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Article

A Novel High-Performance Anode Material with an Enlarged Potential Window for a Hybrid Energy Storage System

by
Abdul Mateen
1,
Muhammad Zubair
2,
Muhammad Saleem
3,
Alexandra Golubenkova
4,
Leonid Voskressensky
4,
Asma A. Alothman
5,
Mohamed Ouladsmane
5,
Awais Ahmad
6,* and
Muhammad Sufyan Javed
7,*
1
Department of Physics and Beijing Key Laboratory of Energy Conversion and Storage Materials, Beijing Normal University, Beijing 100084, China
2
Institute of Energy and Climate Research, Materials Synthesis and Processing (IEK-1), Forschungszentrum Jülich GmbH, 52425 Jülich, Germany
3
Department of Physics, The Islamia University of Bahawalpur, Bahawalpur 63100, Pakistan
4
Department of Organic Chemistry, Faculty of Science, Peoples Friendship University of Russia (RUDN University), Miklukho Maklaya Str., 117198 Moscow, Russia
5
Department of Chemistry, College of Science, King Saud University, Riyadh 11451, Saudi Arabia
6
Departamento de Quimica Organica, Universidad de Cordoba, Edificio Marie Curie (C-3), Ctra Nnal IV-A, Km 396, E14014 Cordoba, Spain
7
School of Physical Science and Technology, Lanzhou University, Lanzhou 730000, China
*
Authors to whom correspondence should be addressed.
Energies 2022, 15(24), 9577; https://doi.org/10.3390/en15249577
Submission received: 13 October 2022 / Revised: 12 November 2022 / Accepted: 6 December 2022 / Published: 16 December 2022
(This article belongs to the Section A2: Solar Energy and Photovoltaic Systems)
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Versions Notes

Abstract

:
Cobalt-iron (CoFe) layered double hydroxides (LDHs) have received much interest for supercapacitors (SCs) because of their ion-insertable layer structure. However, there is still a need for more effort to increase their potential window and overall electrochemical energy storage capability as SC electrodes. In this work, we present a straightforward approach to synthesizing CoFe-LDHs on zinc oxide seeded carbon cloth (ZnO@CC) via a one-step hydrothermal reaction; the obtained electrode is denoted as CoFe-LDH@ZnO@CC. The electrochemical energy storage properties of CoFe-LDH@ZnO@CC are tested as an anode material using a three-electrode setup for SC applications in 1 M Na2SO4 electrolyte. It can operate in a wider potential window reaching up to 1.6 V, exceeding most previously reported anode materials. The CoFe-LDH@ZnO@CC displayed capacitive charge storage accounting for 76% of the total charge stored at 20 mV/s. The CoFe-LDH@ZnO@CC anode delivered a maximum capacitance of 299.8 F/g at 2 A/g, outstanding cycle stability, and retained 97.7% of the initial capacitance value for 5000 cycles at 16 A/g. This study introduces a new strategy for structurally designing electroactive materials for energy storage devices, which might be useful as an anode for SCs.

