Impact Factor 2.746 | CiteScore 2.5
More on impact ›

Original Research ARTICLE

Front. Energy Res., 12 November 2020 |

NiFeRu Layered Double Hydroxide and Its Derivatives Supported on Graphite Foam as Binder-Free Cathode for Nonaqueous Li-O2 Batteries

www.frontiersin.orgMing Song1*, www.frontiersin.orgHua Tan2, www.frontiersin.orgLin Tian1, www.frontiersin.orgJing Li1, www.frontiersin.orgYan Xu1, www.frontiersin.orgLiluo Shi1, www.frontiersin.orgLimei Sun1, www.frontiersin.orgWenchang Zhuang1 and www.frontiersin.orgXihua Du1
  • 1College of Materials and Chemical Engineering, Xuzhou, China
  • 2School of Physical and Mathematical Sciences, Nanyang Technological University, Singapore, Singapore

Li-O2 batteries (LOBs) generally referred as Li-air batteries (LABs) potentially have a high specific capacity among all kinds of metal-ion batteries. However, it suffers severely from sluggish discharge/charge kinetics. A binder-free integrated cathode is fabricated which contains NiFeRu layered double hydroxide (NiFeRu LDH) nanosheets grown on a 3D conductive graphite foam (NiFeRu LDH@GF) in this work. This integrated 3D cathode exhibits a specific capacity of 3,085 mAh g−1 and a cycle life of 46. The electrochemical performances of NiFeRu LDH derived metal oxides (DMO@GF) by calcining NiFeRu LDH@GF at 350°C, 450°C, and 550°C are also been investigated. The 450°C obtained DMO@GF (450-DMO@GF) exhibits the highest catalytic activity for oxygen reduction/evolution reaction. The unique floccule-like and cross-connected structure of the 450-DMO@GF and its low charge transfer resistance are responsible for the outstanding electrochemical performance.


The modern e-society has put increasing demand for new energy sources that can enable long-lasting power and fast charging and/or release of the energy. Among various available batteries, Li-O2 batteries (LOBs), which are also called Li-air batteries (LABs), have the highest theoretical specific energy of 3,505 Wh kg−1. This specific energy is ∼10 times that of Li-ion batteries (Bruce et al., 2012) and higher than other Li metal batteries (Xue et al., 2019; Sun et al., 2020). Therefore, LOBs have attracted immense interest since 1996 as the “holy grail” of batteries (Abraham and Jiang, 1996). However, the development of LOBs are slow because of their low energy efficiency caused by decomposition of nonaqueous electrolyte and carbon-based cathode (Freunberger et al., 2011; Ottakam Thotiyl et al., 2013), short cycle life caused by nonrecovery of the reaction surface/interface (Lu et al., 2016), and poor power performance led by low kinetics of electron/Li+/O2 transport during the oxygen evolution reaction (OER) and oxygen reduction reaction (ORR) (Liu et al., 2015). These issues are all related to the properties of cathode materials, and achieving cathode with high electrochemical performances is still a big challenge. During the discharging process, O2 should be first reduced at the gas/liquid/solid (O2/Li+/e) three-phase reaction interface of cathode. Then, the reduced O2 will combine with Li+ to form Li2O2. In the charging process, Li2O2 should be decomposed to O2 and Li+, which guarantees reuse of the reaction interface of cathode during the following cycles. In addition to the Li anode and electrolyte, these two discharging/charging processes are dependent on the catalytic activity of cathode for ORR and OER. The slow kinetics of ORR and OER taking place in the cathode will undoubtedly give rise to poor battery performances. Thus, there is consensus that a stable cathode material with high ORR and OER activity is the key player of LOBs.

