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Current Issue: 2021  Archive: 2020 2019
Open Access Original Research
High Energy Density Rechargeable Aqueous Lithium Batteries with an Aqueous Hydroquinone Sulfonic Acid and Benzoquinone Sulfonic Acid Redox Couple Cathode

Hironori Takagi , Koichi Kakimoto , Daisuke Mori , Sou Taminato , Yasuo Takeda , Osamu Yamamoto *, Nobuyuki Imanishi 

Graduate School of Engineering, Mie University, Tsu, Mie, 514-8507, Japan

Correspondence: Osamu Yamamoto

Academic Editor: Ahamed Irshad

Special Issue: Batteries: Past, Present and Future

Received: January 12, 2021 | Accepted: February 12, 2021 | Published: February 24, 2021

Journal of Energy and Power Technology 2021, Volume 3, Issue 1, doi:10.21926/jept.2101010

Recommended citation: Takagi H, Kakimoto K, Mori D, Taminato S, Takeda Y, Yamamoto O, Imanishi N. High Energy Density R echargeable Aqueous Lithium Batteries with an Aqueous Hydroquinone Sulfonic Acid and Benzoquinone Sulfonic Acid Redox Couple Cathode. Journal of Energy and Power Technology 2021;3(1):13; doi:10.21926/jept.2101010.

© 2021 by the authors. This is an open access article distributed under the conditions of the Creative Commons by Attribution License, which permits unrestricted use, distribution, and reproduction in any medium or format, provided the original work is correctly cited.


The demand for high energy density rechargeable batteries beyond lithium-ion batteries has increased for electric vehicles. In the present study, a novel high energy density rechargeable aqueous lithium battery was proposed. The battery was composed of a lithium metal anode, a lithium-stable non-aqueous electrolyte, a water-stable lithium-ion conducting solid electrolyte of Li1.4Al0.4Ge0.2Ti1.4(PO4)3-epoxy-TiO2 separator, and a hydroquinone sulfonic acid (HQS)/benzoquinone sulfonic acid (BQS) redox couple in an aqueous acetic acid solution (HAc). An open-circuit voltage of 3.7 V at 25 °C was recorded, and the theoretical energy density of the battery based on the reaction 2Li + BQS + 2H2O = 2 LiOH + HQS was 833 Whkg-1, about two times higher than that of the lithium-ion battery. The battery was successfully cycled at 0.5 mA cm-2 and 25 °C with low polarization.


High energy density battery; aqueous lithium battery; lithium metal electrode; benzoquinone sulfonic acid; solid electrolyte

1. Introduction

A lithium anode is the best candidate for a high energy density battery because of its high theoretical specific capacity of 3860 mAhg-1 and highest electrochemical reduction potential of -3.04 V in comparison to a normal hydrogen electrode (NHE). Lithium reacts vigorously with water; therefore, an aqueous electrolyte is never used, and non-aqueous electrolytes were mainly developed for batteries with lithium anodes [1,2]. In 2004, Visco et al. [3,4] proposed a unique aqueous lithium-air battery that consisted of a lithium metal anode, a water-stable lithium-ion conducting solid electrolyte separator, an aqueous electrolyte, and an air electrode. The electrolyte separator of NASICON-type Li1+xAlxTi2-x(PO4)3 (LATP) prevented direct contact between the lithium metal anode and the aqueous electrolyte solution. The aqueous lithium-air battery has been expected to give a high power density and to operate in an air atmosphere [5].

