Flexible and Stable N-Isopropylacrylamide/Sodium Alginate Gel Electrolytes for Aqueous Zn-MNO₂ Batteries

Abstract

Rechargeable aqueous Zn-ion batteries (ZIBs) have attracted considerable attention owing to their high theoretical capacity of 820 mA h g⁻¹, low cost and intrinsic safety. However, the electrolyte leakage and the instability issues of Zn negative electrodes originating from side reactions between the aqueous electrolyte and Zn negative electrode not only restrict the battery stability, but also result in the short circuit of aqueous ZIBs. Herein, we report a flexible and stable N-isopropylacrylamide/sodium alginate (N-SA) gel electrolyte, which possesses high mechanical strength and high ionic conductivity of 2.96 × 10⁻² S cm⁻¹, and enables the Zn metal negative electrode and MnO₂ positive electrode to reversibly and stably cycle. Compared to the liquid electrolyte, the N-SA hydrogel electrolyte can effectively form a uniform Zn deposition and suppress the generation of irreversible by-products. The assembled symmetric Zn/Zn cells at a current density of 1 mA cm⁻² (capacity: 1 mAh cm⁻²) show a stable voltage profile, which maintains a low level of about 100 mV over 2600 h without an obvious short circuit or any overpotential increasing. Specially, the assembled Zn/N-SA/MnO₂ batteries can deliver a high specific capacity of 182 mAh g⁻¹ and maintain 98% capacity retention after 650 cycles at 0.5 A g⁻¹. This work provides a simple method to fabricate high-performance SA-based hydrogel electrolytes, which illustrates their potential for flexible batteries for wearable electronics.

1. Introduction

With the development of wearable devices and electric vehicles, there is a high demand for sustainable energy storage systems. Lithium-ion batteries (LIBs) are currently being extensively studied due to their high energy density, wide electrochemical window and long cycle life [1]. However, because of the limited resources of lithium and the high cost, toxicity and flammability of organic electrolytes, LIBs assembled with organic electrolytes result in environmental pollution and poor safety performance. Also, the use of organic liquid electrolytes has inevitable leakage, poor flexibility, etc. [2]. Compared to organic electrolyte systems, aqueous rechargeable batteries are expected to be used on a large scale in the energy storage field due to their low production cost, environmental friendliness and high safety performance [3]. In recent years, various aqueous batteries with multivalent metal ions (Zn²⁺, Mg²⁺, Ca²⁺ and Al³⁺) have been widely reported [4]. Among them, the reserves of metallic Zn are 300 times than that of Li in the lithosphere. Aqueous zinc ion batteries (ZIBs) possess high theoretical specific capacity (820 mAh g⁻¹ or 5854 mAh cm⁻³) [5], low toxicity, low fabrication cost, low redox potential (−0.76 V) [6] and inherent safety. However, current aqueous zinc ion batteries have a series of problems during their long cycle life, such as the corrosion of the negative Zn electrode [7] and the formation of Zn dendrites [8]. Zn dendrites might even cause the separator to be punctured [9] and then easily induce a short circuit inside batteries [10]. There are extensive research efforts on improving their cycling stabilities, for example, through interfacial modifying the zinc negative electrode and optimizing the electrolyte formulation and hydrogel electrolytes [11]. Hydrogels are composed of polymers with hydrophilic functional groups, which promote water storage and structural integrity through weak physical hydrogen bonding. Meanwhile, polymer gel electrolytes act both as an electrolyte and as a separator, which can effectively avoid electrolyte leaking. In addition, hydrogel gel electrolytes ensure close contact between the electrode and electrolyte, maintaining the integrity of the flexible ZIBs under external strain [12].