To realize a stable cathode and a superior Li-O2 battery, numerous research efforts concerning catalyst design and catalytic mechanism have been devoted to the electro-catalytic materials field (Chang et al., 2017). Various cathode materials based on carbon materials (Qin et al., 2019), heteroatom doping carbon material (Jiang et al., 2019), noble metal (Zhang et al., 2019), and metal oxides (Yuan et al., 2019) have been used to the LOBs. The aim is to enhance the performances of LOBs by promoting the reaction kinetics associated with Li2O2 generation/decomposition. In particular, the larger overpotential during the charging process than discharging process reveals more sluggish OER kinetics (Lyu et al., 2017). Layered double hydroxide (LDH) has become the protagonist in different areas including photochemistry (Zhao et al., 2014), adsorption (Gu et al., 2015), drug delivery (Ribeiro et al., 2014), and water electrolysis due to its advantages such as more exposed catalytic active sites than 0D or 1D materials, large surface-to-bulk ratios, and easily controllable layered structure adjustment (Cai et al., 2019). Especially, LDHs have attracted increased attention because of their OER catalytic activity since 2013 (Gong et al., 2013). This implies that LDHs are promising in accelerating the kinetics during the charging process for LOBs. However, there are only limited research so far on LDH cathode of LOBs. Recently, cathodes of nonaqueous LOBs based on CoNiFe LDH and conductive RuO2.1 super-lattice composites have been fabricated by casting these composites with polyvinylidene fluoride (PVDF) binder on stainless steel mesh (Lu et al., 2020). It is worth mentioning that LDHs usually have poor conductivity and insufficient active edge sites. Therefore, binder-free cathodes with LDHs supported on conductive substrate will be more superior.

Herein, in this work, we design and realize an integrated binder-free cathode for LOBs by directly growing LDH on a graphite foam (LDH@GF). NiFe LDH doped by Ru (NiFeRu LDH) is selected since catalysts based on trimetal usually offer higher catalytic activity for OER in comparison with bimetal-centered LDH, and Ru has high adsorption capabilities toward oxygen-containing intermediates (Seh et al., 2017). In addition, their derived metal oxides (DMOs) supported on the GF (DMO@GF), by calcination under different temperatures, are also investigated as cathodes of LOBs since transitional metal oxides (e.g., NiO (Tong et al., 2015)) and spinel oxides (e.g., NiCo2O4 (Sun et al., 2014)) have exhibited catalytic activity in LOBs.

Experiment Section

Preparation of Cathode Materials

The 3D graphite foam (GF) substrate was prepared by using the chemical vapor deposition (CVD) method using the nickel foam as a template according to our previous work (Chao et al., 2014; Song et al., 2020). After etching the nickel template using a solution of 1 M FeCl3 and 0.5 M HCl, a free-standing GF (∼0.5 mg cm−2) was obtained. Then, a piece of GF was immersed into a mixed solution of 98% HNO3 and 70% H2SO4 with a mole ratio of 1:3. After washing with deionized water, this hydrophilic-treated GF was immersed into ethylene glycol for 1 h and then transferred into a teflon autoclave containing a mixed solution of Ni(NO3)2·6H2O/Fe(NO3)2·9H2O/RuCl3/NH4F/urea (mole ratio is 5:4:1:35:35). The hydrothermal reaction was carried out at 120°C for 12 h. Then, the NiFeRu LDH supported on GF (NiFeRu LDH@GF, ∼1.3 mg cm−2) cathode was obtained after cooling naturally and washing with deionized water. The fabrication process for NiFeRu LDH@GF cathode is shown in Figure 1.


FIGURE 1. Schematic illustration for the synthesis of NiFeRu-LDH@GF cathode.

The DMOs supported on the GF (DMO@GF, ∼1.0 mg cm−2) cathode was achieved through heating NiFeRu LDH@GF in a quartz tube furnace under Ar gas at 350°C, 450°C, and 550°C for 4 h.


X-ray diffraction (XRD) was performed on an X-ray diffractometer (Bruker-AXS D8 Advance, CuKα, λ = 1.54186). The morphology and microstructure of the cathode were observed through an transmission electron microscope (JEOL 2100 F HRTEM) and scanning electron microscope (JEOL 7600F FESEM). Raman spectra were measured using a Raman system with a laser wavelength of 532 nm (WITec-CRM200).

LOBs Assembly and Electrochemical Tests

The homemade Swagelok-type cells which were assembled under pure argon gas (<0.5 ppm H2O and O2) in a glovebox were used for the electrochemical measurements. A free-standing NiFeRu LDH@GF cathode or a DMO@GF cathode and a Li anode were separated by a Whatman glass fiber separator. The glass fiber separator was first impregnated with 1 M bis(trifluoromethane)sulfonamide (LiTFSI). Tetraethylene glycol dimethyl ether (TEGDME) was used as the solution. The galvanostatic discharge/charge tests were conducted using a Neware battery tester. Electrochemical impedance spectroscopy (EIS) was carried out using CHI660E. The frequency range is from 1 kHz to 1 Hz, and an AC amplitude of 5 mv was applied.