Mainly, two types of aqueous lithium batteries have been proposed in the literature; the one with an aqueous electrolyte and water-stable lithium intercalation electrodes [6], and the other with a water-stable solid electrolyte separator [3]. The former aqueous lithium battery exhibits a high power density; however, the specific energy density is lower than that of conventional lithium-ion batteries [7]. At present, various aqueous lithium batteries with solid electrolyte separators have been suggested. Zhou and co-workers reported a prototype aqueous lithium battery with a solid electrolyte separator [8]. This cell was assembled using 1 M LiClO4 in ethylene carbonate and dimethyl carbonate as an electrolyte for the Li anode and an aqueous solution containing 1 M LiOH and 1 M KOH as the electrolytes for the Ni(OH)2 cathode. The two electrolytes were separated by the LATP. The energy density of this cell was calculated as 857 Whkg-1 based on the weights of the electrode active materials. Similarly, a cell consisting of a lithium anode with a liquid electrolyte and water-soluble Fe(CN)63-/Fe(CN)64- redox couple cathode separated by LATP was proposed by Goodenough et al. [9]. The theoretical specific energy density of this redox couple was recorded as 392 Whkg-1, comparable to that of conventional lithium-ion batteries, although a higher power density was expected. Wu et al. reported a Li/gel-polymer electrolyte/LATP/aqueous electrolyte/LiMn2O4 cell [10]. The specific energy density of the Li/LiMn2O4 cell based on the mass of the electrodes was estimated to be 446 Whkg-1. Imanishi and co-workers [11,12,13] proposed a higher specific energy density aqueous lithium battery that consisted of a lithium anode with a liquid electrolyte, an aqueous MCl2 (M = Co, Ni, and Sn) solution catholyte, and a Li1.4Al0.4Ge0.2Ti1.4(PO4)3 (LAGTP) separator. The theoretical specific energy density of the Li/NiCl2 cell was as high as 1047 Whkg-1 based on the weights of lithium and NiCl2 and was at least twice of the conventional lithium-ion battery. The estimated specific energy density calculated using the mass of cell components with a 0.1 mm thick LAGTP separator (except packaging) was 670 Whkg-1. Moreover, it has been shown in the literature that the battery with a liquid-type catholyte could be developed into a large scale battery without the degradation in cell performance due to the high diffusibility of the active material in the catholyte [13].

In this study, we have developed a novel aqueous lithium rechargeable battery with a water-soluble organic redox couple catholyte of 1,2-hydroquinone-3-sulfonic acid (HQS) and 1,2-benzoquinone-3-sulfonic acid (BQS) and a lithium metal anode. Feng et al. [14] reported an organic cathode composed of 3,4,9,10-perylene-tetracarboxylic acid-dianhydride in an organic solvent, but the solubility of this compound in water was very low. Also, the catholyte and lithium metal anode were separated by LAGTP. The benzoquinone-hydroquinone couple is the prototypical example of an organic redox system, and their electrochemical behavior has been extensively studied for the past many years [15,16,17]. However, the solubility of benzoquinone in water is not very high. Narayanan et al. [18,19,20] reported an aqueous flow battery based on a water-soluble organic redox couple of 1,2-benzoquinone-3,5-disulfonic acid at the cathode and anthraquinone-2-sulfonic acid at the anode. A water-soluble aqueous solution of BQS/HQS was used as the catholyte. The cell reaction of the battery was the following;

$$2\rm{Li}\ +\ BQS\ +\ 2H_2O\ =\ 2\ LiOH\ +\ HQS$$

The open-circuit voltage (OCV) of the cell was around 3.7 V at 25 °C. The theoretical specific energy density based on the masses of the lithium anode, H2O, and BQS with an OCV of 3.7 V was 833 Whkg-1. The quinones are comparatively cheaper (~ $5-10 kg-1) [18]; hence are highly appropriate and attractive for large-size batteries for electric vehicles and various electrical energy storage applications.