Presently, some hydrogel gel electrolytes reported are based on synthetic polymers, such as polyacrylamide (PAM) [13], polyvinyl alcohol (PVA) [14], and polyacrylic acid (PAA) [15], etc. Unfortunately, these hydrogels’ either poor mechanical strength or low ionic conductivity remains challenging. On the other hand, polymer hydrogels derived from natural matrices [16,17,18], such as sodium alginate (SA) [19], guar gum (GG) [20], xanthan gum (XG) [21] and gelatin [22], are cheap, biocompatible and hydrophilic, and widely used in flexible Zn-ion batteries. They are multiple-cross-linked internally by hydrogen, ionic and covalent bonds to obtain a stable three-dimensional network structure, which results in improving their mechanical properties and ionic conductivities. A classical development in ZIBs hydrogel gel electrolytes is the use of sodium alginate (SA) as a polymer matrix to form a hierarchically three-dimensional Zn²⁺-conductor gel electrolyte. SA consists of two monomer units, β-D-mannuronic acid (M-block) and α-L-guluronic acid (G-block) [23]. Because of SA possessing a high concentration of polar groups, high modulus and easy cross-linking with Zn²⁺, many strategies based on natural polysaccharide-SA, such as guar gum/SA/glycol [24], SA-polyacrylamide [25] and gelatin/SA [26], have been proposed to construct high-performance ZIBs hydrogel gel electrolytes. These SA-based hydrogels exhibit high mechanical strength but they suffer from toxic raw materials [27], invoking inert crosslinker initiators [28] and a complex preparation process [29].

Hence, in this work, we prepare a flexible and stable N-isopropylacrylamide (NIPAM)/sodium alginate ZIBs hydrogel gel electrolytes (noted as N-SA) via a simple chain entanglement method. We directly incorporate NIPAM into the SA hydrogel to further enhance its mechanical strength and ionic conductivity. By soaking in 4 mol L⁻¹ (M) ZnSO₄ and 0.1 M MnSO₄ aqueous solution, the chain entanglements of short-chain NIPAM were formed. During the soaking process, Zn²⁺, Mn²⁺ and SO₄²⁻ ions could penetrate into the N-SA hydrogel matrix and give it the high conductivity of the N-SA hydrogels. Thus, due to NIPAM chain entanglements, the N-SA hydrogels show a high conductivity of 2.96 × 10⁻² S cm⁻¹ at room temperature, and this hydrogel can effectively form a uniform Zn deposition and suppress side reactions. of particular note, the assembled Zn/N-SA/MnO₂ batteries can deliver 182 mAh g⁻¹ (~98% retention) at their highest capacity at a current density of 0.5 A g⁻¹ after 650 cycles (see Table S1). Therefore, this work provides a simple method to fabricate high-performance SA-based hydrogel electrolytes, which illustrates their potential for flexible batteries for wearable electronics.

2. Experimental Methods

2.1. Materials

Sodium alginate (SA, M = 398.31 g mol⁻¹, AR, >99%) and ZnSO₄·7H₂O (ACS, 99%) were purchased from Aladdin Chemical Reagent Co., Ltd. (Shanghai, China) MnSO₄·H₂O (AR, 99%), N-isopropylacrylamide (NIPAM, AR, >99%) and ammonium chloride (NH₄Cl, AR, 99%) were purchased from Macklin Chemical Reagent Co., Ltd. Potassium permanganate (KMnO₄, AR, 99%) was also purchased from Macklin Chemical Reagent Co., Ltd. (Shanghai, China) All chemicals were used directly with no purification treatment.

2.2. Preparation of α-MnO₂ Powders

The α-MnO₂ powder was prepared according to the literature method [30]. The general experimental process was as follows: KMnO₄ and NH₄Cl were subsequently completely dissolved in deionized water and then mixed homogeneously. Then, the solution was placed in a Teflon-lined reactor under hydrothermal conditions at 140 °C for 24 h. The obtained powder was filtered, washed with plenty of water, and dried.

