Transition Bimetal Based MOF Nanosheets for Robust Aqueous Zn Battery

High-performance, good stability, low-cost, and environmentally friendly batteries are important for multifunctional electronics and electric vehicles. Compared with the high-energy density lithium-ion batteries, aqueous rechargeable battery has been extensively researched due to high safety, low cost and much better rate performance. Here, we report a one-step approach to fabricate porous Ni-Cu metal–organic framework (MOF) nanosheet arrays structures for stable energy storage with a high-energy (71.2 mWh cm⁻³) and high-stability (capacity retention of ≈91% after 2,500 cycles) performance. Furthermore, we synthesized various porous homogeneous Ni-Co, Ni-Zn, Ni-Fe and Ni-Mn bimetal MOF structures with high surface area and conductivity utilizing this rational design. This work provides a simple efficient strategy for constructing porous homogeneous bimetal MOF nanosheet arrays with high energy and stability performance, holding a great potential for future portable electronics.

Introduction

With the ever-increasing demand for renewable energy sources and conversion techniques, energy storage devices with high energy and power densities, good reliability, and long cycling life are urgently required (Bonaccorso et al., 2015; Wan et al., 2016; Zhai et al., 2018). Although high-energy density lithium-ion batteries have been extensively researched, the overall performance and wide usage have been limited due to their relatively low power density and safety (Kim et al., 2013; Li J. et al., 2015; Xu et al., 2019). By contrast, aqueous rechargeable battery is of particular interest owing to high safety, low cost, and much better rate performance (Duan et al., 2016; Gao et al., 2018; Stock et al., 2019). Zinc-based batteries are an alternative energy source due to their high theoretic capacity (819 mAhg⁻¹), relatively low redox potential and extensive global reserves (Pan et al., 2016; Fu et al., 2019). Particularly, compared with the output voltage of other aqueous batteries (mostly ≤ 1.2 V), nickel–zinc (Ni–Zn) battery has a higher output voltage (≈1.8 V) (Huang et al., 2013; Wang R. et al., 2018). However, the formation of zinc dendrite at anode and irreversible reactions at cathode during the electrochemical reaction will lead to inferior discharge performance and poor cycling stability (<500 cycles) (Liu et al., 2016). Therefore, designing good functionally and structurally stable electrode nanomaterials with high-activity nanostructures is highly important.

Metal–organic frameworks, as porous crystalline coordination polymers, which are formed by coordination bonds between metal atom nodes and organic ligands with periodic structural units (Yaghi and Li, 1995). Due to the highly porous structural characteristics, MOFs could provide a larger exposure reaction surface for fast ion/mass transport, resulting in a high capacitance and rate capability performance (Wu et al., 2017; Qiu et al., 2018). For instance, Dennis et al. first utilizing high electrical conductive MOFs (Ni₃(HITP)₂) for supercapacitors without other binders (Sheberla et al., 2016). Choi et al. prepared and examined 23 different structure nMOFs with multiple organic functionalities and metal ions, which exhibit exceptionally high capacitance (Choi et al., 2014). However, MOFs still have the issue of bad stability, poor conductivity and the blocking of active sites by organic ligands (Li et al., 1999). Recently, two kinds of metallic elements have been incorporated in the crystallization process to successfully synthesize the homogeneous bimetallic MOF topology with different molar ratios (Yan et al., 2017; Wang X.L. et al., 2018). It's electrochemical properties and stability can be significantly improved due to the synergistic interactions, such as improved charge transfer between dopants and host metal atoms (Huang et al., 2018; Wang H. et al., 2018). For example, Li et al. synthesized a mesoporous Ni_0.3Co_2.7O₄ nanorod derived by Co/Ni-MOFs, which delivered a large reversible capacity of 1,410 mAhg⁻¹ after 200 cycles at a current of 100 mAg⁻¹ with an high-rate capability for lithium-ion batteries (Li et al., 2016). Yan et al. reported a Ni–Co bimetal phosphide Ni_0.6Co_1.4P nanocages as highly efficient electrocatalysts with long-term stability (10 h for continuous test) via phosphorization from Ni_0.6Co_1.4(OH)₂ metal-organic framework (Qiu et al., 2018). Additionally, as unique 2D nanostructures could exhibit rapid ion/mass transport, high specific surface area and high percentages of exposed active coordinative metal sites, it would be of great significance to develop 2D MOFs and derived arrayed structures (Zhao et al., 2016; Wu et al., 2020). Thus, combining the homogeneous bimetallic MOF topology and 2D arrayed nanostructures would offer an ideal model to construct highly efficient electrode material with long-term stability and explore precise structure–performance relationships at atomic/molecular levels (Dang et al., 2017; Wan et al., 2017).