2. Experimental

HQS was prepared by ion exchange of 1, 2-hydroquinone-3-sulfonic potassium salt (HQSK, Alfa Aesar) using an ion-exchange resin Amerlyst 15 DRY (Kurita Water, Japan). Since LAGTP had to be decomposed in a strongly acidic solution [21], the pH of the catholyte was adjusted to pH 2. The aqueous solutions of 0.8 M HQS in 5.5 M HAc and 2 M LiCl, 0.015 M H2SO4, and 10 m 1-butyl-3-methylimidazolium chloride (IBMmCl) with 1.0 M HCl (Sigma-Aldrich), all at pH 2.0, were examined as the catholyte. The 2 M LiCl was added to the 5.5 M HAc to increase the conductivity of the electrolyte. The electrochemical performance of the HQS/BQS redox reaction was studied using a beaker cell with a working electrode consisting of a mixture of a Pt-loaded carbon electrode (Pt-C) (Tanaka Kikinzoku, Japan) and polytetrafluoroethylene (PTFE) (Daikin Japan) (8:2 weight ratio), a Pt counter electrode, and Ag/AgCl in saturated KCl reference electrode. The cathode mixture was pressed on a titanium mesh (Nikara, Japan).

The schematic diagram of an in-house-built Swagelok-type full test cell is shown in Figure 1. The cell consisted of a 200 µm thick lithium metal anode (Honjometal, Japan), Li(CF3SO2)2N (LiFSI) dissolved in tetra(ethylene)glycol dimethyl ether (G4) (2:1 mole ratio) and 1,3 dioxolane (DOL, 50 vol%) as anode electrolyte, ca. 200 µm thick LAGTP-epoxy-10 wt% TiO2 as the solid electrolyte separator, an aqueous solution of 0.8M HQS in 5.5 M HAc and 2 M LiCl as the catholyte, and a mixture of Pt-C and PTFE as the cathode. The anode electrolyte LiFSI-2G4-50 vol% DOL was reported to suppress lithium dendrite formation at a high current density [22]. LAGTP-epoxy-TiO2 films were prepared by a previously reported tape casting method [23]. Fine LAGTP powder was prepared by a sol-gel method using citric acid [24]. Briefly, stoichiometric amounts of Ti(OC2H5)4 and Ge(OC2O5)4 (Sigma Aldrich) were dissolved in ethylene glycol, added to a 0.2 M aqueous solution of citric acid, and the solution was stirred well. After the gel formation, stoichiometric amounts of LiNO3, Al(NO3)3.9H2O, and NH4H2PO4 (Nakalai Tesque, Japan) were added to the gel. The gel was kept at 220 °C for several hours and was then heated at 580 °C for 4 h. The gel was then ground and heated again at 800 °C for 4 h. A mixture of LAGTP, a fine TiO2 powder (Kojundo Chemicals Japan, 2 µm particle size), Menhaden fish oil (Sigma Aldrich), Burver@B-98 (Sigma Aldrich), and benzyl-butyl-phthalate (Wako Chemicals, Japan) was ball-milled using a plenary mill (Fritsch, Mode 7). The obtained slurry was tape-casted onto a silicon-coated polyethylene substrate using a two doctor blade apparatus. The green tape-cast sheet was carefully dried at 4 °C followed by heating at 500 °C to remove organic additives, and finally sintered at 950 °C. The LAGTP-epoxy-TiO2 films were prepared by dipping the LAGTP-TiO2 film into a tetrahydrofuran solution containing 0.05 M 1,3-phenylene diamine (Sigma-Aldrich) and 2,2-bis(4-glycidyloxy-phenyl)propane (Sigma-Aldrich), followed by a polymerization reaction at 170 °C for 24 h [25]. The amount of epoxy in the LAGTP-TiO2 film estimated from the weight change was around ca 2 wt%. Lastly, the Pt loaded porous carbon (Tanaka Kikinzoku, Japan) and polytetrafluoroethylene (PTFE) mixture were pressed onto a titanium mesh (Nikara, Japan).

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Figure 1 Schematic of the test cell.

Impedance measurements were conducted using a frequency analyzer (Solatron 1260) in the frequency range of 0.1 Hz to 1 M Hz at a bias voltage of 10 mV. Bulk and grain boundary conductivities of the samples were estimated from the complex impedance plots using Zview 2 software. Electrochemical measurements were conducted using a multichannel potentio-galvanostat (Bio-Logic Science Instrument VMPX).