2.3. Preparation of Electrolytes

The sodium alginate (SA) and NIPAM-SA (N-SA) hydrogel electrolyte was prepared using a uniform casting method and subsequently soaked in 4 mol L⁻¹ (M) ZnSO₄ and 0.1 M MnSO₄ aqueous solution. Briefly, 1.2 g SA (or 1.2 g SA and 0.15 g NIPAM) were dissolved into 30 mL deionized water and stirred at 60 °C for 0.5 h. The as-prepared homogeneous composite solution was then poured into a glass pane and then immersed in the electrolyte solution of 4 M ZnSO₄ + 0.1 M MnSO₄ for 0.5 h. The resulting composite gels were noted as SA and N-SA, respectively.

2.4. Preparation of Electrode and Battery Assembly

MnO₂ electrodes included 70 wt.% of α-MnO₂ powders, 20 wt.% of Super P (SP), and 10 wt.% of carboxymethyl cellulose (CMC). The current collector was the Ti foil. The active mass loading of the MnO₂ electrodes was ~1.5 mg cm⁻². For the liquid electrolyte, the 2032 coin-cell was prepared to measure the electrochemical performances, the positive electrode was MnO₂, the negative electrode is Zn, separator was Whatman glass fiber, and the amount of liquid electrolyte used, consisting of of 4 M ZnSO₄ and 0.1 M MnSO₄, was about 0.03 mL. For the SA and N-SA gel electrolytes, the 2032 coin-cell was also prepared to measure the electrochemical performances, the positive electrode was MnO₂, the negative electrode was Zn, and SA and N-SA gel electrolytes were used as both electrolyte and separator, respectively. All 2032 coin-cells were directly assembled in air.

2.5. Characterizations

A Fourier transform infrared spectrometer (FTIR, Nicolet 6700, Thermo Fisher Scientific, Carlsbad, US) was used to characterize the samples. The micrometer was used for measuring the thickness of the N-SA hydrogel electrolyte. A field-emission scanning electron microscope (SEM, S4800, Hitachi, Tokyo, Japan) was employed to determine the morphology of gel electrolytes and electrodes. X-ray diffraction (XRD, D8 DISCOVER, Bruker, Germany) was used to character the surface of negative Zn electrodes.

Linear scanning voltammetry (LSV), electrochemical impedance spectroscopy (EIS), corrosion tests, and cyclic voltammetry (CV) were carried out on an electrochemical workstation (CHI 660E, Shanghai Chenhua Instrument Co., Ltd., Shanghai, China). The EIS measurements were tested in the frequency range of 10 mHz to 10 kHz with an oscillation amplitude of 5 mV. Galvanostatic charge–discharge (GCD) and rate performance measurements were performed on a CT3001A Land battery testing system (Wuhan Land Electronic Co., Ltd., Wuhan, China). EIS measurements were used to calculate the ionic conductivity (σ) of the electrolytes through stainless steel (SS)||electrolyte||SS symmetrical coin cells according to the reported reference method [31]. LSV curves were measured using a SS||electrolyte||Zn coin cells at a scan rate of 1 mV s⁻¹ to investigate the electrochemical window of the electrolytes. CV curves of Zn||electrolyte||MnO₂ asymmetrical coin cells were obtained at a scan rate of 1 mV s⁻¹.

3. Results and Discussion

The preparation process of the N-SA gel electrolyte is shown in Figure 1a. The N-SA aqueous solution was a transparent and homogeneous viscous liquid with disordered molecular chains. After adding 4 M ZnSO₄ + 0.1 M MnSO₄ solution into N-SA aqueous liquid solution for 30 min, the N-SA gel electrolyte with cross-linked structures was formed online through the Zn²⁺ coordinating function [24]. Figure 1b shows an optical image of a uniform N-SA electrolyte, which is transparent and has excellent flexibility. The N-SA gel electrolyte can be bent at any angle and has a thickness of 325 μm, as shown in Figure 1c. The FTIR spectra of the SA and N-SA hydrogel electrolyte, as well as pure SA and NIPAM powder, were collected as shown in Figures S1 and S2. For the pure SA, the absorption bands at 1590 cm⁻¹ and 1401 cm⁻¹ are attributed to the asymmetric stretching vibrations and symmetric stretching vibrations of -COO⁻ groups on the SA chains, respectively. In contrast, for the SA and N-SA hydrogel electrolyte, these two bands shift to higher values because of coordinate bonds between -COO⁻ groups and Zn²⁺ [19]. Bands were observed in the spectra of NIPAM at 532 cm⁻¹ and 1517 cm⁻¹, which were ascribed to the -NH wagging vibration and the C=O stretching vibration, respectively [32]. For the N-SA hydrogel, these similar characteristic bands also appeared, which suggests the presence of NIPAM. The surface morphology of the N-SA gel electrolyte has uniformity and is even (Figure 1d). As determined by the cross-sectional morphology (Figure 1e), the thickness of the N-SA gel electrolyte is 60 μm, which is lower than the thickness measured using a micrometer. The reason for this is that the sample of SEM images is dried through freezing treatment.