1. Introduction

As a result of the increased use of fossil fuel energy throughout the world, there is an increasing need to develop alternative clean, affordable, and efficient technologies for energy storage. Supercapacitors (SCs) have attracted much interest because of their characteristics of rapid charging–discharging, high specific power, an extended cycle life, and being environmentally friendly [1,2,3]. Compared to rechargeable batteries, SCs offer significantly more energy storage throughout the electrochemical process, making them an integral feature of modern electronic gadgets [4,5]. To a large extent, the SCs’ electrochemical performance is determined by the active material, which is an essential part of the SCs [6,7]. The exploitation of high-capacitive anode and cathode materials has received significant research attention [8,9].
Depending on the method of storing energy, SCs can be divided into electric double-layer capacitors (EDLCs) and Faradaic pseudocapacitors [10,11]. In EDLCs, energy is stored by absorbing the static charges onto the surface of active material. Typically, active materials are prepared by carbon-based substances such as carbon nanotubes [12], graphene [13], and activated carbon (AC) [14]. Besides these materials, because of the many oxidation states of transition metals and their characteristic layered structures, layered double hydroxides (LDHs) have become fascinating candidates as energy storage materials for SCs’ electrodes [15,16]. Considering their layered architectures, adjustable structures, and excessive cation dispersion in layers of metal hydroxide, much interest has focused on mixed metal LDHs [17]. As electrode materials, mixed transition metal LDHs are often the subject of research. Some examples are Ni–Mn LDH [18], Co–Ni LDH [19], Ni–Fe LDH [20], Co–Al LDH [21], and NiCoAl LDH [22]. Cobalt and iron ions coexist in the host layers of the CoFe LDH, which have gained attention because of their synergistic effects and abundant redox reactions in electrochemical processes [23]. However, pristine CoFe LDHs often display poor performances because of poor conductivity, which restricts the energy applications of CoFe LDHs. CoFe LDH nanosheets, including CuO@Co–Fe LDH [24], NiO@Co–Fe LDH [25], and Ni@Co–Fe LDH [26], were presented for energy applications. For instance, the Ni@Co–Fe LDH nanosheet delivered a capacitance of 1289 F/g at 1 A g, and it retains 75.9% capacitance after 5000 cycles [26]. However, such nanostructures possess low potential windows and poor cycling stability. Zinc oxide (ZnO), as a semiconductor material, has received much attention with its potential applications and is a promising active material because of its good conductivity, strong electrochemical activity, and minimal environmental effect [27,28]. Thus, by coupling the excellently conductive ZnO with the highly active CoFe LDH, it is anticipated that the resultant structure will have a wide potential window and outstanding electrochemical performance.
Herein, we report a simple approach to synthesizing CoFe-LDH@ZnO@CC, which, as a binder-free anode, can be operated in a wider potential window up to 1.6 V. The CoFe-LDH@ZnO@CC displayed capacitive charge storage accounting for 76% of the total charge stored at 20 mV/s. The CoFe-LDH@ZnO@CC anode delivered a maximum capacitance of 299.8 F/g at 2 A/g, outstanding cycle stability, and retained 97.7% of the initial capacitance value for 5000 cycles at 16 A/g. This study introduces a new strategy for structurally designing electroactive materials for energy storage devices, which might be useful as an anode for SCs.

2. Experimental Method

2.1. Synthesis of ZnO@CC

In synthesizing ZnO seeds on carbon cloth (CC), 6 M Zn(CH3COO)2·2H2O was mixed in deionized water (DI). The dip-coating method was employed to grow the seed layer in the CC substrate. In this method, the clean CC substrate was dipped in the ZnO aqueous solution for 50 s and then heated at 300 °C for 5 min in a preheated oven. This procedure was performed 5 times to obtain a uniform ZnO seed layer on the CC.

2.2. Synthesis of CoFe-LDH@ZnO@CC

A hydrothermal assembly process was performed to synthesize the CoFe-LDH on seeded ZnO@CC. In a typical procedure, 40 mL of DI water, 0.044 M of Fe(NO3)3·9H2O, and 0.18 M of Co(NO3)2·6H2O were dissolved to make a homogeneous solution. The pH was adjusted at pH 9 by adding 1 M NaOH and continuous stirring. After that, the resulting solution was placed in a Teflon-lined autoclave of 100 mL with two pieces of ZnO@CC (2 × 4 cm2) and heated at a temperature of 120 °C for 12 h. Finally, CoFe-LDH@ZnO@CC was dried for 12 h at 60 °C, after being rinsed three times in DI water.

2.3. Physical Characterization

A field emission scanning electron microscope (FESEM, HITACHI SU8220) was employed to examine the architecture of the prepared samples. For structural analysis, X-ray diffraction (XRD) (X’Pert Pro PANalytical) was used on Cu Kα with λ = 0.15406 nm. Brunauer–Emmett–Teller (BET) analytical curves were employed in the calculation of the surface area, and the Barret–Joyner–Halenda (BJH) analyzer (Micromeritics ASAP2460) was used to assess the sample’s pore size.

2.4. Electrochemical Measurements

The as-prepared CoFe-LDH@ZnO@CC was directly employed as a binder-free working electrode with a platinum plate, Ag and AgCl as the counter and reference electrodes, respectively, using 1 M Na2SO4 aqueous electrolyte. An electrochemical workstation (CHI 660 E, Wuhan, China) was used to perform cyclic voltammetry (CV) (in a potential window of 0.0 to −1.6 V), galvanostatic charge-discharge (GCD) tests (at varying current densities in the range of 2 to 32 A/g), and electrochemical impedance spectroscopy (EIS) measurements (at a frequency range of 0.001 to 100 kHz). To calculate capacitance, the following equation is used;
C s p = I Δ t m × Δ V
where Csp (F/g), m (g), I (A), ΔV (V), and Δt (s) are capacitance, the mass of the anode, current, potential window, and discharging time, respectively.

