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Article

Enhanced Cycle Performance of NiCo2O4/CNTs Composites in Lithium-Air Batteries

by
Dae-Seon Hong
1,2,
Yeon-Ji Choi
1,3,
Chang-Su Jin
1,
Kyoung-Hee Shin
1,
Woo-Jin Song
2 and
Sun-Hwa Yeon
1,*
1
Department of Energy Storage Researh, Korea Institute of Energy Research, Daejeon 34101, Republic of Korea
2
Department of Organic Materials Engineering, Chungnam National University, Daejeon 35015, Republic of Korea
3
Department of Energy Engineering, HanYang University, Seoul 04763, Republic of Korea
*
Author to whom correspondence should be addressed.
Energies 2024, 17(1), 58; https://doi.org/10.3390/en17010058
Submission received: 15 November 2023 / Revised: 7 December 2023 / Accepted: 19 December 2023 / Published: 21 December 2023
(This article belongs to the Special Issue Selected Papers from the 12th Asia-Pacific Forum on Renewable Energy (AFORE 2023))
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Abstract

:
The lithium-air battery is a new type of secondary battery technology that is currently receiving a lot of attention in the field of power storage technology. These batteries are known to offer high energy densities and potentially longer driving ranges. In this study, NiCo2O4 and CNTs were used to create a composite for use as the cathode of a Li-air battery. Improving the 3D needl-like structure that provides extensive transport channels for electrolyte infiltration and numerous sites facilitated charge transfer reactions and the synergistic effect of highly electrocatalytic NiCo2O4 with pronounced activity and high conductive CNTs, with the synthesized NiCo2O4@CNTs composites exhibiting active catalytic performance for both OER and ORR reactions. It also showed improved cycle performance at high current densities. NiCo2O4@CNTs composites were successfully fabricated using a hydrothermal method together with a sequential annealing treatment. The components of the completed composite were confirmed using TGA, XRD, and SEM, and the specific surface area was analyzed using BET. The composite was performed for over 120 cycles at a current density of 200 mA∙g−1, and 500 mA∙g−1 was achieved under the capacity limiting condition of 500 mAh∙g−1. The charging/discharging characteristics were compared under various current densities, exhibiting stable cyclability. The high catalytic activity of NiCo2O4 oxide supports its potential use as a cathode in Li-air batteries.