Figure 2a shows the EIS spectra of stainless steel (SS)/SS symmetrical batteries with the SA and N-SA gel electrolyte at room temperature. The corresponding ionic conductivity was calculated by the reported method [33]. Notably, the N-SA gel electrolyte shows a high ionic conductivity of 2.96 × 10⁻² S cm⁻¹, which is higher than that of the SA gel electrolyte. LSV tests were conducted to evaluate the electrochemical stability of the electrolyte. As shown in Figure 2b, the oxidation potential of the N-SA gel electrolyte is 2.51 V (vs. Zn²⁺/Zn). The LSV curve of the cells with the N-SA gel electrolyte also exhibits a reduction potential of (−0.15 V vs. Zn²⁺/Zn), which is lower than that of cells with liquid electrolyte (−0.094 V vs. Zn²⁺/Zn). These LSV results suggest that the N-SA gel electrolyte has a wide electrochemical window. In addition, we tested the CV curves of Zn/Zn symmetric cells at 1 mV s⁻¹, as shown in Figure S3. The nucleation overpotential of Zn²⁺ in the N-SA hydrogel electrolyte is greater than that in the liquid electrolyte. The larger nucleation overpotential indicates a smaller nucleation radius, implying an easier homogeneous deposition [34]. This demonstrates that the N-SA gel electrolyte is beneficial for small, denser and homogeneous Zn deposition [35]. Furthermore, the Tafel curve was used to measure the corrosion of Zn foil in the electrolyte, as shown in Figure 2c. Compared to the liquid electrolyte, the corrosion potential of zinc with the N-SA gel electrolyte is increased from −0.0084 to 0.0177 V, and the corrosion current of zinc with the N-SA gel electrolyte is decreased from −5.984 to −5.286 A. Higher corrosion potentials and lower corrosion currents indicate a smaller tendency for corrosion reactions and lower corrosion rates, respectively [36].

The Zn/Cu asymmetric cells with different electrolytes were used to study the cycling stability of zinc plating/stripping in this work. As shown in Figure 3a–c, we compare the voltage/capacity curves of Zn/Cu of the N-SA, SA hydrogel electrolyte and liquid electrolyte for different numbers of cycles. For the N-SA cells cycled at 1 mA cm⁻², the discharge/charge behavior remained the same over 500 cycles. However, the voltage profile of cells with the liquid electrolyte increased during both the discharge and charge process. This means that the polarization potential of the N-SA hydrogel electrolyte was considerably lower than those of the liquid electrolyte and SA hydrogel electrolyte. The low polarization potential of zinc plating/stripping in the N-SA hydrogel electrolyte is beneficial for the uniformity of zinc deposition [37]. Notably, the coulomb efficiency (CE) is a crucial parameter for investigating the reversibility and stability of the zinc negative electrode [38]. As shown in Figure 3d, the coulombic efficiency of the N-SA hydrogel cell increases from 86% in the first cycle to 98% after 20 cycles and remains stable at 99% for subsequent cycles. Meanwhile, the Zn/Cu cell with the N-SA hydrogel electrolyte can be stably cycled at 1 mA cm⁻² for more than 500 cycles. In contrast, the CE of Zn/Cu cells with the liquid electrolyte and SA hydrogel electrolyte quickly decreases to 0 after 83 and 200 cycles, respectively. The high and stable coulombic efficiency of the N-SA cell is probably because the side reactions and dendrite growth are significantly restrained. Figure 3e,f shows SEM images of Cu foils after Zn deposition for 5 h at 2 mA cm⁻² in the Zn/Cu asymmetric cells with the N-SA hydrogel electrolyte and liquid electrolyte. For the liquid electrolyte, as shown in Figure 3f, a large number of micron-grade dead Zn particles with irregular shapes appear on the surface of Cu, which is adverse for a high plating/stripping efficiency. Also, in the SEM picture in Figure 3f there are some filaments that are likely to be glass fibers from Whatman. By contrast, the Zn is deposited uniformly and smoothly in the N-SA hydrogel electrolyte, as shown in Figure 3e. Therefore, this N-SA hydrogel electrolyte indicates a homogeneous nucleation process of zinc deposition.

