Effects of repeat unit charge density on the physical and electrochemical properties of novel heterocationic poly(ionic liquid)s

We report the synthesis and structure/property correlations of a series of eight poly(ionic liquid)s (PILs) obtained from sequential AA + BB polyaddition by copper(I)-catalyzed azide–alkyne cycloaddition and the subsequent N-alkylation reaction. The different repeat units contain one to four ion pairs, with one to four bis(trifluorosulfonyl)imide (TFSI) anions and one or two types of ammonium, imidazolium or 1,2,3-triazolium counter-cations. Their physical, ion conducting and electrochemical properties are discussed based on the repeat unit charge density and structure of the cationic moieties. The comparison of several pairs of polyelectrolytes revealed that ionic conductivity is dependent on (1) the ratio between the number of charge carriers per monomer unit and the number of surrounding atoms/groups that can solvate the ions and (2) the nature of the cation. The highest conductivity (1.8 10 5 S cm 1 at 25 1C) was reached when PILs contain two 1,2,3-triazolium cations that are separated by an oxyethylene spacer. The incorporation of an additional type of cation (either imidazolium or ammonium with 1,2,3-triazolium) in one PIL allows its cathodic limit to be increased up to 0.4 V vs. Li/Li (70 1C) and the oxidation instability of 1,2,3-triazolium cations to be overcome.


Introduction
In the last decade, intensive efforts focused on flexible, lightweight and safe energy storage devices have been stimulated by the increased demand of next-generation portable and flexible electronics, wearable devices and electric cars. Both flexible solid-state supercapacitors (SCs) 1,2 and solid-state Li batteries 3-6 have attracted increased interest given the convincing advantages of transitioning from volatile, flammable and toxic liquid electrolytes to lightweight, non-volatile polymer electrolytes. In comparison with the existing technologies, solid-state SCs and Li batteries are smaller in size, light weight, and easy to handle, and offer a broader range of operating temperatures, and greater safety and reliability. 1,3,4,7,8 The development of safe, efficient solid-state SCs and lithium batteries requires solid polymer electrolytes (SPEs) with high ionic conductivity (410 À4 S cm À1 at 25 1C) as well as good electrochemical and thermal stabilities. 3,9 Among promising candidates for SPEs, a new class of polyelectrolytes, namely polymeric analogs of ionic liquids, a.k.a. poly(ionic liquid)s (PILs), has recently gained significant attention. [10][11][12][13][14][15][16][17] PILs can be considered as the macromolecular analogs of ionic liquids (ILs), in the best cases combining the advantages of polymers (viscoelasticity, processability, filmforming properties, etc.) and ILs (high thermal and electrochemical stabilities, enhanced ionic conductivity, etc.). 10,11,15 The use of PILs in SPEs instead of common neutral polymers offers several advantages. Firstly, PILs being polyelectrolytes, impart additional charges to the system. Secondly, when ILs are added to PILs, the optimal homogeneous distribution of charges can be reached at the molecular level due to strong electrostatic interactions, thus minimizing phase separation, IL leakage and providing the possibility of increasing the IL content up to 70-90 wt%. 9,18 Nowadays a broad variety of PILs are prepared using countless combinations of cations (ammonium, pyridinium, imidazolium, phosphonium, 1,2,3-and 1,2,4-triazoliums, etc.) and anions (halides, perfluorinated sulfonimides, etc.). 10,[19][20][21][22] An analysis of a Luxembourg Institute of Science and Technology (LIST), the published data allows the identification of the main factors influencing the bulk conductivity of PILs: the structure of the cation and anion, the length and type of the spacer between the polymer backbone and chemically grafted ion, the glass-transition temperature and the polymerization degree. 