Ion Selectivity and Stability Enhancement of SPEEK/Lignin Membrane for Vanadium Redox Flow Battery: The Degree of Sulfonation Effect

Introduction

The vanadium redox flow battery (VRB) has attracted tremendous interest as a large-scale energy storage technique, for environment protection and sustainable development, in light of its long cycle life, fast response, flexible design, and great reliability via a cost-effective and eco-friendly means (Zhang et al., 2014a; Jia et al., 2015b; Yang et al., 2015; Ye et al., 2016; Lu et al., 2017; Wu et al., 2018, 2019). Proton exchange membrane is a key component in the flow battery, which performs as a separator to isolate the positive and negative electrolyte compartments, and meanwhile to conduct protons (Jia et al., 2012; Yu et al., 2016). An ideal membrane is expected to exhibit high proton conductivity, good chemical and mechanical stability, accurate ion selectivity, and low-cost fabrication approach (Jia et al., 2010; Ding et al., 2018; Yuan et al., 2018). To date, the commercial Nafion membranes have been widely used in VRBs, because of its good proton conductivity, remarkable chemical and mechanical stability (Li et al., 2014a; Dai et al., 2017). However, the high crossover rate of vanadium ions hampers its further application in VRBs (Zhang et al., 2018). Accordingly, several groups have been devoted to enhancing the performance of Nafion membranes by different methods, such as changing the casting solvent and annealing temperature (Dai et al., 2017), altering pretreatment process (Jiang et al., 2016), employing surface modification (Teng et al., 2015), forming composite structure with organic materials, inorganic materials or both (Zeng et al., 2008; Mai et al., 2011; Teng et al., 2013, 2014). The modified membranes usually lower the permeability of vanadium ions. Nevertheless, the extremely high cost of the Nafion membranes is a critical barrier for VRB commercialization (Yuan et al., 2017). Therefore, it is appealing to explore alternative systems of high ion selectivity, good stability and low cost toward practical application.

The sulfonated hydrocarbon polymers and their derivatives are promising candidates as the substitutional membranes (Wang et al., 2013). The sulfonated poly (ether ether ketone; SPEEK) is of particular interest, in view of its low vanadium ion permeability, simple preparation, high chemical, and mechanical stability (Winardi et al., 2014; Jia et al., 2015a). More importantly, the SPEEK membrane is cost-effective, only accounting for about several tenths of the commercial Nafion (DuPont). To enhance the proton conductivity, organic or inorganic materials with abundant hydrophilic groups are usually introduced to form composite membranes. Moreover, the interaction between the additives and the SPEEK matrix also ensures a good chemical and mechanical stability under harsh condition during the VRB operation. Jia et al. (2015a) prepared a composite membrane by blending the SPEEK with functionalized carbon nanotubes. The membrane shows not only high coulombic efficiency (CE), voltage efficiency (VE), and energy efficiency (EE), but also good mechanical stability and low capacity loss, compared with the pristine SPEEK and Nafion 212 membrane. Other SPEEK-based composite membranes also exhibited excellent performances for VRB application, such as SPEEK/SPES [sulfonated poly (ether sulfone)] (Ling et al., 2012), SPEEK/GO (graphene oxide; Kong et al., 2016; Park and Kim, 2016), SPEEK/QPEI [quaternized poly(ether imide)] membranes (Liu et al., 2014, 2015).

Considering the cost of the additives, the lignin has recently been focused in our group, which is a byproduct in paper industry and bio-fuel producing process (Gong, 2016). The lignin possesses abundant hydroxyl groups and thus improves the wettability of the polymer matrix and promotes the proton conductivity of the blend membrane. Figure 1 shows a general structure of lignin, in which the phenol propane unit is linked by alkyl–aryl, alkyl–alkyl and aryl–aryl ether bonds (Tolba et al., 2010; Ge et al., 2014; Zhang et al., 2014b; Zhu et al., 2016; Atifi et al., 2017; Rahman et al., 2018). The lignin interlaces with the SPEEK substrate and reduces the size of water channels. This gives rise to enhanced proton conductivity and meanwhile suppressed ion permeability. On the other hand, the degree of sulfonation (DS) in the SPEEK matrix, i.e., the amount of -SO₃H groups, also affects the proton conductivity. In general, the conductivity increases with the DS. However, a high DS seriously influence the chemical and mechanical stability of the membrane (Xi et al., 2015). In this study, the DS effect on the ion selectivity and stability was systematically studied. An optimized degree of sulfonation was proposed toward the application in VRBs.

