker, M.; Teschner, D.; Knop-Gericke, A.; Dudin, P.; et al. Reactivity of Carbon in Lithium-Oxygen Battery Positive Electrodes. Nano Lett. 2013, 13, 4697–4701. [Google Scholar] [CrossRef] [PubMed]
  10. Oh, S.H.; Black, R.; Pomerantseva, E.; Lee, J.H.; Nazar, L.F. Synthesis of a metallic mesoporous pyrochlore as a catalyst for lithium-O2 batteries. Nat. Chem. 2012, 4, 1004–1010. [Google Scholar] [CrossRef] [PubMed]
  11. Black, R.; Adams, B.; Nazar, L.F. Non-Aqueous and Hybrid Li-O2 Batteries. Adv. Energy Mater. 2012, 2, 801–815. [Google Scholar] [CrossRef]
  12. Lee, J.H.; Black, R.; Popov, G.; Pomerantseva, E.; Nan, F.H.; Botton, G.A.; Nazar, L.F. The role of vacancies and defects in Na0.44MnO2 nanowire catalysts for lithium-oxygen batteries. Energy Environ. Sci. 2012, 5, 9558–9565. [Google Scholar] [CrossRef]
  13. Sun, B.; Wang, B.; Su, D.W.; Xiao, L.D.; Ahn, H.; Wang, G.X. Graphene nanosheets as cathode catalysts for lithium-air batteries with an enhanced electrochemical performance. Carbon 2012, 50, 727–733. [Google Scholar] [CrossRef]
  14. Laoire, C.O.; Mukerjee, S.; Abraham, K.M.; Plichta, E.J.; Hendrickson, M.A. Influence of Nonaqueous Solvents on the Electrochemistry of Oxygen in the Rechargeable Lithium-Air Battery. J. Phys. Chem. C 2010, 114, 9178–9186. [Google Scholar] [CrossRef]
  15. Zhu, X.J.; Zhu, Y.W.; Murali, S.; Stollers, M.D.; Ruoff, R.S. Nanostructured Reduced Graphene Oxide/Fe2O3 Composite as a High-Performance Anode Material for Lithium Ion Batteries. ACS Nano 2011, 5, 3333–3338. [Google Scholar] [CrossRef] [PubMed]
  16. Xu, W.; Xiao, J.; Zhang, J.; Wang, D.Y.; Zhang, J.G. Optimization of Nonaqueous Electrolytes for Primary Lithium/Air Batteries Operated in Ambient Environment. J. Electrochem. Soc. 2009, 156, A773–A779. [Google Scholar] [CrossRef]
  17. Girishkumar, G.; McCloskey, B.; Luntz, A.C.; Swanson, S.; Wilcke, W. Lithium-Air Battery: Promise and Challenges. J. Phys. Chem. Lett. 2010, 1, 2193–2203. [Google Scholar] [CrossRef]
  18. Duke, A.S.; Galhenage, R.P.; Tenney, S.A.; Ammal, S.C.; Heyden, A.; Sutter, P.; Chen, D.A. In Situ Ambient Pressure X-ray Photoelectron Spectroscopy Studies of Methanol Oxidation on Pt(111) and Pt-Re Alloys. J. Phys. Chem. C 2015, 119, 23082–23093. [Google Scholar] [CrossRef]
  19. Padbury, R.; Zhang, X.W. Lithium-oxygen batteries-Limiting factors that affect performance. J. Power Sources 2011, 196, 4436–4444. [Google Scholar] [CrossRef]
  20. Armstrong, A.R.; Holzapfel, M.; Novak, P.; Johnson, C.S.; Kang, S.H.; Thackeray, M.M.; Bruce, P.G. Demonstrating oxygen loss and associated structural reorganization in the lithium battery cathode Li[Ni0.2Li0.2Mn0.6]O2. J. Am. Chem. Soc. 2006, 128, 8694–8698. [Google Scholar] [CrossRef] [PubMed]
  21. Xu, J.J.; Wang, Z.L.; Xu, D.; Zhang, L.L.; Zhang, X.B. Tailoring deposition and morphology of discharge products towards high-rate and long-life lithium-oxygen batteries. Nat. Commun. 2013, 4, 2438. [Google Scholar] [CrossRef] [PubMed]
  22. Sun, B.; Munroe, P.; Wang, G.X. Ruthenium nanocrystals as cathode catalysts for lithium-oxygen batteries with a superior performance. Sci. Rep. 2013, 3, 2247. [Google Scholar] [CrossRef] [PubMed]