3,[10][11][12][13][14][15][16][17]23,24 It should be noted that all of the aforementioned factors are interrelated and that it is their combination that governs the ionic conductivity of PILs. The structures of the most highly conductive PILs synthesized to date [25][26][27][28][29][30][31] are listed in Scheme 1; the maximum bulk ionic conductivity reported in a neat, well-purified linear PIL is 6.7 Â 10 À5 S cm À1 at 30 1C under anhydrous conditions. 31 Although attempts to enhance the ionic conductivity of PILs have been made by varying the anion and cation structures, the length of the spacer and the placement of the ions in the polymer backbone vs. in the side chain, the influence of repeat unit charge density on the bulk conductivity of PILs has been scarcely addressed. 29,[32][33][34][35][36][37][38][39] As seen in Scheme 2, the maximum number of ion pairs per monomer unit reported to date is three, 32 and the structure/conductivity relationships remain sometimes contradictory. For instance, comparable hydroxide conductivities were reported for imidazolium-based PILs having cationic or dicationic repeat units and hydroxide counteranions. 33,34 Conversely, Fan et al. 35 and Drockenmuller et al. 36 observed a ca. 2 fold increase in ionic conductivity for PILs carrying one and two pendent imidazolium or 1,2,3-triazolium cations in each repeating unit (Scheme 2). In total contradiction, Gibson et al. observed a fourfold decrease in ionic conductivity for polyesters when the number of main-chain imidazolium cations was increased from one to two. 29 Finally, while extremely low ionic conductivity was reported for poly(1-vinyl-3-ethylimidazolium) bis(trifluoromethylsulfonyl)-imide, 37,38 the ionic conductivity of the only example of heterodicationic PIL reported so far (i.e. poly(N,N,N-trimethyl)-N-(1-vinylimidazolium-3-ethyl)ammonium bis(trifluoromethyl-sulfonyl)imide 39 ) has not been reported.
Scheme 1 An overview of the most highly conductive PILs reported to date.
Scheme 2 Examples of the repeat unit charge density influence on the ionic conductivity of PILs.
To fill this gap in fundamental knowledge concerning the influence of repeat unit charge density on the bulk ionic conductivity of SPEs, in this work we report the synthesis and comparison of eight PILs obtained from sequential AA + BB polyaddition by copper(I)-catalyzed azide-alkyne cycloaddition (CuAAC) using ammonium or imidazolium dialkynes with a,o-diazido-tetra(ethylene glycol) and subsequent N-alkylation of the 1,2,3-triazole groups. This versatile and general approach afforded the preparation of a series of PILs carrying TFSI counter-anions and differing by the chemical nature and number of cations in the repeat unit (Scheme 4). Their physical and electrochemical properties are discussed based on the repeat unit charge density as well as on the combination and chemical nature of the cations. These novel PILs exhibit conductivity up to 1.6 Â 10 À5 S cm À1 at 25 1C as well as electrochemical stability up to 3.6 V VS. Li + /Li.

Results and discussion
The analysis of Schemes 1 and 2 led us to the conclusion that the synthesis of (meth)acrylate or siloxane monomers with multiple ion pairs would require advanced multistep synthetic procedures. In contrast, synthesis of 1,2,3-triazolium-based PILs (TPILs) through AA + BB CuAAC polyaddition and subsequent quantitative N-alkylation of poly(1,2,3-triazole) intermediates allows unprecedented opportunities for macromolecular design taking advantage of the appealing attributes of the ''click chemistry'' philosophy. 14 Such an approach has been previously applied to the synthesis of aliphatic, aromatic, and ethylene glycol-based TPILs. 14,40,41 Thus, to fulfill the purpose of this study the synthetic platform towards TPILs was selected as the most favorable approach for the synthesis and investigation of a library of monocationic and heterodicationic PILs with tunable repeat unit charge density (Scheme 4 and Table 1). 1,11-Diazido-3,6,9-trioxaundecane (6) was chosen as the diazide monomer due to its easy accessibility and the presence of oxyethylene units that on one hand impart flexibility to the polymer chain and on another improve the solubility of ionic species, facilitate their dissociation, and promote an increase in the ionic conductivity of the resulting PILs. 10 A TFSI ion was selected as an anion providing PILs both with high ionic conductivity (Scheme 1) and electrochemical stability. 6