The long-term cycling property of the symmetric Zn/Zn cells with the N-SA hydrogel electrolyte and liquid electrolyte at a current density of 1 mA cm⁻² is shown in Figure 4a–c. The cell with N-SA hydrogel electrolyte shows a stable voltage profile, which maintains a low level of about 100 mV over 2600 h without an obvious short circuit or any overpotential increasing. In contrast, the cell with the liquid electrolyte exhibits a sudden increase in polarization during the cycling process. This indicates that the N-SA hydrogel electrolyte possesses a stable Zn stripping/plating process. Furthermore, the voltage profiles of the Zn/Zn symmetrical cell with the N-SA gel electrolyte and liquid electrolyte were investigated for different current densities from 0.1 to 2.0 mA cm⁻², as shown in Figure 4d. When the current density increased from 0.1 mA cm⁻² to 2.0 mA cm⁻², the polarization voltages of the N-SA cells are always below 200 mV. However, the symmetric Zn cell with the liquid electrolyte suffer from poor voltage curves. This suggests that the N-SA gel electrolyte is a promising candidate for ZIBs at high current densities. The XRD patterns of the Zn negative electrode collected from the N-SA cells after 30 cycles display similar signals compared to those of fresh Zn foils (Figure 4e). However, in the XRD patterns of the Zn negative electrode cycled in the liquid electrolyte appear several new obvious peaks located at 8.2°, 16.3° and 24.5° (2θ). These peaks suggest the formation of Zn₄SO₄(OH)₆·5H₂O (PDF#69-0688). This indicates that the N-SA hydrogel significantly inhibits interfacial side reactions, reduces the production of “dead” zinc, and results in a highly reversible and efficient plating/stripping of zinc ions.

Electrochemical performance of Zn/MnO₂ cells with the N-SA, SA hydrogel electrolyte and liquid electrolyte at 25 °C was shown in Figure 5. Figure 5a shows the CV curves of the cells with the N-SA hydrogel electrolyte at 0.1 mV s⁻¹ in the voltage range of 0.9~1.9 V at room temperature. The first cycle shows a single reduction peak at approximately ~1.17 V, while two reduction peaks at ~1.34 and ~1.22 V appear in the following cycles. The change in the peak number and position is attributed to the phase transition and morphology evolution during the first cycle [39]. In the oxidation reaction, two overlapped peaks at 1.59 and 1.62 V are observed. This indicates a Zn²⁺ insertion and extraction process in the charge storage mechanism [40]. In addition, the CV curves in the second and third cycles nearly overlap, suggesting the electrochemical reversibility of the cells [41]. As displayed in Figure 5b, c, the Zn/MnO₂ cells with the N-SA hydrogel electrolyte exhibit reversible capacities of 310, 266, 176 and 104 mAh g⁻¹ at current densities of 0.1, 0.2, 0.5 and 1 A g⁻¹, respectively. When the current density decreases back to 0.5 mA cm⁻², the capacities immediately recover to 180 mAh g⁻¹. Thus, the cell with the N-SA hydrogel electrolyte exhibits a good rate performance. Long-term cycling stabilities of the Zn/MnO₂ cells with the N-SA, SA hydrogel electrolyte and liquid electrolyte at 0.5 A g⁻¹ are shown in Figure 5d. The Zn/MnO₂ cells with the N-SA hydrogel electrolyte maintain superior cycling stability compared to the cells in the SA and liquid electrolyte. The reversible capacities are 169, 171, 188, 185 and 182 mAh g⁻¹ after 10, 200, 400, 500 and 600 cycles (Figure S4), respectively. The N-SA cell even delivers a highly reversible capacity of 182 mAh g⁻¹ after 650 cycles, indicating a superior capacity retention of 98% and near 100% coulombic efficiency (Figure S5). This indicates that the N-SA hydrogel electrolyte possesses ultra-stable and highly reversible electrochemical performance during the long cycling, which may be ascribed to the uniform Zn reversible deposition.