Herein, we presented a novel one-step approach to synthesize various porous bimetal organic framework nanosheet arrays structures for stable energy storage. Through mixing solvents, benzenedicarboxylic acid (BDC), nickel foam and different bimetallic precursors and maintained at 130°C for 2 h, we successfully synthesized porous homogeneous Ni-Co, Ni-Cu, Ni-Zn, Ni-Fe and Ni-Mn bimetal MOFs (expressed as Ni,Co-MOF, Ni,Cu-MOF, Ni,Zn-MOF, Ni,Fe-MOF and Ni,Mn-MOF). The as-synthesized nickel foams are uniformly coated with 2D arrayed porous bimetal MOFs, resulting in a high surface area and conductive current collector. Additionally, benefiting from the uniform distribution of metal centers, the Ni-Cu bimetal MOF achieves a high-energy (71.2 mWh cm⁻³) performance and high-stability (capacity retention of ≈91% after 2500 cycles) assembling into a battery. This work provides a simple efficient strategy for constructing robust cathode materials of Ni–Zn battery, which may pave the way for the rational design of high energy storage technology.

Materials and Methods

Materials

Benzenedicarboxylic acid (BDC) was obtained from Shanghai Aladdin Bio-Chem Technology Co., Ltd., and all other chemicals were purchased from Sinopharm Chemical Reagent Co., Ltd. All the solvents used in this study were of analytic grades.

Synthesis of Ni-MOF

First, 30 ml ethanol and 2 ml deionization water were mixed in a 50 ml Teflon-liner. Then 0.3 mmol BDC and 0.3 mmol Ni(NO₃)₂·6H₂O were added into the solution, while sonicated for about 30 min and put a nickel foam (2 2 cm) into the mixed solution. Finally, the 50 ml Teflon-lined autoclave was sealed and maintained at 130°C for 2 h. The product was washed by ethanol and deionization water.

Synthesis of Ni,Cu-MOF

After mixing 30 ml ethanol and 2 ml deionization water in a 50 ml Teflon-liner, the 0.3 mmol BDC, 0.15 mmol Ni(NO₃)₂·6H₂O and 0.15 mmol Cu(NO₃)₂·3H₂O were added into the mixed solution and sonicated for 30 min. With a nickel foam (2 2 cm) putting into the solution, the 50 ml Teflon-lined autoclave was maintained at 130°C for 2 h.

Synthesis of Other Bimetallic MOFs

The synthesis processes of Ni,Co-MOF, Ni,Zn-MOF, and Ni,Mn-MOF were same as the preparation of Ni,Cu-MOF, expect that 0.15 mmol Cu(NO₃)₂·3H₂O was replaced by 0.15 mmol Co(NO₃)₂·6H₂O, Zn(NO₃)₂·6H₂O and Mn(NO₃)₂·4H₂O, respectively. In the process of Ni,Fe-MOF, 0.24 mmol Ni(NO₃)₂·6H₂O and 0.06 mmol Fe(NO₃)₃·9H₂O were added into the mixed solution.