Synthesis of dialkyne monomers
The first step of our investigation started with the design of dialkyne monomers. As first candidates N,N-dimethyl-N,Ndipropargylammonium bis(trifluoromethylsulfonyl)imide (1) and N,N-dibutyl-N,N-dipropargylammonium bis(trifluoromethylsulfonyl)imide (2) each having one ammonium cation were prepared as reported previously. 42 Dipropargyl monomer 3 having two ammonium cations and a flexible n-hexyl spacer in between was designed in order to increase the number of cations and to enable sufficient ion motion (Scheme 3). The synthetic strategy for the preparation of 3 included N-alkylation of N,N,N 0 ,N 0 -tetramethyl-1,6-hexanediamine by propargyl bromide and an ion exchange reaction with excess LiTFSI. As a result, monomer 3 was obtained as a white crystalline solid showing a relatively low melting point (T m = 68-70 1C, Fig. S15 in the ESI †). Monomer 4 was further developed to contain two imidazolium cations and by analogy with 3 has the same linear n-hexyl spacer (Scheme 3). For monomer 4 the reaction pathway contained three steps: (1) synthesis of N-propargyl imidazole through N-alkylation of imidazole with propargyl tosylate, (2) N-alkylation of N-propargyl imidazole by 1,6-dibromohexane and (3) ion exchange reaction with an excess of LiTFSI. After isolation and purification monomer 4 was obtained as a slightly viscous yellow oil. DSC analysis confirmed the glassy behavior of 4 with a single glass transition temperature (T g = -56 1C) and the absence of any crystallization or melting processes (Fig. S16, ESI †).

Synthesis of PILs
Both ionic dialkynes 1-4 and neutral dialkyne 5 were first polymerized with 1,11-diazido-3,6,9-trioxaundecane (6) by AA + BB CuAAC polyaddition in N,N-dimethylformamide (DMF) (Scheme 4). In order to obtain high molar mass PILs, the previously optimized conditions involving CuIP(OEt) 3 as a catalyst and a monomer concentration of 20 wt% were used. 26,44,45 The change from CH 2 Cl 2 to more polar DMF was governed by the solubility of the formed polymers. The application of the abovementioned reaction conditions to the polyaddition of dialkynes 1-4 with diazide 6 resulted in the preparation of PILs having one (Scheme 4, polymers 7 and 8) or two (Scheme 4, polymers 9 and 10) ion pairs per repeat unit.
The molar mass of the obtained polymers was estimated by size exclusion chromatography (SEC). To suppress the insufficiently charged screening or the so-called ''polyelectrolyte effect'' during SEC studies, an electrolyte, namely LiTFSI, was added to the polymer solution in DMF. It was revealed that in all cases CuAAC polyaddition resulted in the formation of high molar mass polymers, with number average molar masses (M n ) ranging from 50 to 120 kg mol À1 for PILs 8-11 (Table 1). PIL 10, based on bisimidazolium monomer 4, showed the highest M n value most probably due to its better solubility (Table 1, polymer 10).
To increase the repeat unit charge density poly(1,2,3-triazole)s 8-11 were further subjected to N-alkylation reaction using iodomethane and ion exchange reaction with LiTFSI to obtain the corresponding 1,2,3-triazolium-containing analogues 12-15 (Scheme 4). PIL 7 was not considered further due to its limited solubility that prevented the quantitative N-alkylation of 1,2,3-triazole groups. It should be mentioned that the previously developed single step method involving N-alkylation of poly(1,2,3-triazole)s 8-11 by N-methyl bis(trifluoromethylsulfonyl)imide 26 could not be performed quantitatively even after 72 h at 90 1C. Probably this can be explained by steric hindrance neighboring the 1,2,3-triazole rings due to the near proximity of an ammonium or imidazolium cation and a bulky TFSI anion. Optimization of the reaction duration and the amount of CH 3 I allowed achieving quantitative N-alkylation of the 1,2,3-triazole groups as confirmed by 1 H NMR. Further ion exchange reaction with excess LiTFSI in aqueous medium led to the preparation of polymers 12-15 having from two to four ion pairs per repeat unit.