1. Introduction

Fossil fuels still account for over 80% of the worldwide energy requirements and have a significant daily impact on global warming and environmental pollution [1,2]. Therefore, the further development of renewable energy options is considered an important step in the effort to address the issue of fossil fuel consumption. In particular, lithium-ion batteries (LIBs), first commercialized by Sony in the 1990s, have been widely used in various applications such as smartphones, laptops, and electric vehicles (EVs) in our daily lives [3]. In lithium-ion batteries (LIBs), through the process of ‘intercalation chemistry’, lithium ions move from an anode to a cathode during the discharge process, passing through the electrolyte and releasing electricity. However, current lithium-ion battery technologies still face various challenges such as high costs associated with limited lithium resources, safety concerns, and unsatisfactory energy densities [4]. Notably, the limited energy storage capacity of lithium-ion batteries (LIBs) serves as a limiting factor in extending the driving range of current electric vehicles (EVs) [5]. Therefore, the next step to enhance the electrical performance of the battery lies in the development of next-generation battery technologies such as lithium-sulfur as well as metal-air batteries, including Li-air and Na-O2 batteries [6]. Lithium-air batteries are considered one of the most promising candidates to replace LIBs due to their low weight, safety, and remarkably high theoretical energy density (approximately 3500 to 5200 Wh∙kg−1), which is comparable to gasoline [7,8,9,10,11]. If its complete theoretical specific energy were to be fully extracted, the lithium-air battery would be the best substitute for fossil fuels in electric vehicles with plug-in capabilities, as it has the potential to offer up to 10 times the energy density of any other battery. In reality, the system yields a much lower specific energy than the theoretical value due to various shortcomings such as high overvoltage, slow kinetics of the oxygen evolution reaction (OER) and oxygen reduction reaction (ORR), the formation of insoluble discharge products in aprotic electrolytes, and difficulties in charge transfer between the solid discharge product and solid cathode. Therefore, researchers from various backgrounds have explored different aspects of the lithium-air system, all with the unified goal of commercializing rechargeable aprotic lithium-air batteries. The lithium-air battery idea was first introduced in 1976 using an aqueous electrolyte, but it failed due to the corrosion of lithium. In 1990, Abraham and Jiang achieved success in assembling a rechargeable lithium-air battery with excellent Coulombic efficiency and minimal overvoltage by using a non-aqueous electrolyte and an air electrode catalyzed by cobalt phthalocyanine [12]. Subsequently, investigations into the advancement of rechargeable aprotic lithium-air batteries have been heightened, focusing on improving their efficiency and cyclic stability [13,14]. To fully achieve the theoretical capacity of the lithium-air system, various configurations of Li-air batteries are under investigation [15]. Lithium-air batteries can be classified into four different types based on the electrolyte they use: aprotic (non-aqueous), aqueous, solid-state, and hybrid systems [16]. Among them, the aprotic (non-aqueous) systems have attracted more attention for their potentially higher energy density and cycle efficiency [17,18,19]. However, lithium-air batteries face challenges, particularly those related to electrolyte instability in oxygen-deficient conditions, reduced efficiency in the reversible cycling of Li metal anodes, and the degradation of catalytic materials [20,21]. The most critical issue is that the discharge products, Li2O2 and Li2CO3, accumulate at the cathode, leading to declining cycling performance by interfering with the oxygen reduction reaction (ORR) and the oxygen evolution reaction (OER) [22,23]. An effective approach to address the aforementioned issue is to develop efficient and corrosion-resistant bifunctional electrocatalysts toward ORR and OER [24].
To address these issues, research has focused on investigating various catalysts. In aprotic lithium-air batteries, well-known catalysts like noble metal catalysts, cheap metal catalysts, and carbon-based catalysts are primarily being examined for their bifunctional catalytic efficacy. Metal oxides have been widely researched as bifunctional electrocatalysts due to their notable catalytic efficacy, minimal toxicity, accessibility, and cost-effectiveness. And transition metal oxide spinel structures have demonstrated effectiveness as bifunctional catalysts, which is attributed to their elevated electrochemical activity and electronic conductivity [25]. In addition, numerous studies have demonstrated that nanostructured architectures, along with the varied configurations of structural units, can serve as a way to adjust the properties of materials. In these designs, the needle-like structure of NiCo2O4-based composites can significantly enhance electrochemical performance through diffusion reduction paths for electrolytes and electrons [26]. It provides effective pathways for oxygen transfer and offers a substantial specific surface area along with abundant active sites [27]. The spinel-type NiCo2O4 has attracted significant focus within the field of electrochemistry due to its excellent activity, high stability, environmental friendliness, and abundant resources [28,29,30]. One approach, particularly effective for enhancing electrochemical properties, involves creating oxygen vacancies on the surface through synthesis to activate the OER [31]. The oxygen defects in these materials are important [32]. The oxygen vacancies can significantly enhance the intrinsic conductivity, thereby improving electrochemical performance [33].
LABs are primarily composed of a porous cathode layer, a separator, a lithium anode, and an electrolyte. Frequently, porous cathode materials are combined with support materials of high conductivity. It is important to note that ‘support material’ refers only to a porous scaffold designed to accommodate Li2O2 (ORR), rather than decomposing Li2O2 (OER). Battery performance aspects such as energy efficiency, cycle retention, and capacity of LABs are significantly influenced by the support materials, and the properties of these support materials are crucial [34]. Specifically, the non-soluble discharge byproduct (mainly Li2O2) is produced on the surface of the support materials. Consequently, the design of the support materials’ structure should be thoughtfully considered to accommodate the discharge product and facilitate the diffusion of O2 gases and the penetration of electrolytes [35]. Carbon nanotubes (CNTs) are commonly employed in electrodes due to their outstanding conductivity, chemical stability, and large surface area [36,37]. However, the capacitance of CNTs is constrained by the mechanism for storing charge at the interface between the electrode and electrolyte [38]. Additionally, it is particularly difficult to disperse CNTs when creating the electrode slurry.
In this study, CNTs were treated with nitric acid to enhance their hydrophilicity, and the metal oxide NiCo2O4 was synthesized through a hydrothermal and an annealing process. The process for preparing NiCo2O4@CNTs follows the same manufacturing steps as NiCo2O4, with the additional inclusion of nitric acid-treated CNTs at the initial stage.
The purpose of this study is to develop a cathode composite with a catalyst for the long-term operation of lithium-air batteries in air conditions. We created a composite using a NiCo2O4 catalyst on CNTs using hydrothermal synthesis and annealing. The composite NiCo2O4@CNTs exhibited a significantly extended cycle life with lower overpotential compared to pristine CNTs.
We converted the conventional CNTs, which were originally used, into hydrophilic CNTs through a hydrothermal synthesis, making dispersion considerably easier. As a result, the synthesized final composite exhibited a longer cycle life compared to previously reported CNTs. Furthermore, the composite was found to have lower resistance than conventional CNTs using electrochemical impedance spectroscopy (EIS) measurements. The outstanding characteristics of the composite are attributed to its excellent OER/ORR reactions at the cathode. This can be considered a significant step toward achieving commercial lithium-air batteries.