Results and Discussion

The crystal structure of NiFeRu-LDH was first researched by XRD. As disclosed in Figure 2A, the diffraction peaks at 11.3°, 22.6°, and 33.9° are the characteristic (009), (006), and (003) facets of the NiFeRu-LDH, respectively (Chen et al., 2018). The peaks appear at 26.6°, 44.7°, and 54.7° (red triangle symbol) are assigned to the graphite substrate (JCPDS #89-8487).


FIGURE 2. Characterization of the as-fabricated NiFeRu-LDH@GF cathode. Typical (A) XRD, (B) Raman, (C, D) SEM, (E) TEM spectra, and corresponding elemental mapping images of (F) Ni, (G) Fe, and (H) Ru.

The Raman technique was carried out to further identify composition of the as-prepared cathode. The G band (1,575 cm−1) in the Raman spectrum (Figure 2B) is identified for the graphite (Tuinstra and Koenig, 1970). D band (1,348 cm−1) of graphite is not observed, which indicates that the GF is highly ordered (Ferrari et al., 2004). The broad band located at around 547 cm−1 and the faint broad feature at around 458 cm−1 are in accordance with the observation of NiFe-LDH (Lu et al., 2014). The doping of Ru is responsible for the small shift of Raman peaks for NiFeRu-LDH in comparison with those of NiFe-LDH.

Field emission scanning electron microscopy (FESEM) was utilized to reveal the morphology of NiFeRu-LDH. NiFeRu-LDH grows uniformly on the surface of GF (Figure 2C). Numerous vertically aligned nanosheets with size of 300–600 nm and thickness of 20–40 nm are observed (Figure 2D). This interconnected structure of nanosheet may be helpful in improving the conductivity and providing more active edge sites of NiFeRu-LDH. The transmission electron microscopy (TEM) photograph further uncovers the nanosheet morphology of NiFeRu-LDH (Figure 2E), and the corresponding energy-dispersive X-ray (EDX) elemental mapping discloses the existence of Ru in the nanosheets (Figure 2F–H). This 3D-structured porous binder-free cathode with a large amount of nanosheets can provide a large reaction interface and abundant highly efficient catalytic active sites for discharging products accommodation.

The electrochemical activity of NiFeRu-LDH@GF is revealed by using the galvanostatic discharge/charge method. Home-made Swagelok-type cells are used to characterize the electrochemical performance. The Li metal is used as anode, and the free-standing NiFeRu-LDH@GF without additional current collectors is the cathode. The cathode and anode are separated by a glass fiber containing electrolyte (details are in the Experimental Section). The first galvanostatic discharging and charging curves of LOBs at various current densities are shown in Figure 3A. The specific discharge capacities of LOBs at 200 mA g−1, 300 mA g−1, and 400 mA g−1 are 3,085 mAh g−1, 2,155 mAh g−1, and 1,085 mAh g−1, respectively. This result indicates that the specific capacity is sensitive to the current density, which is because of the limited conductivity of discharging products and O2 transport limitation (Viswanathan et al., 2011; Zhu et al., 2013). The mid-capacity potential (defined as the potential at half of the specific capacity) for the discharging process at 200 mA g−1 is 2.49 V, which is close to 2.46 V at 300 mA g−1 and 2.43 V at 400 mA g−1. This means the catalytic activity of NiFeRu-LDH@GF for ORR is not the controlling step for the discharging process. However, the mid-capacity potential for the charging process increases from 4.20 V at 200 mA g−1 to 4.32 V at 400 mA g−1. The obviously increased overpotential implies that the catalytic activity of NiFeRu-LDH@GF is not sufficient to OER.


FIGURE 3. Galvanostatic discharge/charge profiles of NiFeRu-LDH@GF electrodes (A) at different current densities and (B) different cycles.

To reveal the cycling performance, the NiFeRu-LDH@GF cathode is tested at a current density of 200 mA g−1, and a fixed specific capacity of 500 mAh g−1 is a commonly used parameter in LOBs (Zhou et al., 2017; Zhang et al., 2018). The overpotential gradually increases for the charging process, and the terminal voltage is higher than 4.4 V after 46 cycles (Figure 3B). Meanwhile, the terminal voltage for the discharging process is about 2.15 V. The performance up to 46 cycles is similar to that of CoNiFe-LDH cathode reported recently (Lu et al., 2020). These results reveal LDHs may not have superior electrochemical properties for LOBs.