3. Results and Discussion

Figure 1 provides a visual representation of the synthesis approach for the CoFe-LDH@ZnO@CC. CC was employed as a binder-free substrate as well as a current collector. The ZnO seeded layer was grown on the CC substrate using a seed-assisted facile dip-coating method. Finally, producing the CoFe-LDH at the ZnO@CC seeded layer was carried out via a hydrothermal method.
The structure of the samples was investigated using FESEM. The FESEM image of the CC (Figure 2a) exhibits the smooth surface of CC fibers with a three-dimensional matrix. Interestingly, following ZnO seed deposition, the CC surface turned porous, which is very important for loading the active materials for energy storage applications (Figure 2b). Surprisingly, the ZnO seeds produced a layer rather than individual quantum dots, suggesting that the ZnO film may serve as the electrode for electric charge collection. As in Figure 2c,d, low-resolution FESEM images of CoFe-LDH@ZnO@CC show the quasi-upright nature of CoFe-LDH nanosheets densely formed on the ZnO@CC. Moreover, as seen in Figure 2d, the tiny cavities are uniformly dispersed and scattered to host the electrolyte ions in the charging–discharging technique. The high-magnification FESEM image (Figure 2e) demonstrates the highly dense growth of CoFe-LDH@ZnO@CC. It verifies the presence of consistently rich cavities, which provide a very conducive structure for accumulating electrolyte ions.
Additionally, the CoFe-LDH nanosheets are quasi-vertical and interlinked in three dimensions, creating an open and porous network structure with an average thickness of ~16.1 nm, as shown in the magnified image (Figure 2f). The modest assembly of CoFe-LDH@ZnO@CC nanosheets with tiny cavities can provide an excellent surface area, and it is useful to transmit ions. It can minimize the resistance at the electrode/electrolyte contact, thereby imparting the electrode with superior electrochemical performance.
The XRD patterns of bare CC, ZnO@CC, and CoFe-LDH@ZnO@CC are illustrated in Figure 3. The characteristic peaks of ZnO@CC are located at 31.8°, 34.5°, 36.5°, and 56.7°, which can be indexed to the (100), (002), (102), and (110) planes of ZnO (JCPDS No. 65-3411) [29]. A prominent (002) characteristic peak positioned at 24.6° is consistent with the CC, indicating that ZnO seeds were effectively formed on the CC substrate. Further, for the CoFe-LDH@ZnO@CC, the characteristic diffraction peaks located at 18.2°, 29.7°, 34.9°, 35.2°, 43.1°, 55.5°, and 63.6° can be attributed to the (111), (220), (311), (400), (531), and (440) planes, respectively (JCPDS No. 22-1086) [30]. Thus, the crystal structures of ZnO@CC and CoFe-LDH remain unchanged throughout the synthesis of CoFe-LDH@ZnO@CC.
As demonstrated in Figure 4, the N2-sorption method was employed to investigate the surface area and porosity of the ZnO@CC and CoFe-LDH@ZnO@CC samples, respectively. Both ZnO@CC and CoFe-LDH@ZnO@CC samples display standard type-III isotherms with a prominent adsorption–desorption hysteresis loop [31], which indicates the presence of typical mesoporous structures, as illustrated in Figure 4a. Surface areas were determined according to the BET method, and for the ZnO@CC and CoFe-LDH@ZnO@CC samples, were found to be 19 m2/g and 42.5 m2/g, respectively. Figure 4b depicts the pore size distribution curves of the ZnO@CC and CoFe-LDH@ZnO@CC samples derived according to the BJH technique. The ZnO@CC and CoFe-LDH@ZnO@CC samples display wider pores with average diameters of 27.5 and 29.8 nm, respectively. The increased surface area and broader pore size would generate abundant active sites with a better approach for the electrolyte ions, hence enhancing the overall performance of CoFe-LDH@ZnO@CC for charge storage [32].
Relating to the electrochemical performance of the ZnO@CC and CoFe-LDH@ZnO@CC as anode materials for SCs, Figure 5a exhibits CV profiles of the CC, ZnO@CC, and CoFe-LDH@ZnO@CC anodes in their respective potential window range at 10 mV/s. The CC and ZnO@CC electrodes contribute negligibly to the capacitance compared with CoFe-LDH@ZnO@CC. It is important to point out that the potential window of CoFe-LDH@ZnO@CC is high, up to 1.6 V, while the CC and ZnO@CC anode can operate only in the range of −1.0 to 0.0 V. Further, the CV profile of CoFe-LDH@ZnO@CC shows prominent redox peaks (anodic at −0.62 V and cathodic at −1.0 V), which suggests the existence of Faradaic redox processes in the CoFe-LDH@ZnO@CC sample. Combining Faradic reactions with EDLC storage explains the redox processes, which contribute to the robust pseudocapacitive nature of the anode material [33].