FIGURE 1

Figure 1. The general structure of lignin and schematic illustration showing the water channel in a composite membrane for vanadium redox flow battery.

Experimental

Materials and Membranes Preparation

The lignin powders (Sigma-Aldrich) were soaked in 2 M hydrochloric acid solution (mass to volume ratio, 1 g per 20 mL) and stirred for 2 h. After that, sodium hydroxide solution was used to neutralize the above mixture, followed by filtration and freeze drying. The DS of SPEEK was controlled to about 41, 50, 59, and 72%, which were measured by titration method according to our previous work (Jia et al., 2015a). For the preparation of SPEEK/lignin composite membranes, 1.6 g of SPEEK was dissolved in 50 mL dimethyl sulfoxide (DMSO), and stirred at 60°C until being dissolving completely. After cooling down to room temperature, 240 mg pretreatment lignin powder was added and vigorously stirred overnight. The mixture was casted on a home-made glass plate and dried in oven at 100°C for solvent evaporation. After cooling, the membrane was peeled off from the glass and soaked in water immediately. Based on the mass ratio of lignin to SPEEK, the composite membranes were named as SPEEK41/L15, SPEEK50/L15, SPEEK59/L15, and SPEEK72/L15. Commercial Nafion 212 membrane (DuPont) was used as the reference. All of the reagents were used as received.

Characterization

Fourier transform infrared spectroscopy (FT-IR, Thermo Fisher Nicolet iS10) was investigated in the range of 400–4,000 cm⁻¹. The microstructure of the as-prepared membranes was examined with field-emission scanning electron microscopy (FESEM, Zeiss Auriga FIB/SEM). Water uptake (WU) was measured as follow: (1) dry membrane was soaked into distill water for 24 h; (2) the membrane was taken out and cleaned with filter paper immediately; (3) the cleaned membrane was weight by Mettler-Toledo analytical balance (ME204E). Swelling ratio (SR) was obtained by measuring the length variation of the membrane before and after immersing in deionized water for 24 h. The WU and SR of these membranes can be calculated through the following equations (Ling et al., 2012).

$\begin{array}{rc}\mathrm{\text{W}}U=\frac{{\mathit{\text{W}}}_{\mathit{\text{wet}}}-{\mathit{\text{W}}}_{\mathit{\text{dry}}}}{{\mathit{\text{W}}}_{\mathit{\text{dry}}}}& (1)\end{array}$

$\begin{array}{rc}\mathrm{\text{SR}}=\frac{{\mathit{\text{L}}}_{\mathit{\text{wet}}}-{\mathit{\text{L}}}_{\mathit{\text{dry}}}}{{\mathit{\text{L}}}_{\mathit{\text{dry}}}}& (2)\end{array}$

where the W_dry and W_wet are the weight of the membrane before and after soaking, respectively; the L_dry and L_wet are the length of the membrane before and after soaking, respectively.

The permeability of VO²⁺ ion across the membranes was investigated as follow: (1) isolating two reservoirs that were filled 70 mL of 1.5 M VOSO₄ in 3.0 M H₂SO₄ solution and 70 mL of 1.5 M MgSO₄ in 3.0 M H₂SO₄, respectively, with a membrane of 2.01 cm² active area; (2) stirring continuously and measuring the concentration of VO²⁺ in MgSO₄ compartment at 24 h intervals by TU-1900 UV-vis spectrometer; (3) sampling with replacement to keep the solution volume stable. A typical experimental setup was shown in Figure 2. The permeability value of the membrane can be calculated using Equation (3) (Jia et al., 2015a):

$\begin{array}{rc}\mathrm{\text{V}}\frac{\text{d}\mathit{\text{C}}(\mathit{\text{t}})}{d\mathit{\text{t}}}=\text{A}\frac{\mathit{\text{P}}}{\mathit{\text{L}}}(\text{C}-\mathit{\text{C}}(\mathit{\text{t}}))& (3)\end{array}$

where V, A, P, L, C, and C(t) are the volume of the VOSO₄ solution, the effective area of the membrane, the permeability of the vanadium ions, the thickness of the membrane, the initial concentration of VO²⁺ in the VOSO₄ compartment, and the vanadium concentration in the MgSO₄ compartment at the moment t, respectively.

FIGURE 2

Figure 2. A typical diffusion cell to measure VO²⁺ permeability.