After being charged back to 1.9 V after 300 cycles, the corresponding SEM images of two electrodes collected from Zn/MnO₂ cells are shown in Figure S6 and Figure 5e,f. As depicted in Figure S6, some flake-like deposits are observed on the surface of the MnO₂ electrode in the liquid electrolyte after 300 cycles. In contrast to this flake-like surface, the MnO₂ surface collected from the N-SA hydrogel electrolytes remains relatively clean without any obvious flakes after cycling. Furthermore, as shown in Figure 5e,f, the SEM images of Zn electrodes are collected from Zn/MnO₂ cells with the N-SA hydrogel electrolyte and liquid electrolyte after 300 cycles. The corresponding SEM images of Zn electrodes cycled after 500 cycles are also displayed in Figure S7. It can be seen that after cycling in the liquid electrolyte, the uneven Zn surface with a large number of sheet-like dendrites and by-products was observed, which may be due to the interfacial degradation of Zn with liquid electrolyte. Conversely, after cycling with the S-NA hydrogel electrolyte, the surface of Zn electrode keeps very flat and uniform. Therefore, for the N-SA hydrogel electrolyte, the parasitic reaction between electrodes and electrolyte are effectively suppressed, which results in satisfactory long-term cycling stabilities of the assembled Zn/MnO₂ cells.

4. Conclusions

In summary, flexible and stable N-isopropylacrylamide (NIPAM)/sodium alginate ZIBs hydrogel gel electrolytes (noted as N-SA) are designed via a simple chain entanglement method. We directly incorporate NIPAM into the SA hydrogel to further enhance its mechanical strength and ionic conductivity. By soaking in 4 mol L⁻¹ (M) ZnSO₄ and 0.1 M MnSO₄ aqueous solution, the chain entanglements of short-chain NIPAM were formed. During the soaking process, Zn²⁺, Mn²⁺ and SO₄²⁻ ions could penetrate the N-SA hydrogel matrix and make the N-SA hydrogels highly conductive. Thus, due to NIPAM chain entanglements, the N-SA hydrogels show a high conductivity of 2.96 × 10⁻² S cm⁻¹ at room temperature. Compared to the liquid electrolyte, the N-SA hydrogel electrolyte can effectively form a uniform Zn deposition and suppress the generation of irreversible by-products. The assembled symmetric Zn/Zn cells at a current density of 1 mA cm⁻² show a stable voltage profile, which maintains a low level of about 100 mV over 2600 h without an obvious short circuit or any overpotential increasing. Of particular note, the assembled Zn/N-SA/MnO₂ batteries can deliver 182 mAh g⁻¹ (~98% retention) at their highest capacity at a current density of 0.5 A g⁻¹ after 650 cycles. Therefore, this work provides a simple method to fabricate high-performance SA-based hydrogel electrolytes, which illustrates their practical applications of aqueous ZIBs.