Fe(OH)2 + OH− ↔ FeOOH + H2O + e−
Co(OH)2 + OH− ↔ CoOOH + H2O + e−
Compared to CC and ZnO@CC, an enhanced specific capacitance can be inferred from the larger CV area for CoFe-LDH@ZnO@CC, due to the outstanding conductivity and interconnectivity of CoFe-LDH. The CV profiles of CoFe-LDH@ZnO@CC at 187 different sweep rates (2–75 mV/s) are presented in Figure 5b. The CoFe-LDH@ZnO@CC sample demonstrated exceptionally capacitive behaviour, outstanding ion responsiveness, and strong rate capabilities, with a slight shift in the cathodic/anodic peaks, even when the sweep rate was relatively high (75 mV/s) [34]. Furthermore, a power law analysis of electrochemical kinetics was performed to investigate the mechanism for charge storage in the CoFe-LDH@ZnO@CC electrode [35].
I(V) = a.vb
and
log (i) = b log (v) + log (a)
where i, v, and a and b are the current density, sweep rate, and arbitrary constants, respectively. If the b-value is 0.5, it indicates that the capacitance was controlled by ionic diffusion; however, if the b-value is equal to 1.0, it indicates the capacitive mechanism predominates during the charging–discharging processes; the corresponding b-values are 0.66 and 0.65, respectively. It demonstrates that synchronous diffusion and capacitive-controlled processes are involved in the electrochemical reaction of the CoFe-LDH@ZnO@CC sample, as shown in Figure 5c. Further, Figure 5d illustrates that at 20 mV/s, the CoFe-LDH@ZnO@CC stores 76% of its charge via a capacitive-controlled process and 24% via a diffusion-controlled process. In addition, the capacitive/diffusion processes for the CoFe-LDH@ZnO@CC sample at varying sweep rates (1–50 mV/s) show that as the sweep rates increase (Figure 5e), the presence of the capacitive-controlled process rises, indicating that the capacitive process dominates the overall capacitance, particularly at high sweep rates.
Figure 6a shows the GCD profiles for CC, ZnO@CC, and CoFe-LDH@ZnO@CC in their potential windows at 10 A/g. The charging and discharging times for the CoFe-LDH@ZnO@CC are 63.1 s. It is much longer than the charging–discharging time of ZnO@CC (21.4 s) and CC (4.4 s), which agrees with the CV data. Further, the GCD profiles of the CoFe-LDH@ZnO@CC electrode at 2 to 32 A/g (Figure 6b) show the symmetrical shape of the GCD profiles across all current densities, which demonstrates the superior capacitive responsiveness and highly reversible charge-discharge of CoFe-LDH@ZnO@CC. A small IR drop in the discharging profile indicates that the CoFe-LDH@ZnO@CC electrode has a low internal resistance [36]. The prolonged discharging time at higher current densities and the constant symmetry exhibit exceptional charge-storage properties [37]. The capacitance (determined according to Equation (1)) of ZnO@CC and CoFe-LDH@ZnO@CC are 52.4 and 299.8 F/g, respectively, at 2 A/g (Figure 6c). The capacitance of the electrodes steadily falls as the current density increases because of the gradual voltage drop and inadequate electrode materials participating in the redox process at higher current densities. However, after raising the current density of the CoFe-LDH@ZnO@CC electrode to 32 A/g, the capacitance remained as high as 41.4% of the initial value, whereas, ZnO@CC retains just 22.9% of its capacitance. This is because of the low internal resistance of CoFe-LDH@ZnO@CC. The enhanced electrochemical performance of CoFe-LDH@ZnO@CC was determined by EIS experiments, and the Nyquist pattern, as shown in Figure 6d, which helps to explain the phenomenon. The computed equivalent series resistance (Rs) from the x-intercept for CoFe-LDH@ZnO@CC is Rs~2.36 Ω, while for ZnO@CC electrode, it is Rs~3.43 Ω. This reveals that the CoFe-LDH@ZnO@CC sample has a stronger electrical conductivity than ZnO@CC.
The cyclic life of both samples was evaluated at 16 A/g. The cyclic stability of the ZnO@CC and CoFe-LDH@ZnO@CC electrodes (Figure 7) shows that the CoFe-LDH@ZnO@CC electrode exhibited a capacitance retention of 97.7% for 1000 cycles, whereas ZnO@CC demonstrated retention of 79.5% for 5000 cycles. Thus, the CoFe-LDH@ZnO@CC electrode has exceptional cyclic performance.
A general comparasion of the current work with previously published similar work is presented in Table 1. These results show that the CoFe-LDH@ZnO@CC material has superior performance, i.e., exceptional capacitance with outstanding cyclic stability. The advantageous CoFe-LDH properties of the material are the primary cause of the CoFe-LDH@ZnO@CC material’s remarkable features. Thus, with the inclusion of cobalt and iron, CoFe-LDH@ZnO@CC possesses an exceptionally high electrochemical activity and relatively high surface area.