To improve the electrochemical performances of LOBs, we further investigate the electrochemical activity of NiFeRu-LDH DMOs supported on the GF (DMO@GF) obtained by calcining NiFeRu-LDH@GF at 350°C, 450°C, and 550°C, respectively. XRD and Raman spectra reveal the component of DMO@GF in Figure 4. The peaks of graphite substrate still appear at 26.6°, 44.7°, and 54.7° (red triangle symbol, JCPDS #89-8487), and the peaks of NiFeRu-LDH disappear. The diffraction peaks at 35.7° and 43.4° are the characteristic (311) and (400) facets of the NiFe2O4, respectively, and the (111) and (200) facets of NiO at the peak position of 37.2° and 43.3° are also observed in Figure 4A (Xue et al., 2020). These results prove that NiFeRu-LDH has changed to metal oxides including NiFe2O4 and NiO. In addition, the diffraction peak intensity of DMOs increases. In addition, the full width at half maximum (FWHM) decreases when the calcination temperature increases. This means more metal oxides are formed, and their crystal size is larger at higher calcination temperature. The diffraction peaks of Ru oxides are not detected because of the low Ru atom ratio in NiFeRu-LDH.


FIGURE 4. Characterization of the NiFeRu-LDH–derived metal oxides supported on graphite foam. Typical (A) XRD and (B) Raman spectra.

Raman spectra of DMO@GF further identify the DMOs (Figure 4B). The G band (1,575 cm−1) of graphite in Raman spectrum still exists, which is consistent with the result of XRD (Figure 4A). The Raman peaks at 188 cm−1, 305 cm−1, 468 cm−1, and 549 cm−1 are related to the symmetric and antisymmetric bending of oxygen atom in iron–oxygen bond at FeO6 octahedral voids (Kumar et al., 2020). The band at 673 cm−1 is responsible for the symmetric stretching vibrations of oxygen atoms against Ni ion in NiO4 tetrahedra. The NiO-related Raman bands at 508 cm−1 and 1,014 cm−1 are also observed in Figure 4B (Qiu et al., 2019). Furthermore, the characteristic peaks of RuO2 at 528 cm−1, 646 cm−1, and 716 cm−1 are included in the broad bands between 450 cm−1 and 750 cm−1 (Huang and Pollak, 1982). These results predict a conclusion that NiFeRu-LDH has transformed to metal oxides on GF.

Galvanostatic discharge/charge method was further utilized to investigate the electrochemical performances of DMO@GF cathode by calcining NiFeRu-LDH@GF at 350°C, 450°C and 550°C (denoted as 350-DMO@GF, 450-DMO@GF and 550-DMO@GF). The specific discharge capacities of 350-DMO@GF, 450-DMO@GF and 550-DMO@GF electrodes are 2,718 mAh g−1, 3,700 mAh g−1, and 2,555 mAh g−1, respectively (Figure 5A). Obviously, only the 450-DMO@GF exhibits higher specific discharge capacity than that of NiFeRu-LDH@GF (Figure 3A). Meanwhile, the mid-capacity potential for the discharging process of 450-DMO@GF is 2.55 V which is close to 2.56 V of 350-DMO@GF and 2.50 V of 550-DMO@GF. This means the discharging over-potential of DMO@GF, especially 450-DMO@GF, is smaller than that of NiFeRu-LDH@GF (2.49 V). More importantly, the mid-capacity potential of DMO@GF for the charging process (4.02 V for 350-DMO@GF, 3.97 V for 450-DMO@GF and 4.01 V for 550-DMO@GF) is much lower than that of NiFeRu-LDH@GF (4.20 V). The cycling properties of 450-DMO@GF cathode are further researched since it has highest specific discharging capacity and smallest charging over-potential (Figure 5B). The cycle life of 58 is realized for 450-DMO@GF cathode at a current density of 200 mA g−1 and a fixed specific capacity of 500 mAh g−1. The terminal voltage for charging and discharging process is 4.08 V and 2.25 V. These cycling performances of 450-DMO@GF are better than those of NiFeRu-LDH@GF (Figure 3B). These results imply that the NiFeRu-LDH DMOs have higher catalytic activity for ORR and OER process in comparison with NiFeRu-LDH. It has been reported that metal oxides such as NiCo2O4, NiO and RuO2 have better electrochemical performances than those of layered-double-hydroxides (Chang et al., 2017), which is consistent with our results.


FIGURE 5. (A) Galvanostatic discharge/charge profiles of DMO@GF electrodes and (B) the cycling performance of 450-DMO@GF cathode. The current density is 200 mA g−1.