Electrical Measurements

For a typical three-electrode system, an Ag/AgCl reference electrode, an Pt plate counter electrode, and a Celgard separator (3501 Coated PP, Celgard LLC) were used in 1 M KOH aqueous solution. All tests were conducted in a three-neck Swagelok cells (t-branch pipe, Swagelok). They were pressed between two stainless steel rods from two necks of the Swagelok cells, and a third neck was used to put a reference electrode into the cell. Cyclic voltammograms (CVs), galvanostatic charge/discharge and impedance spectroscopy were performed by an electrochemical workstation (CHI 760E). The capacitance (C) values were calculated by the equation C = ∫(IV)/(mνΔV). The electrochemical characterizations of all full batteries were tested in a two-electrode cell in a solution of 1 M KOH and 0.02 M Zn(Ac)₂. The anode is a zinc plate with a thickness of 0.15 mm.

Characterization

The morphology size, crystal structure of samples were determined by the scanning electron microscopy (SEM, FEI Nova 450 Nano), transmission electron microscopy (TEM, TECNAI G2 20 U-TWIN), XPS (AXISULTRA DLD-600W) and X-ray diffraction using Cu-Kα radiation (λ=1.5418 Å) (XRD, Philips X' Pert Pro). The mass loading was measured using a microbalance (CPA225D, Sartorius). All electrochemical performance were performed by the ECLab and CHI660E instruments.

Results and Discussion

The synthetic strategy for the various porous bimetal–organic framework nanosheet arrays is schematically depicted in Figure 1. Briefly, the BDC and different bimetallic precursors were added into ethanol and deionization water, then a nickel foam was put into the solution with sonicating for about 30 min. After reacting at 130°C for 2 h in a 50 ml Teflon-lined autoclave, Ni derived MOF and various Ni-Co, Ni-Cu, Ni-Zn, Ni-Fe, and Ni-Mn bimetal MOFs were gradually formed by coordination bonds between metal atom nodes and organic ligands with periodic structural units (Zhao et al., 2016). In this bimetallic MOF structure, six O atoms co-formed the octahedron of Ni and Cu atoms. Four of the six O atoms from carboxylates or hydroxyls and two of them form the other one. Then, the octahedral structure will be connected in the direction of [010] on the (200) lattice plane in the form of edges/angles, finally forming a two-dimensional bimetallic layer separated by BDC molecules. The corresponding bimetallic precursors including Ni(NO₃)₂·6H₂O, Co(NO₃)₂·6H₂O, Cu(NO₃)₂·3H₂O, Zn(NO₃)₂·6H₂O, Mn(NO₃)₂·4H₂O, and Fe(NO₃)₃·9H₂O. Meanwhile, the hydrolysis controlled ion exchange and etching process (Ni²⁺ + 2H₂O = Ni(OH)₂ + 2H⁺, where the H⁺ will etch the MOF to create central void space) contribute to the germination of highly porous 2D arrays nanostructure (Guan et al., 2017).

FIGURE 1

Figure 1. (A) A schematic diagram of growing bimetallic MOFs on pure nickel foam. (B) An enlarged structure diagram of a branch on nickel foam. (C) The schematic diagram of Ni, Cu-MOFs.

Subsequently, we characterize the morphological and compositional features of the Ni,Cu-MOF sample with scanning electron microscopy (SEM) and transmission electron microscopy (TEM). The Ni,Cu-MOF sample after reaction becomes blue, which suggestes that a metathesis between the Cu²⁺ cations and the Ni²⁺ cations in the MOF framework and a coating on nickel foam (Figure S1). As shown in Figures 2a,b, the nanosheet arrays are uniformly coated on nickel foam with a large area. The TEM image of the powder further indicates the porous structures on nanosheets (Figure 2c). It corresponds to the Brunauer–Emmett–Teller (BET) surface areas of 178.87 m² g⁻¹ (Figure S2). In order to observe the distribution of different elements, the Energy-dispersive X-ray spectroscopy (EDS) elemental mapping was conducted (Figure 2d). The corresponding mapping images show the homogeneous distribution of Ni and Cu. The mole ratio of Ni:Cu is about 1.5, which is further confirmed by the inductively coupled plasma mass spectrometry (ICP-MS). These results indicate the successful preparation of Ni,Cu-MOF. Additionally, we may readily control the composition of the resulting porous bimetal organic framework nanostructures. Following a similar process, Ni-Co, Ni-Zn, Ni-Fe and Ni-Mn bimetal MOFs were gradually formed, which were all nanosheet arrays uniformly coated on nickel foams (Figure S3).