3. Results and Discussion

The stability of the solid electrolyte in the aqueous catholyte is an important requirement for the separator in the aqueous lithium batteries. The stability of LATP in the aqueous electrolytes was examined by Imanishi and co-workers [21,26,27,28]. They found that LATP was unstable in strong acid and alkaline aqueous solutions, and the lithium-ion conductivity of LATP was decreased considerably by its immersion in these solutions. We studied the impedance change of the tape cast LAGTP-epoxy-TiO2 films in an aqueous solution of 0.8 M HQS in 5.5 M HAc and 2M LiCl (pH = 2.0). The impedance profiles of Au/LAGTP-epoxy-TiO2/Au as a function of the immersion period in Figure 2(a) showed that the initial total conductivity of the film was 3.7x10-4 Scm-1 at 25 °C. The bulk conductivity was not changed for two weeks, but the grain boundary conductivity was decreased. The total conductivity of the electrolyte after two weeks was 1.5x10-4 Scm-1, followed by no further significant change in total conductivity. The XRD patterns of the LAGTP-epoxy-TiO2 film before and after immersion in 0.8 M HQS in 5.5 M HAc and 2M LiCl (pH = 2.0) for two weeks also showed no significant change. The other requirement of the solid electrolyte separator for the aqueous lithium cell is to be water impermeable. A water permeation test was conducted using an H-type cell, where one chamber was filled with pure water, and the other chamber was filled with 1M LiCl aqueous solution [25]. The water permeation rate was determined from the Cl- content in the chamber with water. The LAGTP-TiO2 film without epoxy resin had a high lithium-ion conductivity of 8.9x10-4 Scm-1, but exhibited water permeation through the film, while no water diffused through the LAGTP-epoxy-TiO2 film over a period of one week. The LAGTP-epoxy-TiO2 film was thus acceptable and recommended for the separator in the proposed aqueous lithium batteries.

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Figure 2 (a) Impedance profiles of the LAGTP epoxy-TiO2 immersed in an aqueous solution of 0.8 M HQS in 5.5 M HAc and 2M LiCl at pH 2.0 and 25 °C as a function of time (b) Water permeation test results for LAGTP-TiO2 and LAGTP-epoxy-TiO2.

Figure 3 shows cyclic voltammograms (CV) for the Pt-C electrode of an aqueous solution of 0.8 M HQS in 5.5 M HAc and 2 M LiCl, an aqueous solution of 15 mM H2SO4, and 10 m IBMmCl with 1.0 M HCl (IBMmCl-HCl) aqueous solution at 25 °C, where HQS was oxidized to BQS at 0.5 mA cm-2 for 20 h. The imidazole supporting electrolyte of IBM-1.0 M HCl was found to suppress the Michael addition reaction of benzoquinone with water [29]. The CV curve of 15 mM H2SO4 solution was similar to that of 1 mM 1, 2 benzoquinone-3,5-disulfonic acid (BQDS) in 1 M H2SO4 solution [17]. The peak potential of 1.15 V vs. NHE was comparable to 1.13 V vs. NHE observed in the case of 1 mM BQDS in 1 M H2SO4 solution [18] corresponding to the redox reaction of HQDS/BQDS. The hydrogen evolution reaction and oxygen evolution potentials at pH 2.0 without overpotential were -0.118 V vs. NHE and 1.111 V vs. NHE, respectively. The oxygen and hydrogen evolution reactions were observed at around 1.5 V vs. NHE and 0.0 V vs. NHE, respectively in 15 mM H2SO4. The CV for 5.5 M HAc and 2M LiCl and 10 m IBMmCl with 1.0 M HCl indicated the initiation of the HQS oxidation reaction at around 0.7 V vs. NHE, although no clear oxidation reaction peak was observed. The CV results for HQS in 15 mM H2SO4 confirmed that the HQS/BQS redox reaction proceeds by a two-electron reaction of BQS + 2H+ + 2e = HQS as reported previously for the hydroquinone-benzoquinone redox system in an aqueous solution [30]. Wu et al. observed the electrochemical oxidation reaction of HAc in an aqueous solution of 0.5 M H2SO4 at 1.14 V vs. NHE for a Pt60Ru10Sn30 electrode with a high Sn content [31], while Sine et al. suggested that the electrode with a low Sn content in Pt80Ru10Sn10 showed no oxidation of HAc in 1 M HClO3-0.1 M HAc aqueous solution [32]. The results showed in the present study were in agreement with the above studies and exhibited no clear oxidation peak for HAc.