To reveal the differences of electrochemical performance for NiFeRu-LDH DMOs, the morphology and structure of DMO@GF are analyzed by SEM. At a low temperature of 350°C, the vertically aligned nanosheets of NiFeRu-LDH partially changed to floccule-like products because of the phase transformation from NiFeRu-LDH to DMOs (Figure 6A). Then, all the nanosheets of NiFeRu-LDH change to floccule-like DMOs that are cross-connected after calcining 450°C (Figure 6B). The floccule-like DMOs further grow to thick nanosheets since the crystal grains grow up accompanying the temperature rising, and no floccule-like products are observed at 550°C (Figure 6C). Obviously, the high specific surface combined with the cross-connected structure of the floccule-like DMOs is beneficial to improve the electrocatalytic activity and meanwhile to lower the overpotential. Therefore, the 450-DMO@GF electrode has the best charge–discharge performance among three DMO@GF electrodes.


FIGURE 6. SEM spectra of the (A) 350-DMO@GF, (B) 450-DMO@GF, and (C) 550-DMO@GF.


FIGURE 7. Nyquist plots of DMO@GF and LDH@GF.

EIS is further introduced to research the mechanism of differences in kinetic characteristic among DMO@GF and LDH@GF (Figure 7). The impedance spectra of LOBs are interpreted and proposed by Laoire. The equivalent circuit is Rs (C (RpW), where Rs is the electronic resistance from the cathode, the current collector, and electrolyte resistance, C is the capacitive contribution of the cathode and anode, Rp is the charge transfer resistance of the two electrodes, and W is the linear Warburg element that is attributed to the diffusion of the O2 and Li+ species to the electrode (Laoire et al., 2011). Obviously, the charge transfer resistance Rp of three DMO@GF electrodes is smaller than that of LDH@GF, which implies that DMO@GF electrodes have higher catalytic activity in LOBs. In addition, the charge transfer resistance of the 450-DMO@GF electrode is smallest among the three DMO@GF electrodes, which is responsible for its outstanding electrochemical performance. These results are consistent with the discharge/charge characteristic of DMO@GF and LDH@GF (Figures 3, 5).


In summary, we present an integrated binder-free cathode for LOBs based on Ru-doped NiFe layered double hydroxide grown on a GF (NiFeRu LDH@GF) through hydrothermal reaction. The vertically aligned NiFeRu LDH nanosheets combined with the ultralight and conductive GF substrate provide a specific capacity of 3,085 mAh g−1 at 200 mA g−1 and a cycle life of 46. Furthermore, we also investigate the NiFeRu LDH DMOs supported on a GF (DMO@GF) by calcining NiFeRu LDH@GF at 350°C, 450°C, and 550°C. The 450°C-obtained DMO@GF (450-DMO@GF) shows the best electrochemical performances among the three DMO@GFs. The specific capacity of 450-DMO@GF is 3,700 mAh g−1, and its cycle life is 58. SEM reveals that the floccule-like 450-DMO@GF has a high specific surface combined with a cross-connected structure. EIS further reveals that the charge transfer resistance of the 450-DMO@GF electrode is smallest. Our results provide a new kind of integrated binder-free cathode to achieving LOBs with high performance.

Data Availability Statement

The original contributions presented in the study are included in the article/supplementary materials, further inquiries can be directed to the corresponding author/s.

Author Contributions

All authors extensively discussed the results, reviewed the manuscript, and approved the final version of the manuscript to be published.


This work was financially supported by the National Natural Science Foundation of China (No. 22075115), the Natural Science Foundation of Jiangsu Province (BK20171,169), the Natural Science Foundation of the Jiangsu Higher Education Institutions of China (19KJA430020, 18KJA430015), the Jiangsu Qing Lan Project (2020, 2018) and the innovation and entrepreneurship training program for college students (xcx2020135).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.


Abraham, K., and Jiang, Z. (1996). A polymer electrolyte‐based rechargeable lithium/oxygen battery. J. Electrochem. Soc. 143, 1–5. doi:10.1149/1.1836378

CrossRef Full Text | Google Scholar

Bruce, P. G., Freunberger, S. A., Hardwick, L. J., and Tarascon, J.-M. (2012). Li-O2 and Li-S batteries with high energy storage. Nat. Mater. 11, 19–29. doi:10.1038/nmat3191

CrossRef Full Text | Google Scholar

Cai, Z., Bu, X., Wang, P., Ho, J. C., Yang, J., and Wang, X. (2019). Recent advances in layered double hydroxide electrocatalysts for the oxygen evolution reaction. J. Mater. Chem. A 7, 5069–5089. doi:10.1039/c8ta11273h