  23. Xu, J.J.; Xu, D.; Wang, Z.L.; Wang, H.G.; Zhang, L.L.; Zhang, X.B. Synthesis of Perovskite-Based Porous La0.75Sr0.25MnO3 Nanotubes as a Highly Efficient Electrocatalyst for Rechargeable LithiumOxygen Batteries. Angew. Chem.-Int. Ed. 2013, 52, 3887–3890. [Google Scholar] [CrossRef] [PubMed]
  24. Lu, Y.C.; Xu, Z.C.; Gasteiger, H.A.; Chen, S.; Hamad-Schifferli, K.; Shao-Horn, Y. Platinum-Gold Nanoparticles: A Highly Active Bifunctional Electrocatalyst for Rechargeable Lithium-Air Batteries. J. Am. Chem. Soc. 2010, 132, 12170–12171. [Google Scholar] [CrossRef] [PubMed]
  25. Wu, Y.; Reddy, M.; Chowdari, B. Ramakrishna, Long-Term Cycling Studies on Electrospun Carbon Nanofibers as Anode Material for Lithium Ion Batteries. ACS Appl. Mater. Interfaces 2013, 5, 12175–12184. [Google Scholar] [CrossRef] [PubMed]
  26. Wu, Y.; Zhu, P.; Reddy, M.; Chowdari, B.; Ramakrishna, S. Maghemite Nanoparticles on Electrospun CNFs Template as Prospective Lithium-Ion Battery Anode. ACS Appl. Mater. Interfaces 2014, 6, 1951. [Google Scholar] [CrossRef] [PubMed]
  27. Pan, H.J.; Yang, J.M.; Wang, S.P.; Xiong, Z.B.; Cai, W.S.; Liu, J.Y. Facile fabrication of porous carbon nanofibers by electrospun PAN/dimethyl sulfone for capacitive deionization. J. Mater. Chem. A 2015, 3, 13827–13834. [Google Scholar]
  28. Yi, B.; Rajagopalan, R.; Burket, C.L.; Foley, H.C.; Liu, X.M.; Eklund, P.C. High temperature rearrangement of disordered nanoporous carbon at the interface with single wall carbon nanotubes. Carbon 2009, 47, 2303–2309. [Google Scholar]
  29. Qi, X.; Ruan, X.F.; Pan, C.X. Graphitization of solid carbon nanofibers at an unexpectedly low temperature. Mater. Lett. 2007, 61, 4272–4275. [Google Scholar] [CrossRef]
  30. Khai, T.V.; Na, H.G.; Kwak, D.S.; Kwon, Y.J.; Ham, H.; Shim, K.B.; Kim, H.W. Significant enhancement of blue emission and electrical conductivity of N-doped graphene. J. Mater. Chem. 2012, 22, 17992–18003. [Google Scholar] [CrossRef]
  31. Lin, Z.Y.; Waller, G.H.; Liu, Y.; Liu, M.L.; Wong, C.P. Simple preparation of nanoporous few-layer nitrogen-doped graphene for use as an efficient electrocatalyst for oxygen reduction and oxygen evolution reactions. Carbon 2013, 53, 130–136. [Google Scholar] [CrossRef]
  32. Ogasawara, T.; Debart, A.; Holzapfel, M.; Novak, P.; Bruce, P.G. Rechargeable Li2O2 electrode for lithium batteries. J. Am. Chem. Soc. 2006, 128, 1390–1393. [Google Scholar] [CrossRef] [PubMed]
  33. Abraham, K.M.; Jiang, Z. A polymer electrolyte-based rechargeable lithium/oxygen battery. J. Electrochem. Soc. 1996, 143, 1–5. [Google Scholar] [CrossRef]
  34. Mizuno, F.; Nakanishi, S.; Kotani, Y.; Yokoishi, S.; Iba, H. Rechargeable Li-Air Batteries with Carbonate-Based Liquid Electrolytes. Electrochemistry 2010, 78, 403–405. [Google Scholar] [CrossRef]
  35. Laoire, C.O.; Mukerjee, S.; Plichta, E.J.; Hendrickson, M.A.; Abraham, K.M. Rechargeable Lithium/TEGDME-LiPF6/O2 Battery. J. Electrochem. Soc. 2011, 158, A302–A308. [Google Scholar] [CrossRef]
  36. Carboni, M.; Brutti, S.; Marrani, A.G. Surface Reactivity of a Carbonaceous Cathode in a Lithium Triflate/Ether Electrolyte-Based Li-O2 Cell. ACS Appl. Mater. Interfaces 2015, 7, 21751–21762. [Google Scholar] [CrossRef] [PubMed]