FIGURE 2

Figure 2. SEM images of (a,b) Ni,Cu-MOF coated nickel foam. (c) TEM image of the porous Ni,Cu-MOF nanosheet. (d) EDS elemental mapping scanning from TEM for the corresponding nanpsheet.

To explore the crystal structure and surface states of products, we applied the X-ray diffraction (XRD), X-ray photoelectron spectroscopy (XPS) and Raman analyses. Figure 3A shows all XRD patterns for Ni-MOF, Ni,Co-MOF, Ni,Cu-MOF, Ni,Zn-MOF, Ni,Fe-MOF, and Ni,Mn-MOF samples, revealing that the products are isostructural to the previously reported Ni-based MOFs (No. 985792) (Mesbah et al., 2014; Zhao et al., 2016). As shown in the magnification of the XRD patterns, the 2θ value of the (200) diffraction peaks clearly shift toward smaller diffraction angles with an increase in the lattice size (Figure S4). This phenomenon may result from the larger atom radius of Co (1.16 Å), Cu (1.17 Å), Zn (1.25 Å), Fe (1.17 Å), Mn (1.17 Å) than that of Ni (1.15 Å). Meanwhile, the lattice size of Ni,Zn-MOF has the largest change, which is matched with the biggest atomic radius. Furthermore, with the introduction of Cu element, the diffraction peaks of the Ni,Cu-MOF are still identical to the Ni-MOF, suggesting the Cu²⁺ partly substituted for Ni²⁺ in the metal–organic frameworks could retain the Ni-MOF crystal structure (Brozek and Dincǎ, 2013; Sun et al., 2015). In addition, XPS is used to probe the surface chemical valence. The survey spectrum of Ni,Cu-MOF shows the coexistence of Ni, Cu, O and C atoms with an elemental composition of Ni:Cu close to 1.46 (oxygen may be caused by the exposure of product in the air) (Figure S5), matching well with the ICP-MS result discussed above. Compared with the common Ni⁰ peaks at 853 eV and 870 eV of nickel foam (Figure S6) (Wang R. et al., 2018), the additional characteristic Ni²⁺, Ni³⁺ peaks and two shakeup satellites of Ni,Cu-MOF are fitted with two spin-orbit doublets and confirm the successful formation of nickel oxides upon the reaction process (Figure 3B) (Yuan et al., 2012). It can be seen that the Ni²⁺ peaks shift to a higher binding energy compared to Ni-MOF, indicating that partial electrons transfer from Ni²⁺ to Cu²⁺. The addition of copper can enhance the valence state of nickel, and the higher valence state of Ni (referred to as Ni^*) atoms have a strong ability to accept electrons, which is corresponds to the previous reports (Burke et al., 2015; Zhao et al., 2016; Li et al., 2017). The peaks centered at 935.2 and 955.7 eV can be assigned to the Cu 2p_3/2 and Cu 2p_1/2 (Figure 3C). Additionally, the typical core level O 1s XPS spectra of the Ni,Cu-MOF is displayed in Figure 3D. The peak at 529.6 eV is typical metal–oxygen bonds, and the peaks at 531.3 and 531.8 eV correspond to the defects with surface oxygen and adsorbed water, respectively (Guan et al., 2017). In addition to verifying this bimetal strategy is applicable to the preparation of other metal organic frameworks, we following synthesize different bimetal MOFs including Ni,Co-MOF, Ni,Zn-MOF, Ni,Fe-MOF, and Ni,Mn-MOF.