4. Conclusions

We have presented a straightforward method for synthesizing CoFe-LDH@ZnO@CC via a hydrothermal reaction. The binder-free CoFe-LDH@ZnO@CC anode was studied as a potential candidate for SC applications using a three-electrode setup in 1 M Na2SO4. Compared to other reported anode materials, it has a larger potential window, reaching up to 1.6 V. The CoFe-LDH@ZnO@CC sample displayed good charge storage capability, with capacitive-type charge storage accounting for 76% of the total charge stored at 20 mV/s. The fabricated CoFe-LDH@ZnO@CC sample exhibited a maximum capacitance of 299.8 F/g at 2 A/g and retained 97.7% of its initial capacitance for 5000 cycles at 16 A/g. The exceptional performance of CoFe-LDH@ZnO@CC may make it a desirable candidate to use as an excellent performance anode material for SCs.

Author Contributions

Conceptualization, A.M. and A.A.; Methodology, M.Z., M.S., A.G., L.V., A.A.A., M.O. and M.S.J.; Formal analysis, A.M. and A.A.; Investigation, M.Z., M.S., A.G. and L.V.; Resources, A.A.A. and A.A.; Data curation, A.M., M.Z., A.G., L.V., A.A.A. and M.S.J.; Writing—original draft, A.M., M.Z., M.S., M.O. and M.S.J.; Visualization, A.G., A.A.A., M.O. and A.A.; Supervision, A.A. and M.S.J.; Project administration, M.S., L.V., M.O. and M.S.J.; Funding acquisition, A.A. and M.S.J. All authors have read and agreed to the published version of the manuscript.

Funding

This work was funded by the Researchers Supporting Project Number (RSP-2021/243) at King Saud University, Riyadh, Saudi Arabia.

Data Availability Statement

Not applicable.

Acknowledgments

This work was financially supported by the Research Fund for International Scientists (52250410342), Scientific Research start-up grant for Youth Researchers at Lanzhou University and Supercomputing Center of Lanzhou University. This work was funded by the Researchers Supporting Project Number (RSP-2021/243) at King Saud University, Riyadh, Saudi Arabia. This publication has been prepared with support from the RUDN University Strategic Academic Leadership Program (L.V.).