  37. Jung, H.G.; Hassoun, J.; Park, J.B.; Sun, Y.K.; Scrosati, B. An improved high-performance lithium-air battery. Nat. Chem. 2012, 4, 579–585. [Google Scholar] [CrossRef] [PubMed]
  38. Lim, H.D.; Song, H.; Kim, J.; Gwon, H.; Bae, Y.; Park, K.Y.; Hong, J.; Kim, H.; Kim, T.; Kim, Y.H.; et al. Superior Rechargeability and Efficiency of Lithium-Oxygen Batteries: Hierarchical Air Electrode Architecture Combined with a Soluble Catalyst. Angew. Chem.-Int. Ed. 2014, 53, 3926–3931. [Google Scholar] [CrossRef] [PubMed]
  39. Sun, B.; Huang, X.D.; Chen, S.Q.; Munroe, P.; Wang, G.X. Porous Graphene Nanoarchitectures: An Efficient Catalyst for Low Charge-Overpotential, Long Life, and High Capacity Lithium-Oxygen Batteries. Nano Lett. 2014, 14, 3145–3152. [Google Scholar] [CrossRef] [PubMed]
  40. Adams, B.D.; Radtke, C.; Black, R.; Trudeau, M.L.; Zaghib, K.; Nazar, L.F. Current density dependence of peroxide formation in the Li-O2 battery and its effect on charge. Energy Environ. Sci. 2013, 6, 1772–1778. [Google Scholar] [CrossRef]
  41. Tan, P.; Shi, L.; Shyy, W.; Zhao, T.S. Morphology of the Discharge Product in Non-aqueous Lithium-Oxygen Batteries: Furrowed Toroid Particles Correspond to a Lower Charge Voltage. Energy Technol. 2016, 4, 393–400. [Google Scholar] [CrossRef]
  42. Griffith, L.D.; Sleightholme, A.E.S.; Mansfield, J.F.; Siegel, D.J.; Monroe, C.W. Correlating Li/O2 Cell Capacity and Product Morphology with Discharge Current. ACS Appl. Mater. Interfaces 2015, 7, 7670–7678. [Google Scholar] [CrossRef] [PubMed]
  43. Hu, Y.X.; Han, X.P.; Cheng, F.Y.; Zhao, Q.; Hu, Z.; Chen, J. Size effect of lithium peroxide on charging performance of Li-O2 batteries. Nanoscale 2014, 6, 177–180. [Google Scholar] [PubMed]
  44. Zhou, J.; Sui, Z.; Zhu, J.; Li, P.; Chen, D.; Dai, Y.; Yuan, W. Characterization of surface oxygen complexes on carbon nanofibers by TPD, XPS and FT-IR. Carbon 2007, 45, 785. [Google Scholar]
  45. Song, S.; Xu, W.; Zheng, J.; Luo, L.; Engelhard, M.; Bowden, M.; Liu, B.; Wang, C.; Zhang, J. Complete Decomposition of Li2CO3 in Li-O2 Batteries Using Ir/B4C as Noncarbon-Based Oxygen Electrode. Nano Lett. 2017, 17, 1417. [Google Scholar] [PubMed]
  46. Jaber-Ansari, L.; Puntambekar, K.P.; Tavassol, H.; Yildirim, H.; Kinaci, A.; Kumar, R.; Saldana, S.J.; Gewirth, A.A.; Greeley, J.P.; Chan, M.K.Y.; et al. Defect Evolution in Graphene upon Electrochemical Lithiation. ACS Appl. Mater. Interfaces 2014, 6, 17626–17636. [Google Scholar] [CrossRef] [PubMed]
Applsci 08 00209 g001 550
Figure 1. Electron microscope images of carbon nanofibers (CNF) 1000, CNF 1200 and CNF 1400. (a,b) SEM and TEM images of (a–d) CNF 1000, (e–h) CNF 1200, and (i–l) CNF 1400.
Figure 1. Electron microscope images of carbon nanofibers (CNF) 1000, CNF 1200 and CNF 1400. (a,b) SEM and TEM images of (a–d) CNF 1000, (e–h) CNF 1200, and (i–l) CNF 1400.
Applsci 08 00209 g001
Applsci 08 00209 g002 550
Figure 2. Analysis of CNF 1000, 1200 and 1400 of (a) XRD patterns, (b) Raman results, XPS analysis (c) C1s and (d) O1s.
Figure 2. Analysis of CNF 1000, 1200 and 1400 of (a) XRD patterns, (b) Raman results, XPS analysis (c) C1s and (d) O1s.