FIGURE 3

Figure 3. (A) The XRD patterns of Ni-MOF, Ni,Co-MOF, Ni,Cu-MOF, Ni,Zn-MOF, Ni,Fe-MOF, Ni,Mn-MOF and the standard pattern, respectively. (B–D) High-resolution XPS spectra of Ni 2p, Cu 2p, and O 1s.

Based on the uniform 2D arrayed porous bimetal organic framework nanostructures, it can not only provide high surface area, good electrical conductivity and short ion diffusion length, but also ensure high active site, making it a very promising electrode material for energy storage applications. The electrochemical properties of nickel foam, Ni-MOF, Ni,Cu-MOF, Ni,Co-MOF, Ni,Zn-MOF, Ni,Fe-MOF and Ni,Mn-MOF electrodes were firstly tested in a three-electrode system using a 1 M KOH aqueous solution as the electrolyte, a Pt plate as the counter electrode, and a Ag/AgCl as the reference electrode. As shown in the cyclic voltammograms (CV) curves in the potential range from 0 to 0.6 V at a same scan rate of 10 mV s⁻¹, in addition to the nickel foam has little performance (Figure S7), others all exhibit obvious redox reactions between Ni²⁺ and Ni³⁺ with OH⁻ (Figure 4A) (Guan et al., 2016). It can be seen that the bimetal MOF electrodes exhibited much higher current density than that of the Ni-MOF electrode, indicating that the capacity can be greatly improved by homogeneous bimetal hybridity. Figure 4B comparatively shows the typical charge and discharge curves of all samples at 2 mA cm⁻², where all curves show characteristic charge and discharge plateaus at 0.25 V~0.35 V and 0.3 V~0.35 V, respectively. The smallest difference value of the charging and discharging platforms of Ni,Cu-MOF indicates the least polarization and good reversibility, which is conducive to its cyclic stability (Figure S8). Conversely, the values of Ni,Zn-MOF and Ni,Mn-MOF are relatively large and resulting in their poor cyclic stability. Impressively, Ni,Cu-MOF and Ni,Zn-MOF all reach a remarkable high capacity of 1.8 and 2.0 C cm⁻² at 0.5 mA cm⁻² (Figure 4C). When the current density increased from 1 to 80 mA cm⁻², the Ni,Cu-MOF electrode could retain a capacity of 53.0%, indicating that the Ni-Cu bimetal based cathode had a good rate capability. Compared with valuable areal capacity due to the support of nickel foam, specific capacity evaluated by mass loading is also important. As shown in Figure S9, the Ni,Cu-MOF and Ni,Zn-MOF show the maximum specific capacity of 1,837 and 2,086 C g⁻¹ at 0.5 A g⁻¹. All details of CV curves at different scan rates and GCD curves at different current density of Ni-MOF, Ni,Co-MOF, Ni,Cu-MOF, Ni,Zn-MOF, Ni,Fe-MOF, Ni,Mn-MOF samples are shown in Figures S10–S15. Additionally, cycling stability is another one of the key parameters of batteries. The Ni,Zn-MOF electrode shows a drastic capacity decay of 70% over 1,500 cycles, while the Ni,Cu-MOF electrode shows a gradual increase at the beginning and an overall decay of 6% over 5000 cycles (Figure 4D). In order to explain this phenomenon, the electrode of Ni,Zn-MOF after reaction was characterized by SEM in Figure S16. The electrode structure is no longer a porous nanosheet arrays, and the collapsed structure directly affects the cycling stability. Additionally, the increase in capacity during the initial cycling stage is likely due to activation of the active materials (Kim et al., 2015). The SEM images of other electrodes after cycling test showed that the hierarchical structure were well maintained, which further confirming the excellent cycling behavior (Figure S17). Compared with the poor cycling stability of Ni-MOF, these results suggest that bimetal strategy is benefit to the stability of metal organic frameworks for batteries.