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Figure 3 Cyclic voltammograms of the Pt-C electrode for 0.8 M HQS in 5.5 M HAc and 2 M LiCl (HAc), 15 mM H2SO4 (H2SO4), and 10 m IBMmCl-1.0 M HCl (IBMmCl-HCl) aqueous solutions at 25 °C. The scan rate was 5 mV s-1.

The redox reaction kinetics of HQS/BQS on Pt-C electrodes was examined in aqueous solutions with pH 2.0 at 25 °C. The overpotential (η) vs. current density (j) curves of 0.8 M HQS in 5.5 M HAc-2 M LiCl (HAc), 15 mM H2SO4 (H2SO4), and 10 m IBMmCl-1.0 M HCl (IBMmCl-HCl) aqueous solutions are shown in Figure 4, where the BQS reduction overpotentials were measured once around 20% of HQS was oxidized, and the overpotentials were recorded after the polarization for 10 min at each current density. The results showed that the oxidation overpotentials of HQS were low in the catholyte, whereas the reduction overpotentials of BQS were higher than the oxidation overpotential and depended on the catholyte. At a low current density, the lowest overpotential was observed in 0.8 M HQS taken in 5.5 M HAc-2 M LiCl (HAc), but at a high current density, the opposite was observed, and the overpotentials of the studied catholyte was higher than the other catholyte. The change in cell voltage with polarization period curves are shown in Figure 5. The cells were charged initially at 0.5 mAcm-2 for 10 mAh and then discharged at 0.5 mAcm-2. At this moment, around 80% of BQS was reduced to HQS with an overpotential of 0.5 V. The flat discharge overpotentials of around 0.15 V at 0.5 mAcm-2 were observed in 15 mM H2SO4 and 5.5 M HAc-2 M LiCl.

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Figure 4 Overpotential (η) vs. current density (j) curves for the oxidation of HQS and reduction of BQS on a Pt-C electrode in 0.8 M HQS in 5.5 M HAc-2 M LiCl (HAc), 15 mM H2SO4 (H2SO4), and 10 m IBMmCl-1.0 M HCl (IBMmCl-HCl) at 25 °C.

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Figure 5 Electrode potential vs. capacity curves for HQS oxidation and BQS reduction on a Pt-C electrode in 0.8 M HQS in 5.5 M HAc-2 M LiCl (HAc),15 mM H2SO4 (H2SO4), and 10 m IBMmCl-1.0 M HCl (IBMmCl-HCl) at 25 °C.

The full cell performance of the lithium metal anode and the BQS/HQS redox couple cathode was also investigated. The Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M BQS in 5.5 M HAc-2 M LiCl aqueous solution/Pt-C cell was tested at 25 °C. The OCV was 3.7 V, which was slightly lower than that of 3.92 V estimated from the BQS reduction potential in 1 M H2SO4 reported in the literature [17]. The low OCV could be due to the high pH of the catholyte, the junction potential between LAGTP-epoxy-TiO2 and the aqueous catholyte and anode electrolyte, and low lithium-ion activity at the Li/anode electrolyte. The impedance profile of the full cell at 25 °C is shown in Figure 6. The result showed two semicircles; one in the high-frequency range of 1 MHz and 25 kHz corresponds to the contribution of the grain boundary lithium-ion conduction in LAGTP-epoxy-TiO2 and the other in a low-frequency range of 25 kHz and 0.1 kHz attributed to the contribution of charge transfer resistance [33]. The intercept of the high-frequency semicircle with the real axis at high frequency is the sum of the bulk resistance of LAGTP-epoxy-TiO2 and the resistances of the buffer electrolyte and the catholyte. The ratio of these electrolyte resistances to the total cell resistance was around 0.5. In this study, a 1 mm thick anode electrolyte and 0.2 mm thick LAGTP-epoxy-TiO2 separator were used. The electrolyte resistance could be reduced by reducing the thicknesses of these electrolytes. Figure 7 shows the charge and discharge overpotential vs. current density curve for the Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2 M LiCl aqueous cell, where the cell was precharged at 0.5 mAcm-2 for 50 h (20% of full charge). The charging overpotentials increased slightly with the increasing current density, while the discharging overpotential showed a significant increase. At 2 mAcm-2, the round trip overpotential was 1.2 V, corresponding to a 33% energy loss.