2. Materials and Methods

2.1. Fabrication of Air Cathodes

Synthesis of the MWCNTs-COOH: 1 g of MWCNTs powder was stirred with 100 mL of HNO3 (Nitric Acid 70 wt %) at 90 °C for 2 h. After the reaction was completed, the resulting mixture was filtered, washed several times with D∙I water and ethanol, and then vacuum dried at 100 °C for 12 h to obtain the final powder.
Synthesis of the NiCo2O4: Co(NO3)2·6H2O (1.098 g) and Ni(NO3)2·6H2O (0.549 g) were dissolved in water in a 2:1 molar ratio, and then 1.68 g of urea was added. The solution was stirred for one hour until a bright pink color appeared. Afterward, it was placed in a Teflon-lined stainless steel autoclave and then heated at 120 °C for 12 h. The paste obtained through the hydrothermal process was filtered and washed several times with water and ethanol. Subsequently, it was vacuum dried overnight at 100 °C. Finally, the precursor underwent 2 h annealing at 350 °C at a slow heating rate (2 °C∙min−1) for the formation of NiCo2O4.
Synthesis of the NiCo2O4@CNTs: Co(NO3)2·6H2O (1.098 g) and Ni(NO3)2·6H2O (0.549 g) were dissolved in water at a molar ratio of 2:1, and then 1.68 g of urea, along with 0.3 g of MWCNTs-COOH, was added. Subsequently, the procedure was conducted exactly the same way as the NiCo2O4 synthesis method.

2.2. Material Characterization

The structural phases of the samples were analyzed using X-ray diffraction (SmartLab High Temp, Rigaku, Tokyo, Japan) with the following parameters: Cu target (λ = 1.54056 Ǻ), working voltage 45 kV, working current 200 mA, and the 2θ scanning ranging from 10° to 80°. The micromorphology of the product was observed using field emission scanning electron microscopy (Regulus 8220, HITACHI, Tokyo, Japan). The specific surface area of different samples was determined using a specific surface area and porosity analysis system (Belsorp max, Osaka, Japan).

2.3. Electrode Fabrication and Battery Measurement

The air cathodes were prepared by mixing three types of self-made powders and PVDF binders in a 9:1 ratio. Organic solvent NMP was used to create the slurry. Then, the prepared slurry was coated onto the prepared Gas Diffusion Layer (GDL) and vacuum dried at 100 °C for 12 h. The mass loading was calculated as the combined mass of oxide and carbon and was set at 0.5 mg/cm2 (±0.1).
CR 2032 coin cells were assembled in a glove box using the prepared air cathode, lithium foil as the anode, a Whatman glass fiber (GF/A) separator, and a 1 M LiTFSI TEGDME (tetraethylene glycol dimethyl ether) electrolyte. The assembled cell was allowed to rest for 12 h in an air atmosphere before conducting discharge-charge tests. The discharge-charge tests (Neware BTS 8.0, Neware, Dongguan, China) were carried out in the constant current (CC) mode under flowing air gas (60 sccm), and the cut-off voltage was set to a range from 2.2 V to 4.5 V at 200 mA·g−1 and 500 mA·g−1.
Galvanostatic discharge-charge profiles were collected using the same battery cycler. To gain a more comprehensive understanding of the electrochemical responses of all cathodes, electrochemical impedance spectroscopy (EIS) was also conducted at an amplitude of 0.01 V, and a frequency range of 1 MHz to 0.01 Hz of the LABs was also applied to evaluate the LABs performances.