The area resistance (R) of membranes was investigated by a resistance tester (DME-20, DM, China). The electrolytes in both compartments were 1.5 M VOSO₄ and 3 M H₂SO₄, and the conductivity (σ) of the membrane can be calculated as follow (Ling et al., 2012):

$\begin{array}{rc}\sigma =\frac{\mathit{\text{L}}}{\mathit{\text{AR}}}& (4)\end{array}$

where R represents the resistance difference between the cell with and without membrane, L is the thickness of the membrane, and A is the active area of membrane (13.5 cm²).

Cell Testing

The VRB single cell consisted of a composite membrane (13.5 cm²) sandwiched between two carbon felt electrodes (13.5 cm²), and two graphite polar plates (current collectors). The 1.5 M VO${}_2^{+}$ in 3.0 M H₂SO₄ and 1.5 M V³⁺ in 3.0 M H₂SO₄ solutions were used as catholyte and anolyte, respectively. The cell performance was measured by Arbin battery testing system (BT-I, Arbin, USA) including open circuit voltage decay (OCV), long cycle charge-discharge, and rate performance. The OCV (75% state of charge) was terminated when the voltage of the testing cell declined below 0.85 V. The potential range was between 0.7 and 1.75 V at room temperature.

Results and Discussion

Membrane Characterization

Figure 3 shows the FT-IR spectra of lignin, pure SPEEK, and the composite membranes. The broad band at 3,400 cm⁻¹ is ascribed to the hydrogen bond and OH vibration. For lignin, the peaks at 2,938 and 2,849 cm⁻¹ are assigned to the C-H stretch in methyl and methylene group (-CH₂-), and those at 1,594 and 1,511 cm⁻¹ are attributed to the aromatic rings of phenyl propane skeleton (characteristic bands of lignin; Faix, 1991). For SPEEK membrane alone, the following fingerprint absorption peaks are present: 3,428 cm⁻¹ (O-H stretching of -SO₃H groups), 1,076 cm⁻¹ (symmetric stretching of O = S = O), and 706 cm⁻¹ (S-O stretching; Li et al., 2014b; Ma et al., 2018). For composite membranes, the intensity of the peaks for -SO${}_3^{-}$ (1,076, 1,020, and 706 cm⁻¹) increases with the DS, because of the increased amount of the -SO₃H. More importantly, all of the composite membranes exhibit the characteristic peaks of lignin, indicating the incorporation of lignin into the SPEEK matrix. Compared with the pure SPEEK, the peaks of O-H stretching (3,248 cm⁻¹) shift toward the low frequency and the peak intensity decreases in the composite membranes. This suggests the hydrogen bond interaction between the -OH groups of lignin and the -SO₃H groups of SPEEK.

FIGURE 3

Figure 3. FT-IR spectra of (A) lignin powder, (B) pure SPEEK membrane, (C) SPEEK41/L15, (D) SPEEK50/L15, (E) SPEEK59/L15, (F) SPEEK72/L15.

Figures 4A,B reveals that the lignin powders are homogeneously dispersed in the SPEEK solution without any precipitates, even after 240 h. This is a prerequisite for forming a uniform composite membrane. Figures 4C,D displays the resulting SPEEK and SPEEK50/L15 membranes which exhibit uniform and dense surface. This would hamper the crossing of vanadium ions and enhance the cycle stability of the membrane. Moreover, the lignin particles are homogeneously embedded into the polymer matrix and can improve the wetting property of the composite membrane. The 3D structure of lignin also provides more pathways for protons transport and reduces the water channels to repulse vanadium ions. Therefore, the lignin is introduced into the SPEEK matrix, which can enhance the proton conductivity while inhibit the vanadium ions permeation.

FIGURE 4

Figure 4. Photographs of SPEEK solution and SPEEK/lignin mixture in DMSO: (A) initial and (B) after 240 h; SEM images of (C) pure SPEEK and (D) SPEEK50/L15 membranes.

The proton transport generally proceeds via the vehicle and Grotthuss mechanism in the membrane. As such, the water uptake is a critical property. It has been demonstrated that the proton conductivity of the proton exchange membrane enhances with the WU amount. However, a high water uptake usually results in low mechanical stability. Table 1 shows that the WU of SPEEK/lignin membranes increases with the DS, as more hydrophilic -SO₃H groups enhance the wetting property of the membrane. Similarly, the SR displays the same tendency as the WU.