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Figure 6 Impedance profile of Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2 M LiCl aqueous solution/Pt-C cell at 25 °C.

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Figure 7 Overpotential (η) vs. current density (j) curves for Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2 M LiCl aqueous solution/Pt-C cell at 25 °C.

The cycling performance of the Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2M LiCl aqueous solution/Pt-C cell at 0.5 mA cm-2 for 1 h discharge, 1 h rest, and then 1 h charge cycle at 25 °C is shown in Figure 8. The round-trip overpotential was 0.4 V, which corresponds to a 12% energy loss. The discharge voltages were slightly decreased with each cycle. The deep charge and discharge profiles at 0.5 mAcm-2 are shown in Figure 9. The cut-off voltages for charge and discharge were 4.5 V and 2.5 V, respectively, and the mass of the charged HQS was 0.189 g (65 mAh). The observed charge and discharge capacities were 49.6 and 26.5 mAh, respectively, which corresponded to 76% and 41% utility of the active material in the catholyte, respectively. The potential plateau for the hydrogen evolution reaction was observed at around 2.2 V. The calculated energy density of the proposed Li/HQSK cell was 358 Whkg-1 based on the masses of Li, H2O, and BQS and 41% utilization of BQS with an operating voltage of 3.4 V. The calculated energy density of the proposed new type aqueous lithium battery was comparable to that of the convention lithium-ion battery. The calculated specific energy density of the cell generally depends on the specific area capacity [34], and the cell performance of a solid active material such as LiCoO2 in the lithium-ion batteries depends on the thickness of the electrode [35]. However, the cell performance of a cell with a liquid catholyte shows no significant dependence on the specific area capacity, as reported in the literature [11]. Hence, the proposed Li/BQS battery with a liquid catholyte could provide high energy density at a high area capacity.

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Figure 8 Cycling performance of the Li/(LiFSI-2G)-50 vol%DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2 M LiCl aqueous solution/Pt-C cell at 0.5 mAcm-2 and 25 °C.

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Figure 9 Charge and discharge curves of the Li/(LiFSI-2G)-50 vol% DOL/LAGTP-epoxy-TiO2/0.8 M HQS-5.5 M HAc-2 M LiCl aqueous solution/Pt-C cell at 0.5 mAcm-2 and 25 °C.

4. Conclusion

The proposed novel aqueous lithium battery with a water-soluble and less expensive organic catholyte showed a higher theoretical specific energy density than conventional lithium-ion batteries. The cell performed well at 0.5 mAcm-2 and 25 °C and showed no significant degradation after 37 cycles. The battery with the aqueous catholyte could charge and discharge at a high specific area capacity, and the cost of the cathode active materials was lower than that of conventional lithium-ion batteries. Thus the proposed novel battery has a potential application for large-capacity batteries for electric vehicles and electric energy storage systems.

Author Contributions

HT prepared the solid electrolyte thin films, performed electrochemical measurements, and setup the full cell. KK prepared LAGTP fine powder. DM, S T, YT and OY supported and gave advice on each experimental work. NI managed the research direction and provided instructions and opportunities for discussions among all authors


This work was supported by JST Adaptable and Seamless Technology transfer Program through Target-driven R&D (A-STEP) Grant Number JPMJTM120EP.

Competing Interests

The authors have declared that no competing interests exist.


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