PILs 8-10 and 12-15 are amorphous and readily soluble in acetone, acetonitrile and polar aprotic solvents (i.e. DMF, DMSO, DMAc and NMP). Their structure, composition and purity were supported by 1 H, 13 C and 19 F NMR and FTIR spectroscopy (see e.g.

Thermal properties of PILs
Thermal properties of PILs 7-10 and 12-15 were assessed via differential scanning calorimetry (DSC) and thermogravimetric analysis (TGA). DSC analysis revealed several interconnections between T g and the chemical structure of PILs (e.g. Fig. S17 and S18 (ESI †) for polymers 10 and 14). Firstly, the increase in the length of side chains in the ammonium cations affords a decrease in T g ( Table 1, polymers 7 and 8). This tendency fully correlates with the melting point variation with the carbon number in the side alkyl chain for 1-methyl-3-alkyl imidazolium ILs 46 and with the size of the side chain in 1,2,3-triazolium PILs. 43 The separation of the ammonium cations by a flexible aliphatic spacer increases the flexibility of the polymer backbone and thus reduces T g ( Table 1, polymers 7 and 9). The transition from ammonium to imidazolium cations results in the lowering of PIL heat resistance (Table 1, polymers 9 and 10, 13 and 14), which was found to be in full agreement with data reported for (meth)acrylate-based PILs. 47,48 The correlation between repeat unit charge density and T g can be summarized as follows: Thus, it can be concluded that with the exception of polymer 7, which does not contain a flexible spacer between ammonium and 1,2,3-triazole groups, the increase in repeat unit charge density induces a rise in T g . This reduction of polymer chain mobility is most likely due to electrostatic interactions.
The thermal stability of PILs in air was found to be strongly dependent on the cation structure (Table 1  (T onset values) according to the cation's nature can be summarized as follows: (1,2,3-triazolium cations, 280 1C) 4 T onset 9 (ammonium cations, 270 1C) As generally observed for ILs 49 and methacrylate PILs, 47 the imidazolium PIL 10 demonstrates higher thermal stability than PILs 7, 8 and 9 having ammonium cations ( Table 1). The transition to 1,2,3-triazolium cations in polymer 15 results in the lowering of the T onset value in comparison with imidazolium analog 10. The thermal stability of PILs decreased following the orders below with respect to the repeat unit charge density: Analyzing the thermal stability data mentioned above, it is possible to summarize that the increase in the repeat unit charge density of PILs affords a decrease in their decomposition temperatures. This is mainly due to the limited thermal stability of the 1,2,3-triazolium cation towards de-N-alkylation. 50

Electrochemical properties of PILs
Ionic conductivities of polymer electrolytes were investigated as a function of temperature by electrochemical impedance spectroscopy (Table 1 and Fig. 1). Depending on the chemical nature of the cations and the repeat unit charge density the s values determined at 25 1C under anhydrous conditions for synthesized PILs varied from 9.8 Â 10 À10 to 1.8 Â 10 À5 S cm À1 .