TABLE 1

Table 1. Property of different membranes.

The permeability of the resulting membranes is shown in Figure 5. The VO²⁺ permeability of SPEEK/lignin membranes increases with the degree of sulfonation. This is attributed to the high DS that generally imparts abundant -SO${}_3^{-}$ groups in the polymer matrix, which drastically improve the proton conductivity (see Table 1) and also accelerate the crossover of vanadium ions through the membrane. The ion selectivity (Zhang et al., 2014a; Ji et al., 2017), namely the ratio of proton conductivity to ion permeability, is widely used to describe the balance between the two processes. Figure 5B shows that the ion selectivity of the composite membranes is much higher than that of the Nafion 212, regardless of the DS in SPEEK, because of the suppressed permeability of VO²⁺ ion. This clearly demonstrates the advances of the composite system. In particular, the SPEEK59/L15 membrane exhibits the best performance (61.96 × 10⁴ S min cm⁻³), nearly five-fold increment as compared to the Nafion 212 (12.78 × 10⁴ S min cm⁻³). The incorporation of lignin into the SPEEK substrate provides more proton transport pathway and meanwhile adjusts the water channels to repulse vanadium ions, thus giving rise to high ion selectivity.

FIGURE 5

Figure 5. Comparison between Nafion 212 and SPEEK/Lignin membranes: (A) VO²⁺ permeability; (B) permeability and ion selectivity.

Cell Performances

To systematically study the performance of the composite membranes, the OCV, long cycle process, and rate performance of VRB single cells were carried out under different conditions. The OCV is a critical parameter to verify the vanadium ions cross rate in the membranes, as the vanadium ions crossing the membrane results in self-discharge and therefore the cell voltage declines accordingly. Figure 6A reveals that the OCV curves decrease rapidly with the enhanced DS in the composite membrane. It is obvious that the voltage decay (above 0.85 V) of cells assembled with the composite membranes is much slower than that of Nafion 212 (288.6 vs. 14.05 h for SPEEK41/L15 vs. Nafion). This indicates that the SPEEK/lignin composite membrane efficiently suppresses the permeation of vanadium ions, in good agreement with the results in Figure 5.

FIGURE 6

Figure 6. (A) Open circuit voltage decay of different membranes, (B) the charge-discharge performance of VRB cells employing different membranes at 120 mA cm⁻².

Figure 6B displays the typical charge-discharge curves of the VRB cells using different membranes under current density of 120 mA cm⁻². As a high area resistance (see Table 1) usually leads to high ohmic polarization, the average charge voltage of cells with SPEEK/lignin membranes is slightly higher than that of the Nafion 212, with the average discharge voltage being on the contrary. However, the SPEEK59/L15 membrane exhibits the best discharge capacity, as a result of high ion selectivity, consistent with the above discussion.

Figure 7 shows the cycling performance of cells assembled with SPEEK59/L15 and Nafion 212 membranes from 50 to 320 mA cm⁻². The Coulombic efficiency of the cells with SPEEK59/L15 (up to 99.56%) is higher than that of Nafion 212 over the whole rate range. This originates from the reduced vanadium ion permeability with the composite membranes. It is noted that the CE of both cells increases with the current density. This is mainly due to the shortened charge-discharge time under high current density, which suppresses the crossover of vanadium ions through the membrane. Figure 7B reveals that the discharge capacity of SPEEK59/L15 is higher than that of the Nafion 212 under current density ≤ 250 mA cm⁻². This can be attributed to the overpotential and ohmic polarization under high current. Therefore, the better performance of SPEEK59/L15 is ascribed to the synergistic effect from the lignin additives and SPEEK matrix, which provides more proton transport pathway and meanwhile suppresses the crossover of the vanadium ions.

FIGURE 7

Figure 7. The Coulombic efficiency (A) and discharge capacity (B) of the cells with SPEEK59/L15 and Nafion 212 membranes at current density between 50 and 320 mA cm⁻².

Figure 8 displays the stability performance of the corresponding VRB cells operated at 120 mA cm⁻². The Coulombic efficiency decreases with the degree of sulfonation (Figure 8A). This agrees well with the varying trend of VO²⁺ permeability (Figure 5A), as a high DS improves the proton conductivity but accelerates the crossover of vanadium ions through the membrane. As such, the voltage efficiency increases with the DS (Figure 8B). Accordingly, the cells with SPEEK59/L15 membranes exhibit an impressive energy efficiency (EE = CE × VE, up to 82.75%), comparable to that of the Nafion 212. This is attributed to the best ion selectivity for the SPEEK59/L15 membrane. It is noteworthy that the cells with SPEEK72/L15 fail after only 29th cycles, as a high DS deteriorates the mechanical and chemical stability of the membrane.