CrossRef Full Text | Google Scholar

Chang, Z., Xu, J., and Zhang, X. (2017). Recent progress in electrocatalyst for Li-O2Batteries. Adv. Energy Mater. 7, 1700875. doi:10.1002/aenm.201700875

CrossRef Full Text | Google Scholar

Chao, D., Xia, X., Liu, J., Fan, Z., Ng, C. F., Lin, J., et al. (2014). A V2O5/conductive-polymer core/shell nanobelt array on three-dimensional graphite foam: a high-rate, ultrastable, and freestanding cathode for lithium-ion batteries. Adv. Mater. 26, 5794–5800. doi:10.1002/adma.201400719

CrossRef Full Text | Google Scholar

Chen, G., Wang, T., Zhang, J., Liu, P., Sun, H., Zhuang, X., et al. (2018). Accelerated hydrogen evolution kinetics on NiFe-layered double hydroxide electrocatalysts by tailoring water dissociation active sites. Adv. Mater. 30, 1706279. doi:10.1002/adma.201706279

CrossRef Full Text | Google Scholar

Ferrari, A., Robertson, J., Reich, S., and Thomsen, C. (2004). Raman spectroscopy of graphite. Phil. Trans. Roy. Soc. Lond. 362, 2271–2288. doi:10.1098/rsta.2004.1452

CrossRef Full Text | Google Scholar

Freunberger, S. A., Chen, Y., Peng, Z., Griffin, J. M., Hardwick, L. J., Bardé, F., et al. (2011). Reactions in the rechargeable lithium-O2Battery with alkyl carbonate electrolytes. J. Am. Chem. Soc. 133, 8040–8047. doi:10.1021/ja2021747

CrossRef Full Text | Google Scholar

Gong, M., Li, Y., Wang, H., Liang, Y., Wu, J. Z., Zhou, J., et al. (2013). An advanced Ni-Fe layered double hydroxide electrocatalyst for water oxidation. J. Am. Chem. Soc. 135, 8452–8455. doi:10.1021/ja4027715

CrossRef Full Text | Google Scholar

Gu, Z., Atherton, J. J., and Xu, Z. P. (2015). Hierarchical layered double hydroxide nanocomposites: structure, synthesis and applications. Chem. Commun. 51, 3024–3036. doi:10.1039/c4cc07715f

CrossRef Full Text | Google Scholar

Huang, Y. S., and Pollak, F. H. (1982). Raman investigation of rutile RuO2. Solid State Commun. 43, 921–924. doi:10.1016/0038-1098(82)90930-9

CrossRef Full Text | Google Scholar

Jiang, Z.-L., Sun, H., Shi, W.-K., Cheng, J.-Y., Hu, J.-Y., Guo, H.-L., et al. (2019). P-doped hive-like carbon derived from pinecone biomass as efficient catalyst for Li-O2 battery. ACS Sustain. Chem. Eng. 7, 14161–14169. doi:10.1021/acssuschemeng.9b02790

CrossRef Full Text | Google Scholar

Kumar, A., Singh, A. K., Tomar, M., Gupta, V., Kumar, P., and Singh, K. (2020). Electromagnetic interference shielding performance of lightweight NiFe2O4/rGO nanocomposite in X- band frequency range. Ceram. Int. 46, 15473–15481. doi:10.1016/j.ceramint.2020.03.092

CrossRef Full Text | Google Scholar

Laoire, C. O., Mukerjee, S., Plichta, E. J., Hendrickson, M. A., and Abraham, K. M. (2011). Rechargeable lithium/TEGDME-LiPF[sub 6]∕O[sub 2] battery. J. Electrochem. Soc. 158, A302. doi:10.1149/1.3531981

CrossRef Full Text | Google Scholar

Liu, T., Leskes, M., Yu, W., Moore, A. J., Zhou, L., Bayley, P. M., et al. (2015). Cycling Li-O2 batteries via LiOH formation and decomposition. Science 350, 530–533. doi:10.1126/science.aac7730

CrossRef Full Text | Google Scholar

Lu, J., Jung Lee, Y., Luo, X., Chun Lau, K., Asadi, M., Wang, H.-H., et al. (2016). A lithium-oxygen battery based on lithium superoxide. Nature 529, 377–382. doi:10.1038/nature16484