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. Synthesis process forming CoFe-LDH@ZnO@CC.
Figure 1. Synthesis process forming CoFe-LDH@ZnO@CC.
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Figure 2. FESEM images of (a) CC; (b) ZnO@CC; (c,d) Low-magnification FESEM images of CoFe-LDH@ZnO@CC; (e) High-magnification FESEM images of CoFe-LDH@ZnO@CC; (f) an enlarged view.
Figure 2. FESEM images of (a) CC; (b) ZnO@CC; (c,d) Low-magnification FESEM images of CoFe-LDH@ZnO@CC; (e) High-magnification FESEM images of CoFe-LDH@ZnO@CC; (f) an enlarged view.
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Figure 3. XRD patterns of CC, ZnO@CC, and CoFe-LDH@ZnO@CC (Asterisk denoted the peaks generated form CC).
Figure 3. XRD patterns of CC, ZnO@CC, and CoFe-LDH@ZnO@CC (Asterisk denoted the peaks generated form CC).
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Figure 4. (a) N2-sorption isotherms of ZnO@CC and CoFe-LDH@ZnO@CC; (b) BJH pore-size distribution of ZnO@CC and CoFe-LDH@ZnO@CC.
Figure 4. (a) N2-sorption isotherms of ZnO@CC and CoFe-LDH@ZnO@CC; (b) BJH pore-size distribution of ZnO@CC and CoFe-LDH@ZnO@CC.
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Figure 5. (a) CV profiles of the CC, ZnO@CC, and CoFe-LDH@ZnO@CC samples; (b) CV profiles of ZnO@CC and CoFe-LDH@ZnO@CC at different sweep rates; (c) Calculation of b-values log(current density) versus log(sweep rate); (d) Percentage diffusion/capacitive mechanisms of CoFe-LDH@ZnO@CC; (e) Percentage contribution of diffusion/capacitive mechanisms at different sweep rates (1–50 mV/s) for CoFe-LDH@ZnO@CC.
Figure 5. (a) CV profiles of the CC, ZnO@CC, and CoFe-LDH@ZnO@CC samples; (b) CV profiles of ZnO@CC and CoFe-LDH@ZnO@CC at different sweep rates; (c) Calculation of b-values log(current density) versus log(sweep rate); (d) Percentage diffusion/capacitive mechanisms of CoFe-LDH@ZnO@CC; (e) Percentage contribution of diffusion/capacitive mechanisms at different sweep rates (1–50 mV/s) for CoFe-LDH@ZnO@CC.
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Figure 6. (a) GCD profiles of CC, ZnO@CC, and CoFe-LDH@ZnO@CC; (b) GCD profiles of CoFe-LDH@ZnO@CC at 2–32A/g; (c) Capacitance of ZnO@CC and CoFe-LDH@ZnO@CC vs. current density; (d) EIS plots.
Figure 6. (a) GCD profiles of CC, ZnO@CC, and CoFe-LDH@ZnO@CC; (b) GCD profiles of CoFe-LDH@ZnO@CC at 2–32A/g; (c) Capacitance of ZnO@CC and CoFe-LDH@ZnO@CC vs. current density; (d) EIS plots.
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Figure 7. Cyclic stability of ZnO@CC and CoFe-LDH@ZnO@CC.
Figure 7. Cyclic stability of ZnO@CC and CoFe-LDH@ZnO@CC.
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Table
Table 1. The comparison of ZnO@CC and CoFe-LDH@ZnO@CC with previously related work.
Table 1. The comparison of ZnO@CC and CoFe-LDH@ZnO@CC with previously related work.
Sr. No.Electrode MaterialsElectrolyteSpecific Capacitance (F/g)Current Density (A/g)No. of Cycles (n)Retention Rate (%)References
1 CoFe-LDH@ZnO@CC Na2SO4 299.8 2 5000 97.7 This work
2Co3O4 microspheresKOH261.10.5200090.2[38]
3Co3O4 particulatesKOH224.382.75100072.2[39]
4Co3O4 flakesKOH26320100089.4[40]
5α-Fe2O3Na2SO42161100089.2[41]
6NiOKOH1161200084[42]
7Al doped NiFe2O4Na2SO4250.90.5100096[43]
8NiFe2O4Na2SO4240.9 1200092.9[44]
9CoFe2O4/FeOOHKOH2320.5100091.3[45]
10CoFe2O4/rGOKOH1941250071.9[46]
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Mateen, A.; Zubair, M.; Saleem, M.; Golubenkova, A.; Voskressensky, L.; Alothman, A.A.; Ouladsmane, M.; Ahmad, A.; Javed, M.S. A Novel High-Performance Anode Material with an Enlarged Potential Window for a Hybrid Energy Storage System. Energies 2022, 15, 9577. https://doi.org/10.3390/en15249577

AMA Style

Mateen A, Zubair M, Saleem M, Golubenkova A, Voskressensky L, Alothman AA, Ouladsmane M, Ahmad A, Javed MS. A Novel High-Performance Anode Material with an Enlarged Potential Window for a Hybrid Energy Storage System. Energies. 2022; 15(24):9577. https://doi.org/10.3390/en15249577

Chicago/Turabian Style

Mateen, Abdul, Muhammad Zubair, Muhammad Saleem, Alexandra Golubenkova, Leonid Voskressensky, Asma A. Alothman, Mohamed Ouladsmane, Awais Ahmad, and Muhammad Sufyan Javed. 2022. "A Novel High-Performance Anode Material with an Enlarged Potential Window for a Hybrid Energy Storage System" Energies 15, no. 24: 9577. https://doi.org/10.3390/en15249577

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