FIGURE 4

Figure 4. (A) CV curves of the Ni foam, Ni-MOF, Ni,Co-MOF, Ni,Cu-MOF, Ni,Zn-MOF, Ni,Fe-MOF, and Ni,Mn-MOF, respectively. (B) Charge–discharge curves at 2 mA cm⁻². (C) Rate performance of all samples. (D) Cycling performance collected for 2,500 cycles.

To further probe the application of the robust Ni,Cu-MOF anode material, a full cell was assembled with a commercial Zn plate as cathode material (denoted as Ni,Cu-MOF//Zn). Figure 5A shows the CV curves of the Zn plate and Ni,Cu-MOF electrodes at 0.2 and 2 mV s⁻¹ in 1 M KOH and 0.02 M Zn(Ac)₂ electrolyte, where both electrodes are composed of a pair of strong redox peaks. Consequently, the full cell was assembled and two typical CV curves were displayed in Figure 5B. A pair of reduction and oxidation peaks were observed at ≈1.75 and ≈1.95 V, respectively. The representative galvanostatic discharge (GD) curves of the full cell collected at different current densities were illustrated in Figure 5C, revealing its superior electrochemical performance with a discharge plateau at ≈1.7 V with negligible voltage hysteresis even under 40 mA cm⁻². Moreover, the typical voltage–capacity curves of the Ni,Cu-MOF//Zn battery and Ni foam//Zn battery at 20 mA cm⁻² were presented in Figure 5D. As expected, the Ni,Cu-MOF//Zn battery discharge plateau was longer and the capacity of 0.55 mA h cm⁻² was higher. The coulombic efficiency of the Ni,Cu-MOF//Zn battery was 99.3%, demonstrating that the electrochemical property was improved obviously. The high-rate performance of the Ni,Cu-MOF//Zn battery was further evaluated in Figure 5E. The obtained cell showed a stable high-rate characteristic, and the capacities were ranging from 0.807 mA h cm⁻² at 2 mA cm⁻² to 0.432 mA h cm⁻² at 40 mA cm⁻². When the current density was suddenly recovered to 10 mA cm⁻² after 30 cycles, the average capacity of this battery could be restored to 0.607 mA h cm⁻², proving its good electrochemical reversibility. One of the main bottlenecks of aqueous rechargeable batteries is the inferior cycle stability. Based on the rapid ion/mass transport by porous 2D arrays and highly reversible redox behavior by bimetal incorporation, the Ni,Cu-MOF//Zn battery could still retain 92% of its original capacity after 2500 cycles and the coulombic efficiency during charging/discharging process was close to 99% (Figure 5F). The discharge curves of the Ni,Cu-MOF//Zn battery compared with the original profile after cycling for 2500th were shown in the inset of Figure 5F. The little attenuation of capacity clarified the good compressibility and a great promise for energy storage devices.

FIGURE 5

Figure 5. (A) Comparison of CV curves of Ni,Cu-MOF anode and Zn cathode at 0.2 and 2 mV s⁻¹, respectively. (B) CV curves of full cell with the charge–discharge densities changed from 2 to 40 mA cm⁻². (C) Galvanostatic discharge profiles of the Ni,Cu-MOF//Zn at different current densities from 2 to 40 mA cm⁻². (D) Charge–discharge curves of Ni,Cu-MOF//Zn and nickel foam//Zn batteries at 20 mA cm⁻². (E) Long-term stability and reversibility of Ni,Cu-MOF//Zn battery with the charge–discharge densities changed from 2 to 40 mA cm⁻². (F) Cycling performance of the Ni,Cu-MOF//Zn battery collected for 2,500 cycles. The inset is the comparison of discharge curves after 1st to 2500th cycles.