FIGURE 8

Figure 8. The Coulombic efficiency (A), voltage efficiency (B), energy efficiency (C), and discharge capacity retention (D) of VRB cells using different membranes under current density of 120 mA cm⁻².

The capacity retention of VRB cells is a key factor to measure the ion imbalance in the operation process. Figure 8D discloses that the discharge capacity retention of the cells assembled with Nafion 212 maintains just 55.96% after 100 cycles under 120 mA cm⁻². In contrast, under the same conditions, the cells with SPEEK59/L15 keep about 94.80% after 100 cycles, and more than 85% after 200 cycles. This demonstrates that the SPEEK59/L15 membrane substantially suppresses the crossover of vanadium ions and thus enhances the stability and prolongs the cycle life. The cells with the SPEEK59/L15 membranes show the best capacity retention and outperform the other ones. The SPEEK59/L15 membranes synthesized by an eco-friendly and cost-effective approach exhibits high ion selectivity and excellent stability, making it a promising candidate for efficient VRB system.

Conclusions

The SPEEK/lignin composite membranes were optimized by controlling the degree of sulfonation toward the VRB application. The VRB cells with SPEEK59/L15 membranes exhibit an impressive energy efficiency up to 82.75%, low vanadium ion permeability, high ion selectivity, and high capacity retention (94.80% after 100 cycles and over 85% after 200 cycles). The good performance is assigned to the synergistic effect from the lignin additives and SPEEK matrix, which improves the proton conductivity and suppresses the crossover of the vanadium ions. The eco-friendly and cost-effective composite membranes make it a competent candidate for VRB energy storage technique.

Author Contributions

MD, LS, and CJ conceived the idea and supervised the work. JY and XL synthesized the membranes and performed most of the experiments. JY, XL, CW, and SW prepared the samples and analyzed the data. JY, XL, MD, LS, and CJ participated in analyzing the data and wrote the report. All authors read and approved the final manuscript.

Funding

The project was supported by Open Fund of National Engineering Laboratory of Highway Maintenance Technology, Changsha University of Science & Technology (kfj170105, kfj170107). LS was grateful for the financial support from the National Natural Science Foundation of China (No. 51871037, 51501024), the Fundamental Research Funds for the Central Universities (No. 2018CDQYCL0027), and the Chongqing Entrepreneurship and Innovation Program for the Returned Overseas Chinese Scholars (No. cx2017035).

Conflict of Interest Statement

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

We acknowledge the support from the 100 Talented Team of Hunan Province.

References

Atifi, S., Miao, C. W., and Hamad, W. Y. (2017). Surface modification of lignin for applications in polypropylene blends. J. Appl. Polym Sci. 134:45103. doi: 10.1002/app.45103

CrossRef Full Text | Google Scholar

Dai, J. C., Teng, X. G., Song, Y. Q., and Ren, J. (2017). Effect of casting solvent and annealing temperature on recast Nafion membranes for vanadium redox flow battery. J. Membr. Sci. 522, 56–67. doi: 10.1016/j.memsci.2016.09.014

CrossRef Full Text | Google Scholar

Ding, M., Ling, X., Yuan, D., Cheng, Y., Wu, C., Chao, Z. S., et al. (2018). SPEEK membrane of ultrahigh stability enhanced by functionalized carbon nanotubes for vanadium redox flow battery. Front. Chem. 6:286. doi: 10.3389/fchem.2018.00286

CrossRef Full Text | Google Scholar

Faix, O. (1991). Classification of Lignins from Different Botanical Origins by FT-IR Spectroscopy, Holzforschung-International Journal of the Biology, Chemistry, Physics and Technology of Wood, 45, 21–28.

Google Scholar

Ge, Y. Y., Xiao, D., Li, Z. L., and Cui, X. M. (2014). Dithiocarbamate functionalized lignin for efficient removal of metallic ions and the usage of the metal-loaded bio-sorbents as potential free radical scavengers. J. Mater. Chem. A 2, 2136–2145. doi: 10.1039/C3TA14333C

CrossRef Full Text | Google Scholar

Gong, S. D. (2016). A green and environment-friendly gel polymer electrolyte with higher performances based on the natural matrix of lignin. J. Power Sourc. 307, 624–633. doi: 10.1016/j.jpowsour.2016.01.030

CrossRef Full Text | Google Scholar

Ji, Y., Tay, Z. Y., and Li, S. F. Y. (2017). Highly selective sulfonated poly(ether ether ketone)/titanium oxide composite membranes for vanadium redox flow batteries. J. Membr. Sci. 539, 197–205. doi: 10.1016/j.memsci.2017.06.015

CrossRef Full Text | Google Scholar

Jia, C. K., Cheng, Y. H., Ling, X., Wei, G. J., Liu, J. G., and Yan, C. W. (2015a). Sulfonated Poly(Ether Ether Ketone)/functionalized carbon nanotube composite membrane for vanadium redox flow battery applications. Electrochim. Acta 153, 44–48. doi: 10.1016/j.electacta.2014.11.123

CrossRef Full Text | Google Scholar

Jia, C. K., Liu, J. G., and Yan, C. W. (2010). A significantly improved membrane for vanadium redox flow battery. J. Power Sources 195, 4380–4383. doi: 10.1016/j.jpowsour.2010.02.008

CrossRef Full Text | Google Scholar

Jia, C. K., Liu, J. G., and Yan, C. W. (2012). A multilayered membrane for vanadium redox flow battery. J. Power Sources 203, 190–194. doi: 10.1016/j.jpowsour.2011.10.102

CrossRef Full Text | Google Scholar

Jia, C. K., Pan, F., Zhu, Y. G., Huang, Q. Z., Lu, L., and Wang, Q. (2015b). High–energy density nonaqueous all redox flow lithium battery enabled with a polymeric membrane. Sci. Adv. 1:e1500886. doi: 10.1126/sciadv.1500886

PubMed Abstract | CrossRef Full Text | Google Scholar

Jiang, B., Yu, L. H., Wu, L. T., Mu, D., Liu, L., Xi, J. Y., et al. (2016). Insights into the impact of the nafion membrane pretreatment process on vanadium flow battery performance. ACS Appl. Mater. Inter. 8, 12228–12238. doi: 10.1021/acsami.6b03529

PubMed Abstract | CrossRef Full Text | Google Scholar

Kong, L. Q., Zheng, L. Y., Niu, R. T., Wang, H. X., and Shi, H. F. (2016). A sulfonated poly(ether ether ketone)/amine-functionalized graphene oxide hybrid membrane for vanadium redox flow batteries. RSC Adv. 6, 100262–100270. doi: 10.1039/C6RA22665E

CrossRef Full Text | Google Scholar

Li, Z. H., Dai, W. J., Yu, L. H., Xi, J. Y., Qiu, X. P., and Chen, L. Q. (2014a). Sulfonated poly(ether ether ketone)/mesoporous silica hybrid membrane for high performance vanadium redox flow battery. J. Power Sources 257, 221–229. doi: 10.1016/j.jpowsour.2014.01.127

CrossRef Full Text | Google Scholar

Li, Z. H., Liu, L., Yu, L. H., Wang, L., Xi, J. Y., Qiu, X. P., et al. (2014b). Characterization of sulfonated poly(ether ether ketone)/poly(vinylidene fluoride-co-hexafluoropropylene) composite membrane for vanadium redox flow battery application. J. Power Sourc. 272, 427–435. doi: 10.1016/j.jpowsour.2014.08.101

CrossRef Full Text | Google Scholar

Ling, X., Jia, C. K., Liu, J. G., and Yan, C. W. (2012). Preparation and characterization of sulfonated poly(ether sulfone)/sulfonated poly(ether ether ketone) blend membrane for vanadium redox flow battery. J. Membr. Sci. 415–416, 306–312. doi: 10.1016/j.memsci.2012.05.014

CrossRef Full Text | Google Scholar

Liu, S., Wang, L. H., Ding, Y., Liu, B. Q., Han, X. T., and Song, Y. L. (2014). Novel sulfonated poly (ether ether keton)/polyetherimide acid-base blend membranes for vanadium redox flow battery applications. Electrochim. Acta 130, 90–96. doi: 10.1016/j.electacta.2014.02.144