CrossRef Full Text | Google Scholar

Lu, X., Sakai, N., Tang, D., Li, X., Taniguchi, T., Ma, R., et al. (2020). CoNiFe layered double hydroxide/RuO2.1 nanosheet superlattice as carbon-free electrocatalysts for water splitting and Li-O2 batteries. ACS Appl. Mater. Interfaces 12, 33083–33093. doi:10.1021/acsami.0c07656

CrossRef Full Text | Google Scholar

Lu, Z., Xu, W., Zhu, W., Yang, Q., Lei, X., Liu, J., et al. (2014). Three-dimensional NiFe layered double hydroxide film for high-efficiency oxygen evolution reaction. Chem. Commun. 50, 6479–6482. doi:10.1039/c4cc01625d

CrossRef Full Text | Google Scholar

Lyu, Z., Zhou, Y., Dai, W., Cui, X., Lai, M., Wang, L., et al. (2017). Recent advances in understanding of the mechanism and control of Li2O2formation in aprotic Li-O2batteries. Chem. Soc. Rev. 46, 6046–6072. doi:10.1039/c7cs00255f

CrossRef Full Text | Google Scholar

Ottakam Thotiyl, M. M., Freunberger, S. A., Peng, Z., and Bruce, P. G. (2013). The carbon electrode in nonaqueous Li-O2 cells. J. Am. Chem. Soc. 135, 494–500. doi:10.1021/ja310258x

CrossRef Full Text | Google Scholar

Qin, L., Lv, W., Wei, W., Kang, F., Zhai, D., and Yang, Q.-H. (2019). Oxygen-enriched carbon nanotubes as a bifunctional catalyst promote the oxygen reduction/evolution reactions in Li-O2 batteries. Carbon 141, 561–567. doi:10.1016/j.carbon.2018.10.025

CrossRef Full Text | Google Scholar

Qiu, Z., Ma, Y., and Edvinsson, T. (2019). In operando Raman investigation of Fe doping influence on catalytic NiO intermediates for enhanced overall water splitting. Nanomater. Energy 66, 104118. doi:10.1016/j.nanoen.2019.104118

CrossRef Full Text | Google Scholar

Ribeiro, L. N. M., Alcântara, A. C. S., Darder, M., Aranda, P., Araújo-Moreira, F. M., and Ruiz-Hitzky, E. (2014). Pectin-coated chitosan-LDH bionanocomposite beads as potential systems for colon-targeted drug delivery. Int. J. Pharm. 463, 1–9. doi:10.1016/j.ijpharm.2013.12.035

CrossRef Full Text | Google Scholar

Seh, Z. W., Kibsgaard, J., Dickens, C. F., Chorkendorff, I., Nørskov, J. K., and Jaramillo, T. F. (2017). Combining theory and experiment in electrocatalysis: insights into materials design. Science 355, eead4998. doi:10.1126/science.aad4998

CrossRef Full Text | Google Scholar

Song, M., Tan, H., Li, X., Tok, A. I. Y., Liang, P., Chao, D., et al. (2020). Atomic‐layer‐deposited amorphous MoS 2 for durable and flexible Li-O 2 batteries. Small Methods 4, 1900274. doi:10.1002/smtd.201900274

CrossRef Full Text | Google Scholar

Sun, B., Huang, X., Chen, S., Zhao, Y., Zhang, J., Munroe, P., et al. (2014). Hierarchical macroporous/mesoporous NiCo2O4nanosheets as cathode catalysts for rechargeable Li-O2batteries. J. Mater. Chem. A 2, 12053–12059. doi:10.1039/c4ta01888e

CrossRef Full Text | Google Scholar

Sun, C., Shi, X., Zhang, Y., Liang, J., Qu, J., and Lai, C. (2020). Ti3C2Tx MXene interface layer driving ultra-stable lithium-iodine batteries with both high iodine content and mass loading. ACS Nano 14, 1176–1184. doi:10.1021/acsnano.9b09541

CrossRef Full Text | Google Scholar

Tong, S., Zheng, M., Lu, Y., Lin, Z., Li, J., Zhang, X., et al. (2015). Mesoporous NiO with a single-crystalline structure utilized as a noble metal-free catalyst for non-aqueous Li-O2 batteries. J. Mater. Chem. A 3, 16177–16182. doi:10.1039/c5ta03685b

CrossRef Full Text | Google Scholar

Tuinstra, F., and Koenig, J. L. (1970). Raman spectrum of graphite. J. Chem. Phys. 53, 1126–1130. doi:10.1063/1.1674108