The energy density and power density are two important parameters for describing electrochemical performance of Ni,Cu-MOF//Zn battery (Wu et al., 2019; Liu et al., 2020). As revealed in Figure 6A, the as-fabricated Ni,Cu-MOF//Zn battery exhibited a maximum voluminal energy density of 71.23 mWh cm⁻³ at a power density of 3530.61 mW cm⁻³, which outperforms most reported asymmetric supercapacitors and aqueous electrolyte-based batteries, such as hVCNT2//hVCNT2 (41 mWh cm⁻³) (Wu et al., 2016), FGN-300//FGN-300 (27.2 mWh cm⁻³) (Yan et al., 2014), SANF//Zn (15.1 mWh cm⁻³) (Wang R. et al., 2018), CNTs//Fe₃O₄-C (1.56 mWh cm⁻³) (Li R. et al., 2015), NiCo//Zn (8 mW h cm⁻³) (Huang et al., 2017). Additionally, the areal energy density of 1.40 mWh cm⁻² at a power density of 59.2 mW cm⁻² is also consistently high when compared with other researchs like SANF//Zn (0.754 mWh cm⁻²) (Wang R. et al., 2018), Zn//Co₃O₄ (0.97 mWh cm⁻²) (Wang et al., 2016), NiAlCo LDH/CNT//Zn (0.27 mWh cm⁻²) (Gong et al., 2014), CC-CF@NiO//CC-CF@ZnO (0.22 mWh cm⁻²) (Liu et al., 2016), Zn//MnO₂ (0.06 mWh cm⁻²) (Pan et al., 2016), SWNT/rGO//SWNT/rGO (0.03 mWh cm⁻²) (Yu et al., 2014) and CF@NiO//CF@Fe₃O₄ (0.006 mWh cm⁻²) (Guan et al., 2016) (Figure 6B).

FIGURE 6

Figure 6. Ragone plots of the device based on (A) the volume and (B) the area of the device. The values reported from other electrochemical energy storage devices are included for comparison.

Conclusion

In conclusion, a new one-step approach to fabricate porous bimetal organic framework nanosheet arrays nanostructures were successfully applied for stable energy storage. Due to the synergetic effect of bimetal incorporation and 2D arrayed nanostructures topology, the charge transfer between the dopants and the host metal atoms and rapid ion/mass transport can significantly enhance the electrochemical properties and stability. For aqueous recharge-able Ni–Zn battery applications, the outstanding performance of Ni,Cu-MOF//Zn battery which achieved a maximum energy density of 71.23 mW h cm⁻³ (1.40 mW h cm⁻²) and a maximum power density of 3,530.61 mW cm⁻³ (59.2 mW h cm⁻²) in 1 M KOH electrolyte indicates the importance of homogeneous bimetallic MOF topology. Remarkably, the Ni,Cu-MOF//Zn could provide promising cycling durability with about 92% capacity retention after 2,500 cycles. This bimetal organic frameworks derived strategy may open up new opportunities for the rational design of homogeneous porous nanostructures and stable energy storage device.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation.

Author Contributions

JW conceived the study designed the experiments, performed the experiments work, and wrote the manuscript. WX and BW perfected the revision of the manuscript. JL, ZX, and DT performed the SEM and TEM testing. YX analyzed the structure data. All authors approved the manuscript for publication. All authors contributed to the article and approved the submitted version.

Funding

This work was financially supported by the National Natural Science Foundation of China (51773158, 61971211), the Program for Youth Scholar Teachers Supporting Plan in Universities of Henan Province (2018GGJS157), the National Project Cultivation Plan (193137), and the Hubei Key Laboratory of Biomass Fiber and Ecological Dyeing and Finishing Open Fund (184083027).

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.

Acknowledgments

The authors thank to the facility support of the State Key Laboratory for Hubei New Textile Materials and Advanced Processing Technology and the Analysis and Testing Center of Wuhan Textile University.

Supplementary Material

The Supplementary Material for this article can be found online at: https://www.frontiersin.org/articles/10.3389/fmats.2020.00194/full#supplementary-material

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