CrossRef Full Text | Google Scholar

Liu, S., Wang, L. H., Li, D., Liu, B. Q., Wang, J. J., and Song, Y. L. (2015). Novel amphoteric ion exchange membranes by blending sulfonated poly(ether ether ketone)/quaternized poly(ether imide) for vanadium redox flow battery applications. J. Mater. Chem. A 3, 17590–17597. doi: 10.1039/C5TA04351D

CrossRef Full Text | Google Scholar

Lu, W. J., Yuan, Z. Z., Zhao, Y. Y., Zhang, H. Z., Zhang, H. M., and Li, X. (2017). Porous membranes in secondary battery technologies. Chem. Soc. Rev. 46, 2199–2236. doi: 10.1039/C6CS00823B

PubMed Abstract | CrossRef Full Text | Google Scholar

Ma, Y. J., Qaisrani, N. A., Ma, L. L., Li, P. Y., Li, L., Gong, S. T., et al. (2018). Side chain hydrolysis method to prepare nanoporous membranes for vanadium flow battery application. J. Membr. Sci. 560, 67–76. doi: 10.1016/j.memsci.2018.05.014

CrossRef Full Text | Google Scholar

Mai, Z. S., Zhang, H. M., Li, X. F., Xiao, S. H., and Zhang, H. Z. (2011). Nafion/polyvinylidene fluoride blend membranes with improved ion selectivity for vanadium redox flow battery application. J. Power Sources 196, 5737–5741. doi: 10.1016/j.jpowsour.2011.02.048

CrossRef Full Text | Google Scholar

Park, S., and Kim, H. (2016). Preparation of a sulfonated poly(ether ether ketone)-based composite membrane with phenyl isocyanate treated sulfonated graphene oxide for a vanadium redox flow battery. J. Electrochem. Soc. 163, A2293–A2298. doi: 10.1149/2.0731610jes

CrossRef Full Text | Google Scholar

Rahman, O., Shi, S. B., Ding, J. H., Wang, D. L., Ahmad, S., and Yu, H. B. (2018). Lignin nanoparticles: synthesis, characterization and corrosion protection performance. New J. Chem. 42, 3415–3425. doi: 10.1039/C7NJ04103A

CrossRef Full Text | Google Scholar

Teng, X. G., Dai, J. C., Bi, F. Y., and Yin, G. P. (2014). Ultra-thin polytetrafluoroethene/Nafion/silica composite membrane with high performance for vanadium redox flow battery. J. Power Sources 272, 113–120. doi: 10.1016/j.jpowsour.2014.08.060

CrossRef Full Text | Google Scholar

Teng, X. G., Dai, J. C., Su, J., and Yin, G. P. (2015). Modification of Nafion membrane using fluorocarbon surfactant for all vanadium redox flow battery. J. Membr. Sci. 476, 20–29. doi: 10.1016/j.memsci.2014.11.014

CrossRef Full Text | Google Scholar

Teng, X. G., Dai, J. C., Su, J., Zhu, Y. M., Liu, H. P., and Song, Z. G. (2013). A high performance polytetrafluoroethene/Nafion composite membrane for vanadium redox flow battery application. J. Power Sources 240, 131–139. doi: 10.1016/j.jpowsour.2013.03.177

CrossRef Full Text | Google Scholar

Tolba, R., Tian, M., Wei, J. L., Jiang, Z. H., and Chen, A. C. (2010). Electrochemical oxidation of lignin at IrO2-based oxide electrodes. J. Electroanal. Chem. 649, 9–15. doi: 10.1016/j.jelechem.2009.12.013

CrossRef Full Text | Google Scholar

Wang, N. F., Yu, J., Zhou, Z., Fang, D., Liu, S. Q., and Liu, Y. N. (2013). SPPEK/TPA composite membrane as a separator of vanadium redox flow battery. J. Membr. Sci. 437, 114–121. doi: 10.1016/j.memsci.2013.02.053

CrossRef Full Text | Google Scholar

Winardi, S., Raghu, S. C., Oo, M. O., Yan, Q., Wai, N., Lim, T. M., et al. (2014). Sulfonated poly (ether ether ketone)-based proton exchange membranes for vanadium redox battery applications. J. Membr. Sci. 450, 313–322. doi: 10.1016/j.memsci.2013.09.024

CrossRef Full Text | Google Scholar

Wu, C., Lou, X., and Jia, C. (2019). Porous Ni-Mo-Co hydroxide nanoflakes on carbon cloth for supercapacitor application. J. Nanosci. Nanotechnol. 19, 272–276. doi: 10.1166/jnn.2019.16450

PubMed Abstract | CrossRef Full Text | Google Scholar

Wu, C., Zhu, Y., Ding, M., Jia, C. K., and Zhang, K. L. (2018). Fabrication of plate-like MnO₂ with excellent cycle stability for supercapacitor electrodes. Electrochim. Acta 291, 249–255. doi: 10.1016/j.electacta.2018.08.126

CrossRef Full Text | Google Scholar

Xi, J. Y., Li, Z. H., Yu, L. H., Yin, B. B., Wang, L., Liu, L., et al. (2015). Effect of degree of sulfonation and casting solvent on sulfonated poly(ether ether ketone) membrane for vanadium redox flow battery. J. Power Sourc. 285, 195–204. doi: 10.1016/j.jpowsour.2015.03.104

CrossRef Full Text | Google Scholar

Yang, R. D., Cao, Z. S., Yang, S. W., Michos, I., Xu, Z., and Dong, J. (2015). Colloidal silicalite-nafion composite ion exchange membrane for vanadium redox-flow battery. J. Membr. Sci. 484, 1–9. doi: 10.1016/j.memsci.2015.03.012

CrossRef Full Text | Google Scholar

Ye, J. Y., Li, Z., Dai, Z., Zhang, Z. Y., Guo, M. Q., and Wang, X. J. (2016). Facile synthesis of hierarchical CuO nanoflower for supercapacitor electrodes. J. Electron. Mater. 45, 4237–4245. doi: 10.1007/s11664-016-4587-1

CrossRef Full Text | Google Scholar

Yu, L. H., Lin, F., Xu, L., and Xi, J. Y. (2016). A recast Nafion/graphene oxide composite membrane for advanced vanadium redox flow batteries. RSC Adv. 6, 3756–3763. doi: 10.1039/C5RA24317C

CrossRef Full Text | Google Scholar

Yuan, Z., Zhang, H., and Li, X. (2018). Ion conducting membranes for aqueous flow battery systems. Chem. Commun. 54, 7570–7588. doi: 10.1039/C8CC03058H

PubMed Abstract | CrossRef Full Text | Google Scholar

Yuan, Z. Z., Dai, Q., Qiao, L., Zhao, Y. Y., Zhang, H. M., and Li, X. F. (2017). Highly stable aromatic poly (ether sulfone) composite ion exchange membrane for vanadium flow battery. J. Membr. Sci. 541, 465–473. doi: 10.1016/j.memsci.2017.07.036

CrossRef Full Text | Google Scholar

Zeng, J., Jiang, C. P., Wang, Y. H., Chen, J. W., Zhu, S. F., Zhao, B. J., et al. (2008). Studies on polypyrrole modified nafion membrane for vanadium redox flow battery. Electrochem. Commun. 10, 372–375. doi: 10.1016/j.elecom.2007.12.025

CrossRef Full Text | Google Scholar

Zhang, H. Z., Ding, C., Cao, J. Y., Xu, W. X., Li, X. F., and Zhang, H. M. (2014a). A novel solvent-template method to manufacture nano-scale porous membranes for vanadium flow battery applications. J. Mater. Chem. A 2, 9524–9531. doi: 10.1039/c4ta00917g

CrossRef Full Text | Google Scholar

Zhang, S., Sun, J., Zhang, X., Xin, J., Miao, Q., and Wang, J. (2014b). Ionic liquid-based green processes for energy production. Chem. Soc. Rev. 43, 7838–7869. doi: 10.1039/C3CS60409H

PubMed Abstract | CrossRef Full Text | Google Scholar

Zhang, Y. X., Wang, H. X., Yu, W. K., Shi, J. L., and Shi, H. F. (2018). Sulfonated poly(ether ether ketone)-based hybrid membranes containing polydopamine-decorated multiwalled carbon nanotubes with acid-base pairs for all vanadium redox flow battery. J. Membr. Sci. 564, 916–925. doi: 10.1016/j.memsci.2018.07.065

CrossRef Full Text | Google Scholar

Zhu, H. L., Luo, W., Ciesielski, P. N., Fang, Z. Q., Zhu, J. Y., Henriksson, G., et al. (2016). Wood-derived materials for green electronics, biological devices, and energy applications. Chem. Rev. 116, 9305–9374. doi: 10.1021/acs.chemrev.6b00225

CrossRef Full Text | Google Scholar