3. Results and Discussion

3.1. Characterization of Samples

Figure 1 presents the TGA measurement values of different samples. While NiCo2O4 remains relatively stable up to temperatures exceeding 800 °C, it can be observed that both MWCNTs-COOH and NiCo2O4@CNTs experience a rapid combustion of carbon at temperatures exceeding 350 °C, causing it to dissipate. Specifically, when calculating the evaporation rate of NiCo2O4@CNTs, carbon was found to account for approximately 8%. This implies that the synthesized NiCo2O4@CNTs composites contained a CNT content of 8%.
Figure 2 shows the EDS mapping image of the NiCo2O4@CNTs composites. This was performed to experimentally analyze the components more accurately. Table 1 presents the mass and atomic ratios of the NiCo2O4@CNTs composites. When examining the chart, it is clear that each element is visibly distributed. The composite contains 21.21% carbon, 37.48% oxygen, 28.93% cobalt, and 12.37% nickel. While EDS mapping does not provide a quantitative distribution, it still confirms that the elements coexist in a granular form through the synthesis. These results confirm that the synthesis was successfully achieved.
Figure 3 presents the X-ray diffraction analysis (XRD), which was conducted to analyze the structural characteristics of the NiCo2O4@CNTs composites and other samples. The pattern of the NiCo2O4@CNTs closely matches that of NiCo2O4, with a slight presence of the MWCNTs pattern. In the XRD pattern of the MWCNTs-COOH, the two peaks at 25.9° and 43° correspond to the (002) and (100) planes, respectively, and the peaks at 18.90°, 31.14°, 36.69°, 44.62°, 59.09°, and 64.98° are respectively identified as the (111), (220), (311), (400), (511), and (440) planes belonging to the NiCo2O4, and the NiCo2O4@CNTs pattern contains both samples. No additional impurities or peaks corresponding to other phases were observed.
Figure 4 shows an SEM image taken to examine the morphologies of the MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs. Figure 4a,b depict MWCNT-COOH with a smooth-walled structure. Figure 4c,d show the images of NiCo2O4. Upon inspection of the images, it can be observed that spherical structures resembling needles have formed. Figure 4e,f show the presence of CNTs alongside the nanoneedle cluster structures. While the majority of the morphology corresponds to NiCo2O4, the content of CNTs has been previously investigated using EDS mapping and TGA.
N2 adsorption-desorption isotherms of the different samples are compiled in Figure 5 for the analysis of their porous structure, revealing a large surface area. The numerical values for each sample are presented in Table 2. The surface area value of MWCNTs-COOH is 417.53 m2∙g−1 and that of NiCo2O4 is 100.83 m2∙g−1. The specific surface area value of NiCo2O4@CNTs (221.21 m2∙g−1) falls between the values of the other two samples, as observed. This once again demonstrates the successful outcome of the previous synthesis experiment for NiCo2O4@CNTs.
Surface area is one of the critical factors of anode performance. If it is too large, capacity may be limited [39,40,41]. This is, in part, attributed to the binder, which blocks most pores below ~300 Å, and which is a dominant influence on the pore-size distribution for many high-surface-area carbons.