Applsci 08 00209 g002
Applsci 08 00209 g003 550
Figure 3. Electrochmical properties of CNF electrodes. Voltage profiles of (a) CNF 1000, (b) CNF 1200 and (c) CNF 1400. Cycle performances of (d) CNF 1000, (e) CNF 1200, and (f) CNF 1400.
Figure 3. Electrochmical properties of CNF electrodes. Voltage profiles of (a) CNF 1000, (b) CNF 1200 and (c) CNF 1400. Cycle performances of (d) CNF 1000, (e) CNF 1200, and (f) CNF 1400.
Applsci 08 00209 g003
Applsci 08 00209 g004 550
Figure 4. Electron microscope images of (a–d) CNF 1000, (e–h) CNF 1200 and (i–l) CNF 1400 after the discharging and charging.
Figure 4. Electron microscope images of (a–d) CNF 1000, (e–h) CNF 1200 and (i–l) CNF 1400 after the discharging and charging.
Applsci 08 00209 g004
Applsci 08 00209 g005 550
Figure 5. Analysis of CNF 1000, 1200 and 1400 after the discharging (a) XRD patterns (b) Raman results.
Figure 5. Analysis of CNF 1000, 1200 and 1400 after the discharging (a) XRD patterns (b) Raman results.
Applsci 08 00209 g005
Table
Table 1. Some typical achievements for lithium oxygen cells in cathode materials, electrolytes, difference of charge and discharge voltage, and current density.
Table 1. Some typical achievements for lithium oxygen cells in cathode materials, electrolytes, difference of charge and discharge voltage, and current density.
Carbon Materials (for Oxygen Electrode)ElectrolyteDifferences of Change and Discharge Viltage (V)Curremt DesityCapacity (mAhg-c−1)Ref.
Super P carbon + α-MnO2LiPF6-PC1.370 mAhg-c−11000[32]
Chevlon carbon + Co-phthalocyanineLiPF6-PC-EC-PAN0.920.1 mAcm−2 (discharge)0.05 mAcm−2 (charge)520[33]
Super P carbon + MnO2LiTFSi-PC1.80.02 mAhg-c−1800[34]
BP2000 carbon + MnO2LiPF6-TEGDME1.40.13 mAhg-c−1800[35]
Super P carbonLiPF6-TEGDME1.870 mAhg-c−13000[36]
Carbon on carbon paperLiCF2SO2-TEGEME1.7500 mAhg-c−13000[37]
CNT fibrilTEGEME1.62000 mAhg-c−11000[38]
All carbon-nanofiberLiPF6-EC:DMC~1.5543 mAhg-c−1−5000[7]
Graphene nanosheetsLiClO4-PC1.220.1 mAhg-c−12332[13]
Porous graphene nanoarchitecturesDMSO1.579200 mAhg-c−129,375[39]
CHF 1000 (this work)LiTFSi-TEGEME1.5850 mAhg-c−11000
CHF 1000 (this work)LiTFSi-TEGEME1.4250 mAhg-c−11000
CHF 1000 (this work)LiTFSi-TEGEME1.1650 mAhg-c−11000

Share and Cite

MDPI and ACS Style

Han, H.; Jeon, Y.; Liu, Z.; Song, T. Highly Graphitic Carbon Nanofibers Web as a Cathode Material for Lithium Oxygen Batteries. Appl. Sci. 2018, 8, 209. https://doi.org/10.3390/app8020209

AMA Style

Han H, Jeon Y, Liu Z, Song T. Highly Graphitic Carbon Nanofibers Web as a Cathode Material for Lithium Oxygen Batteries. Applied Sciences. 2018; 8(2):209. https://doi.org/10.3390/app8020209

Chicago/Turabian Style

Han, Hyungkyu, Yeryung Jeon, Zhiming Liu, and Taeseup Song. 2018. "Highly Graphitic Carbon Nanofibers Web as a Cathode Material for Lithium Oxygen Batteries" Applied Sciences 8, no. 2: 209. https://doi.org/10.3390/app8020209

APA Style

Han, H., Jeon, Y., Liu, Z., & Song, T. (2018). Highly Graphitic Carbon Nanofibers Web as a Cathode Material for Lithium Oxygen Batteries. Applied Sciences, 8(2), 209. https://doi.org/10.3390/app8020209

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop