Physicochemical compatibility of highly-concentrated solvate ionic liquids and a low-viscosity solvent

High ionic carrier mobilities are important for the electrolyte solutions used in high-performance batteries. Based on the functional sharing concept, we fabricated mixed electrolytes consisting of solvate ionic liquids (SIL), which are highly concentrated solution electrolyte, and the non-coordinating low-viscosity dilution solvent 1,1,2,2-tetrafluoroethyl 2,2,3,3-tetrafluoropropyl ether (HFE). We investigated the thermal, transport, and static properties of electrolytes with different ratios of SIL to HFE. In particular, the interactions between the SILs and HFE and static correlations of the coordinating (ether-based molecules), non-coordinating (HFE), and carrier ionic species (lithium salt) were clarified by applying the excess density concept. Ether molecules always formed strong complexes with lithium cations regardless of the absence or presence of HFE. The repulsion force between the SILs and HFE was strongly affected by lithium salt concentration. From our results, we proposed dissociation/association models for these electrolyte systems.


Introduction
Renewable energy technology or industry such as solar, wind power, geothermal heat, and biomass are prospective contributors to achieve a sustainable low-carbon society because they do not emit greenhouse gases. 1 However, renewable energies are unstable because of their large output uctuations and both their power generation and equipment are expensive. To solve these problems, it is necessary to develop large-scale secondary battery systems to level the input and output loads of natural energies. [2][3][4][5] Renewable energy also needs to meet the demands of low cost, high energy density, and long life to realize its effective use. Lithiumsulfur (Li-S) batteries are attracting attention as possible successors of Li-ion batteries with highenergy density and low cost. 6 Generally, Li-S batteries are composed of an S/carbon composite as a positive electrode, Li metal as the negative electrode, and mixture of solvent(s) and salt(s) as electrode as the electrolyte. 7 An S positive electrode has a larger theoretical capacity (1672 mA h g À1 ) than that of conventional electrode materials such as Li x CoO 2 (0.5 < x < 1; 137 mA h g À1 ). Elemental S (S 8 ) can react in multistep processes (discharge: cleavage, charge: recombination) involving 16 electron transfer reactions. These properties make Li-S battery systems promising as innovative high-energy-density power storage devices. In addition, elemental S is environmentally friendly, inexpensive because it is obtained as a by-product from oil rening, and also has low toxicity, which makes it a safe positive electrode material. However, the reaction intermediate lithium polysulde (Li 2 S x ; x ¼ 2-8) can dissolve into commonly used electrolyte solution during charge/discharge at the positive electrode/electrolyte interface, which leads to cell degradation during cycling. [8][9][10][11] Dissolution and diffusion of Li 2 S x into the electrolyte solution has serious effects on the performances of Li-S batteries for the following reasons.
(1) Capacity degradation of the S electrode by decreasing of the net positive S electrode mass.
(3) Re-oxidative reaction of the reduced intermediate (generated as shown in (2)) at the S positive electrode (redox shuttle mechanism) Therefore, control of Li 2 S x dissolution is essential to realize high-performance Li-S batteries.
The solubility of Li 2 S x depends on electrolyte, and therefore the design of electrolyte is important for improving battery performance. Dokko et al. used solvate ionic liquids (SILs) as the electrolyte for Li-S batteries owing to the low solubility of Li 2 S x . 12 Their SILs consisted of a 1 : 1 complex of glyme molecules and Li salt with weak Lewis acidity/basicity. Glyme molecules and Li cations can form quite stable coordinated cations, such as [Li(Glyme)] + , which exist in the liquid state at room temperature, and have weak basicity with similar complex structures. 13,14 SILs are a type of room-temperature ionic liquid because of their liquid properties at room temperature and composition of complex cations and counter anions. 15 As room-temperature ionic liquids, SILs show not only high thermal stability and low volatility but also high ionic conductivity and a wide electrochemical window. 13 Meanwhile, SILs hardly interact with Li 2 S x , and can control the dissolution of the reactive intermediate Li 2 S x into electrolyte solution. 12 Long cycle life (over 800 cycles) and high coulombic efficiencies (over 97%) have been realized by using Li-S batteries. 16 However, the glyme and Li salt are not equimolar near the electrode/ electrolyte interface owing to the Li alloying and de-alloying into the electrode associated with charge/discharge process, even if the equimolar mixture is used for the electrolyte. 17 Thus, Li 2 S x can dissolve into the electrolyte through dynamic electrochemical reactions because of the presence of free glyme molecules 18 originating from the desolvated SIL. Against such a background, we proposed using non-equimolar SILs (mixture of glyme with excess Li salt) to suppress battery degradation through the formation of robust complexes. 19 Such an electrolyte can suppress the dissolution of Li 2 S x into free glyme (non-coordinated solvent molecules) during the discharge process of Li-S batteries. 20 Recently, 'super-concentrated' electrolytes using other solvent systems have attracted attention for use as chemically/ electrochemically stable electrolytes. [21][22][23][24] However, the viscosity of electrolyte systems increases with of Li salt concentration, which raises the internal resistance of the cell and decreases of input/ output performance. To obtain a low-viscosity electrolyte solution, the concept of dilution with the low-viscosity non-coordinating uorinated solvent 1,1,2,2-tetrauoroethyl 2,2,3,3-tetrauoropropyl ether (HFE) has been proposed to realize electrochemically stable batteries with suitable charge/discharge rate capability without destroying the solvated structure of SILs. 25 In previous research, dilution of HFE was valid for systems with a 1 : 1 molar ratio of glyme to Li salt; however, the effects of dilution with HFE on nonequimolar SILs were unclear. Also, understanding the interactions between HFE and SILs (including the coordinated solvent and Li salt) is very important for designing of high-performance Li-S batteries. In this report, we investigate the thermal, static (density), and transport (viscosity) properties of mixture of SILs and HFE. The interactions between coordinated solvent (glyme) and noncoordinated solvent (HFE) molecules and dissolved salts are claried.

Samples
Distilled and dried tetraglyme (G4, Nippon Nyukazai Co., Ltd.;  Fig. 1) was used as a solvent to dilute these electrolytes by a predetermined amount.

Thermal analysis
The thermal properties of prepared samples were investigated using a thermogravimetry/differential thermal analysis (TG/ DTA) using a Thermo plus EVO2 analyzer (Rigaku) from 303.15 to 753.15 K at a heating rate of 10 K min À1 . The thermal transitions of prepared samples were also investigated using the differential scanning calorimetry (DSC) on the same systems. Samples for DSC measurements were hermetically sealed in aluminium pans in a dry argon-lled glovebox. Thermograms were recorded during a cooling scan (303.15 K to 173.15 K) followed by a heating scan (173.15 to 303.15 K), at the same cooling and heating rates of 10 K min À1 .

Viscosity and density measurements
Viscosity (h) and density (r) measurements were carried out using a Stabinger-type viscometer/density measurement system (SVM3000/G2, Anton Paar). The temperature was set in the range of 283.15 to 353.15 K at 5 K intervals while heating samples.   1.25 conrmed that the molar ratio of HFE to [Li a (G4) 1 ]TFSA a was less than one in both systems. Moreover, T g values shied to lower temperature with increasing HFE mole fraction, which was attributed to freezing point depression. Fig. 3(c) shows the relationship between observed T g and HFE mole fraction for two systems. T g of both [Li 1 (G4) 1 ]TFSA and [Li 1.25 (G4) 1 ]TFSA 1.25 decreased by more than 30 K upon dilution with HFE.  1.25 . At all measured temperatures, the neat SIL with a ¼ 1.25 displayed higher h values than those for the neat SIL with a ¼ 1. This is because of difference in   Fig. 6(a) and (b), respectively. In static state, Li + and G4 form stable complex cations with a 1 : 1 molar ratio and excess Li + should promote repulsion with the dilution solvent HFE. In fact, LiTFSA and HFE cannot dissolve each other (Fig. S1 †). As a result, r was decreased by addition of excess LiTFSA. Also, G4-Li + complexes should always undergo ligand exchange and the diluted systems might form clusters consisting of SIL domains and HFE domains.

Interaction between SILs and HFE
The r values of [Li a (G4) 1 ]TFSA a (a ¼ 1, 1.25) and HFE mixed electrolyte solutions were lower than the middle point between the r values of the neat SILs and HFE. To investigate the r changes upon mixing the SIL and HFE, the excess density (E r ) was calculated as follows, 27 where x is the molar fraction of HFE, r measured is the measured density, r HFE is the density of neat HFE, and r SIL is the density of the neat SIL, respectively. Fig. 7 Fig. 6. The decreasing r of the samples with a ¼ 1.25 between x ¼ 0 and 0.2 was consistent with the minimum E r value at x ¼ 0.2, which suggests the possibility of microphase separation of SIL and HFE. Our result were consistent with those of a previous spectroscopic report that indicated the formation of a microscopic stable coordination microstructure between Li + and glyme molecules even if SIL was diluted with HFE. 25 In contrast, positive values of E r were observed for the samples with a ¼ 1 and a high molar fraction of HFE at 323.15 K. In the case of high temperature and low SIL concentration, slight solubility between the SIL and HFE might occur through colligative property. In the future, we will further investigate the nanoscopic relationships between LiTFSA, G4 using high energy X-ray diffraction and Raman spectroscopy measurements.

Conclusions
Mixtures of solvated ionic liquids ([Li 1 (G4) 1 ]TFSA, [Li 1.25 (G4) 1 ] TFSA 1.25 ) that were diluted with the solvent HFE were prepared, and their thermal, transport, and static properties were investigated. The results of this study are summarized as follows.
(1) The boiling temperature of HFE and decomposition temperature of SIL were observed independently in all measured systems. T g s of SILs were obtained regardless of HFE dilution even though freezing point depression was observed. Thermal investigations indicated there were no strong interactions between the SILs and HFE.
(2) The viscosity of [Li 1.25 (G4) 1 ]TFSA 1.25 was approximately three times higher than that of [Li 1 (G4) 1 ]TFSA at 303.15 K. Upon dilution with HFE, the SILs possessed almost the same viscosity values independent of the Li salt concentration, which leads to equal uidity in the electrolyte solutions. Dilution with HFE was therefore effective to achieve high ionic mobility of electrolyte solutions regardless of Li salt concentration.
(3) The densities of [Li 1.25 (G4) 1 ]TFSA 1.25 was higher than that of [Li 1 (G4) 1 ]TFSA at all measured temperatures and the same tendencies were observed for density as for viscosity measurements. To analyze density changes of the mixtures caused by HFE dilution, excess densities were calculated as an index for the repulsion/attraction between the SILs and HFE. [Li 1.25 (G4) 1 ] TFSA 1.25 exhibited larger volume expansion than that of [Li 1 (G4) 1 ]TFSA upon HFE dilution and the excess Li salt in the  formed should increase the repulsion force of the SIL towards HFE. Therefore, compatibility of the SIL with excess Li salt and HFE is suitable from the viewpoint of battery performance, such as rate capability.

Conflicts of interest
There are no conicts of interest to declare.