3.2. Electrochemical Performance

Figure 6 illustrates the electrochemical impedance spectroscopy (EIS) data for each assessed cathode, evaluated on LABs at an open circuit voltage (OCV) over a range of frequencies from 1 MHz to 0.01 Hz, with an amplitude of 0.01 V. The depressed semicircle in the middle of the frequency range represents the charge transfer resistance (Rct), which can be evaluated using the diameter of the semicircle [42,43]. The Rct of the MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs cathodes were 279 Ω, 281 Ω, and 211 Ω, respectively, indicating that the transfer resistance of the NiCo2O4@CNTs before recharging was smaller than those of MWCNTs-COOH and NiCo2O4 cathodes. From the results, it can be inferred that the low transfer resistance of the NiCo2O4@CNTs may contribute to the outstanding reversibility of ORR and OER and the enhancement in electrochemical performance.
The coin cells assembled using the prepared samples underwent discharge-charge testing in an air atmosphere within a voltage range of 2.2 to 4.5 V. Figure 7 presents the first galvanostatic discharge and charge profiles of the different electrodes at a current density of 400 mA∙g−1 from 2.2 to 4.5 V. As a result, the discharge specific capacities of the MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs cathodes were 3,297, 10,180, and 17,137 mAh∙g−1, respectively. Specifically, the specific capacity of MWCNTs-COOH was measured to be relatively lower, which is believed to be attributed to the discharge byproducts (Li2O2) formed during the discharge-charge process, obstructing active sites and resulting in reduced capacity.
The addition of catalysts substantially increased the discharge-specific capacity and overall performance of the coin cells [44]. This discovery confirms that the porous and heterostructured design of NiCo2O4 electrodes provides more space and sites for the accumulation of Li+ ions, leading to improved energy storage performance compared to other electrodes.
The current density testing was conducted under conditions of 200 mA∙g−1 and 500 mA∙g−1, and the capacity was set at 500 mAh∙g−1. Both the current density and capacity were determined based on the combined values of the carbon and metal oxides. The voltage gap is the difference between the charge terminal voltage point and the discharge terminal voltage point after the 30th cycle. Figure 8 shows the discharge-charge process under a limited capacity mode of 500 mAh∙g−1 at a specific current of 200 mA∙g−1. Figure 8a,b represent the discharge-charge cycle curves of the MWCNTs-COOH. It can be observed that approximately 55 cycles of charge and discharge occur, after which the capacity was no longer maintained. The electrode also showed quite large voltage gaps of 1.59 V (Figure 8a) at 30 cycles. Therefore, it is evident that in cells using only carbon, discharge-charge cycles occur relatively briefly. The reason for this is that discharge byproducts (Li2O2) on the air cathode do not decompose and accumulate and obstruct active sites.
Figure 8c,d depict the NiCo2O4 samples, which maintained cycling for approximately 71 cycles. The electrode showed voltage gaps of 1.49 V (Figure 8c) at 30 cycles. This indicates that it has better performance characteristics than MWCNT-COOH. Figure 8e,f depict the cycling characteristics of the NiCo2O4@CNTs composite. It maintained its capacity for approximately 160 cycles, demonstrating significantly higher cycling stability compared to other samples. The electrode showed quite low voltage gaps of 1.27 V (Figure 8e) at 30 cycles. This was the lowest voltage value among the samples.
As demonstrated in our experiments, the NiCo2O4@CNTs composite with an appropriate carbon content significantly enhanced electrochemical performance [45]. Notably, the ultrahigh electrochemical performance of the NiCo2O4@CNTs composite can be attributed to its unique three-dimensional structure [46,47]. During the formation of the nanoneedle cluster cathode structure, more active sites were created on the surface, improving OER and ORR performance and thereby enhancing the effective activity of the catalyst. However, pure NiCo2O4 exhibited relatively low cycle stability due to its very low specific surface area, resulting in a limited number of active sites. For a more thorough evaluation of cyclability at a high specific current, the coin cells were also evaluated at a specific current of 500 mA∙g−1 (Figure 9). It was surprising that even at such an elevated discharge-charge rate, the cell with the NiCo2O4@CNTs composite performed for 120 cycles, while the cells containing the MWCNTs-COOH and NiCo2O4 cells operated for only 35 and 42 cycles. This confirms that there is a distinct difference in cycle stability, particularly as the current density increases. In particular, NiCo2O4@CNTs composites exhibited significantly higher cycle characteristics compared to the other two samples.
The NiCo2O4@CNTs composite electrode also showed quite low voltage gaps of 1.40 V (Figure 9e) at 30 cycles among all samples. The NiCo2O4@CNTs not only provided a straightforward pathway for electron transport but also aided in the decomposition of Li2CO3 and Li2O2, helping to reduce over-potentials and ultimately leading to stability.
Figure 10 presents the surface after the fifth discharge-charge cycle (500 mA∙g−1, 500 mAh∙g−1) for MWCNTs, NiCo2O4, and NiCo2O4@CNTs. Figure 10a represents MWCNTs-COOH. Upon examining the images, it is evident that discharge byproducts (Li2O2) generated during the charge-discharge process are not decomposed and remain abundantly on the surface. Figure 10b represents the surface of NiCo2O4. It is observed that the decomposition of discharge byproducts on the surface of NiCo2O4 occurred more effectively than in MWCNTs-COOH. This can be interpreted as a well-supported catalytic role. Finally, Figure 10c depicts the composite of NiCo2O4@CNTs. The image in Figure 10c confirms that the decomposition of Li2O2 most effectively occurs on the surface of NiCo2O4@CNTs. This indicates excellent cycle stability through the most reversible reaction.
Figure 11 shows the rate performance of the NiCo2O4@CNTs composite. The current densities progressively increased from 50 to 100, 200, 300, and 500 mA∙g−1. No notable increase in polarization was observed in the discharging processes; in contrast, the charge polarization increased gradually, especially at current densities of 300 mA∙g−1 and 500 mA g−1. This indicates a gradual decrease in cycle performance from a current density of 300 mA∙g−1. Therefore, as the current density increases, the cycle life characteristics decrease accordingly. The NiCo2O4@CNTs electrode displayed a great rate of performance in lithium-air batteries. These results confirm superior performance compared to cycle life and capacity data reported in other papers with different catalysts on CNTs [48,49].
Figure 12 illustrates a schematic of the discharge-charge process of the NiCo2O4@CNTs. In such a unique structure, the ultrafine NiCo2O4 phase offered high catalytic activity for ORR and OER. However, in this document, the studied catalyst, NiCo2O4, had a spherical shape with a reported surface area of 90 m2∙g−1 [50]. In contrast, we achieved a nanoneedle cluster structure with a surface area of 221.21 m2∙g−1. This study suggests that the NiCo2O4@CNTs we synthesized significantly expanded the active site area, resulting in high-performance characteristics within the catalyst material itself. As a whole, these electrochemical performance results make the NiCo2O4@CNTs composite a promising candidate for LABs.