CrossRef Full Text | Google Scholar

Viswanathan, V., Thygesen, K. S., Hummelshøj, J. S., Norskov, J. K., Girishkumar, G., Mccloskey, B. D., et al. (2011). Electrical conductivity in Li2O2 and its role in determining capacity limitations in non-aqueous Li-O2 batteries. J. Chem. Phys. 135, 214704. doi:10.1063/1.3663385

CrossRef Full Text | Google Scholar

Xue, P., Sun, C., Li, H., Liang, J., and Lai, C. (2019). Superlithiophilic amorphous SiO 2 -TiO 2 distributed into porous carbon skeleton enabling uniform lithium deposition for stable lithium metal batteries. Adv. Sci. 6, 1900943. doi:10.1002/advs.201900943

CrossRef Full Text | Google Scholar

Xue, Z., Li, L., Cao, L., Zheng, W., Yang, W., and Yu, X. (2020). A simple method to fabricate NiFe2O4/NiO@Fe2O3 core-shelled nanocubes based on Prussian blue analogues for lithium ion battery. J. Alloys Compd. 825, 153966. doi:10.1016/j.jallcom.2020.153966

CrossRef Full Text | Google Scholar

Yuan, M., Zhang, S., Lin, L., Sun, Z., Yang, H., Li, H., et al. (2019). Manganese carbodiimide nanoparticles modified with N-doping carbon: a bifunctional cathode electrocatalyst for aprotic Li-O2 battery. ACS Sustain. Chem. Eng. 7, 17464–17473. doi:10.1021/acssuschemeng.9b04674

CrossRef Full Text | Google Scholar

Zhang, T., Zou, B., Bi, X., Li, M., Wen, J., Huo, F., et al. (2019). Selective growth of a discontinuous subnanometer Pd film on carbon defects for Li-O2 batteries. ACS Energy Lett. 4, 2782–2786. doi:10.1021/acsenergylett.9b02202

CrossRef Full Text | Google Scholar

Zhang, X., Wang, C., Chen, Y.-N., Wang, X.-G., Xie, Z., and Zhou, Z. (2018). Binder-free NiFe 2 O 4/C nanofibers as air cathodes for Li-O 2 batteries. J. Power Sources 377, 136–141. doi:10.1016/j.jpowsour.2017.12.002

CrossRef Full Text | Google Scholar

Zhao, Y., Li, B., Wang, Q., Gao, W., Wang, C. J., Wei, M., et al. (2014). NiTi-Layered double hydroxides nanosheets as efficient photocatalysts for oxygen evolution from water using visible light. Chem. Sci. 5, 951–958. doi:10.1039/c3sc52546e

CrossRef Full Text | Google Scholar

Zhou, Y., Lyu, Z., Wang, L., Dong, W., Dai, W., Cui, X., et al. (2017). Co3O4 functionalized porous carbon nanotube oxygen-cathodes to promote Li2O2 surface growth for improved cycling stability of Li-O2 batteries. J. Mater. Chem. A 5, 25501–25508. doi:10.1039/c7ta09932k

CrossRef Full Text | Google Scholar

Zhu, D., Zhang, L., Song, M., Wang, X., Mi, R., Liu, H., et al. (2013). Intermittent operation of the aprotic Li-O2 battery: the mass recovery process upon discharge interval. J. Solid State Electrochem. 17, 2539–2544. doi:10.1007/s10008-013-2116-1

CrossRef Full Text | Google Scholar

Keywords: Li-O2 battery, layered double hydroxide, binder-free cathode, graphite foam, derived metal oxide

Citation: Song M, Tan H, Tian L, Li J, Xu Y, Shi L, Sun L, Zhuang W and Du X (2020) NiFeRu Layered Double Hydroxide and Its Derivatives Supported on Graphite Foam as Binder-Free Cathode for Nonaqueous Li-O2 Batteries. Front. Energy Res. 8:612093. doi: 10.3389/fenrg.2020.612093

Received: 30 September 2020; Accepted: 22 October 2020;
Published: 12 November 2020.

Edited by:

Xinghui Wang, Fuzhou University, China

Reviewed by:

Chao Lai, Jiangsu Normal University, China
Yongqi Zhang, University of Electronic Science and Technology of China, China

Copyright © 2020 Song, Tan, Tian, Li, Xu, Shi, Sun, Zhuang and Du. This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.

*Correspondence: Ming Song,