4. Conclusions

In this study, MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs were synthesized and prepared using hydrothermal synthesis and sintering processes. Subsequently, material analysis and electrochemical evaluations were conducted. Initially, TGA measurements confirmed an 8% carbon content in the NiCo2O4@CNTs, and EDS mapping was utilized to determine the composite’s composition ratio. Further structural analysis was carried out using XRD, while morphological analysis was conducted using SEM. BET measurements revealed that the specific surface area of the NiCo2O4@CNTs at 221.21 m2∙g−1 represented an intermediate value between the other two samples. The resulting NiCo2O4@CNTs composites were successfully designed and applied as the air cathode for a Li-air battery, and an electrochemical evaluation test was conducted. First, EIS measurements revealed a significant reduction in charge transfer resistance for the NiCo2O4@CNTs cell. The battery utilizing the NiCo2O4@CNTs composite air cathode demonstrated stable cycling performance for more than 100 cycles at current densities of 200 mA∙g−1 and 500 mA∙g−1. The NiCo2O4@CNTs composite air electrode revealed two times longer lifespan with 1.27 V (200 mA∙g−1) and 1.40 V (500 mA∙g−1) lower over-potentials. To analyze this, the surface of the electrode was examined after 30 cycles, revealing that NiCo2O4@CNTs composites promote the decomposition of discharge byproducts (Li2O2). The cell exhibited very great stability after extended cycles in air, avoiding the instability issues of conventional non-aqueous Li-air batteries. Overall, this study confirms the feasibility of enhanced designs for air cathodes in Li-air batteries.

Author Contributions

Conceptualization, D.-S.H.; Formal analysis, Y.-J.C., C.-S.J., K.-H.S. and W.-J.S.; Writing—review & editing, S.-H.Y. All authors have read and agreed to the published version of the manuscript.

Funding

This research was supported by a grant from the R&D Program (20220610100010, 20023127) funded by the Ministry of Trade, Industry and Energy, and the R&D Program (C3-2410, C3-2426, C3-2411) funded by the KIER of Republic of Korea, respectively.

Data Availability Statement

Data are contained within the article.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. TGA curves of the different samples.
Figure 1. TGA curves of the different samples.
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Figure 2. EDS mapping of the NiCo2O4@CNTs composites.
Figure 2. EDS mapping of the NiCo2O4@CNTs composites.
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Figure 3. XRD patterns of different samples.
Figure 3. XRD patterns of different samples.
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Figure 4. SEM image of MWCNTs-COOH (a,b), NiCo2O4 (c,d), and NiCo2O4@CNTs composites (e,f).
Figure 4. SEM image of MWCNTs-COOH (a,b), NiCo2O4 (c,d), and NiCo2O4@CNTs composites (e,f).
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Figure 5. N2 adsorption-desorption isotherm plots of different samples.
Figure 5. N2 adsorption-desorption isotherm plots of different samples.
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Figure 6. EIS spectra of different electrode cells before recharge.
Figure 6. EIS spectra of different electrode cells before recharge.
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Figure 7. Comparison of the initial discharge-charge profiles of the LABs from 2.2 to 4.5 V for MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs cathode at 400 mA∙g−1.
Figure 7. Comparison of the initial discharge-charge profiles of the LABs from 2.2 to 4.5 V for MWCNTs-COOH, NiCo2O4, and NiCo2O4@CNTs cathode at 400 mA∙g−1.
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Figure 8. (a) Galvanostatic discharge-charge voltage MWCNTs-COOH and (b) voltages corresponding to (a). (c) Galvanostatic discharge-charge voltage NiCo2O4 and (d) voltages corresponding to (c). (e) Galvanostatic discharge-charge voltage NiCo2O4@CNTs and (f) voltages corresponding to (e) at a current density of 200 mA∙g−1.
Figure 8. (a) Galvanostatic discharge-charge voltage MWCNTs-COOH and (b) voltages corresponding to (a). (c) Galvanostatic discharge-charge voltage NiCo2O4 and (d) voltages corresponding to (c). (e) Galvanostatic discharge-charge voltage NiCo2O4@CNTs and (f) voltages corresponding to (e) at a current density of 200 mA∙g−1.
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Figure 9. (a) Galvanostatic discharge-charge voltage MWCNTs-COOH and (b) voltages corresponding to (a). (c) Galvanostatic discharge-charge voltage NiCo2O4 and (d) voltages corresponding to (c). (e) Galvanostatic discharge-charge voltage NiCo2O4@CNTs and (f) voltages corresponding to (e) at a current density of 500 mA∙g−1.
Figure 9. (a) Galvanostatic discharge-charge voltage MWCNTs-COOH and (b) voltages corresponding to (a). (c) Galvanostatic discharge-charge voltage NiCo2O4 and (d) voltages corresponding to (c). (e) Galvanostatic discharge-charge voltage NiCo2O4@CNTs and (f) voltages corresponding to (e) at a current density of 500 mA∙g−1.
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Figure 10. SEM images of (a) MWCNTs-COOH, (b) NiCo2O4, and (c) NiCo2O4@CNTs after 5th charging.
Figure 10. SEM images of (a) MWCNTs-COOH, (b) NiCo2O4, and (c) NiCo2O4@CNTs after 5th charging.
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Figure 11. Cell potential profiles of the Li-air cells using NiCo2O4@CNTs composites at different current densities.
Figure 11. Cell potential profiles of the Li-air cells using NiCo2O4@CNTs composites at different current densities.
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Figure 12. Schematic illustration of the discharge-charge process of NiCo2O4@CNTs composite electrodes.
Figure 12. Schematic illustration of the discharge-charge process of NiCo2O4@CNTs composite electrodes.
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Table 1. EDS mapping data of the obtained NiCo2O4@CNTs composites.
Table 1. EDS mapping data of the obtained NiCo2O4@CNTs composites.
ElementWt %Atomic %
C21.2136.71
O37.4848.70
Co28.9310.21
Ni12.374.38
Total99.99100
Table 2. N2 adsorption-desorption representing the surface area.
Table 2. N2 adsorption-desorption representing the surface area.
SampleS (m2∙g−1)
MWCNTs-COOH417.53
NiCo2O4100.83
NiCo2O4@CNTs221.21
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Hong, D.-S.; Choi, Y.-J.; Jin, C.-S.; Shin, K.-H.; Song, W.-J.; Yeon, S.-H. Enhanced Cycle Performance of NiCo2O4/CNTs Composites in Lithium-Air Batteries. Energies 2024, 17, 58. https://doi.org/10.3390/en17010058

AMA Style

Hong D-S, Choi Y-J, Jin C-S, Shin K-H, Song W-J, Yeon S-H. Enhanced Cycle Performance of NiCo2O4/CNTs Composites in Lithium-Air Batteries. Energies. 2024; 17(1):58. https://doi.org/10.3390/en17010058

Chicago/Turabian Style

Hong, Dae-Seon, Yeon-Ji Choi, Chang-Su Jin, Kyoung-Hee Shin, Woo-Jin Song, and Sun-Hwa Yeon. 2024. "Enhanced Cycle Performance of NiCo2O4/CNTs Composites in Lithium-Air Batteries" Energies 17, no. 1: 58. https://doi.org/10.3390/en17010058

APA Style

Hong, D. -S., Choi, Y. -J., Jin, C. -S., Shin, K. -H., Song, W. -J., & Yeon, S. -H. (2024). Enhanced Cycle Performance of NiCo2O4/CNTs Composites in Lithium-Air Batteries. Energies, 17(1), 58. https://doi.org/10.3390/en17010058

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