The influence of the cation chemical structure on the ionic conductivity of monocationic PILs can be ranked as follows: s 15 (1,2,3-triazolium, 1.6 Â 10 À5 S cm À1 ) c s 10 (imidazolium, 6.0 Â 10 À7 S cm À1 ) 4 s 9 (ammonium, 5.8 Â 10 À8 S cm À1 ) This order fully correlates with the previously reported influence of cation structures on the conductivity of ILs. 51,52 The insertion of side ''dangling'' chains decreases T g and improves ionic conductivity as it can be concluded from the comparison of PILs 7 and 8 (Table 1). Such an increase in s can be explained by the decrease in packing density of the corresponding polyelectrolyte. 10 The separation of cations by an aliphatic spacer in 9 increases the solvation of ions and thus influences their dissociation and improves ionic conductivity ( Table 1, polymers 7 and 9). Finally, the influence of repeat unit charge density on the ionic conductivity of PILs can be ranked in the following decreasing orders: Taking these data into account it is possible to conclude that in the present work the repeat unit charge density vs. conductivity dependence passes through the maximum at PILs carrying two ion pairs. There are several possible explanations of the observed phenomenon. Possibly, the initial increase in the number of cations leads to the increase in the repeat unit charge density or in the concentration of free anions and results in the conductivity magnification. However, at some point in a solid polymer, only the surrounding atoms/groups can solvate the ions, the ratio between the number of charges and the solvating groups becomes too low for efficient dissociation and the conductivity starts to decrease. Following this assumption, the dilution of ions by incorporation of an aliphatic spacer leads to an immediate rise in ionic conductivity (Table 1, polymers 7 and 9). Another explanation can be connected with the highly documented influence of the PIL structure/composition on T g . 10 As the increase in repeat unit charge density generally induces a rise of T g (Table 1 and Fig. S20, ESI †) and as ionic conductivity has an inverse relationship with the latter, 10 it becomes obvious that the increase in the number of charges will reduce the ionic conductivity of PILs. In accordance with this assumption the transfer from monocationic or dicationic PILs (Table 1, polymers 8, 9, and 10) to tricationic or tetracationic ones (Table 1, polymers 12, 13, and 14) is accompanied by an increase in T g and as a result in a decrease in s. Finally, it seems obvious that 1,2,3-triazolium being the most ion conducting cation studied herein and in the literature, 31 its presence systematically enhances s, except for PIL 12, compared to the corresponding poly(1,2,3-triazole) analogue 8.
Additionally, the charge density of PILs was calculated as the number of charges per gram of polymeric material (Table 1 and Fig. S21, ESI †) and its influence on the ionic conductivity of PILs was estimated by the following decreasing orders: s 9 (1.90 mmol g À1 , 5.8 Â 10 À8 S cm À1 ) 4 s 13 (2.43 mmol g À1 , 8.3 Â 10 À9 S cm À1 ) 4 s 7 (1.55 mmol g À1 , 9.8 Â 10 À10 S cm À1 ) s 10 (1.82 mmol g À1 , 6.0 Â 10 À7 S cm À1 ) 4 s 14 (2.37 mmol g À1 , 4.2 Â 10 À7 S cm À1 ) s 15 (2.06 mmol g À1 , 1.8 Â 10 À5 S cm À1 ) 4 s 16 (1.97 mmol g À1 , 9.6 Â 10 À6 S cm À1 ) Similarly to repeat unit charge density, the charge density vs. conductivity dependence passes through the maximum at an average value of 1.92 mmol g À1 . It can also be concluded that the ionic conductivity of PILs is mainly ruled by segmental motion and T g of polyelectrolytes rather than by their charge density.
The conductivity of PILs as a function of inverse temperature between 10 and 110 1C is shown in Fig. 1. Independently of the repeat unit charge density the ionic conductivity of all studied PILs increased with increasing temperature and reached a level ranging from ca. 1 Â 10 À4 to 3 Â 10 À3 S cm À1 at 110 1C. The temperature dependence of conductivity did not follow linear Arrhenius behavior indicating that anion diffusion results from various mechanisms: hopping of TFSI anions along a positively charged polymer backbone and local segmental motion of polymer chains.
Besides ionic conductivity another important property that should be considered for practical applications of PILs in e.g. the field of energy is their electrochemical stability. The electrochemical stability towards oxidative processes at the interface with the cathode is particularly important for battery applications. 3,53 The electrochemical stability limits of PILs were assessed via cyclic voltammetry. As reasonable for electrochemical applications the ionic conductivity (410 À5 S cm À1 ) for PILs studied in this work was achieved only at 70 1C (Fig. 1); the latter was chosen as the experimental temperature for ESW studies. It should be noted that the selected temperature exceeds the T g of all PILs and therefore during measurements they were in a rubber-like elastic state. Fig. 2 shows the anodic and cathodic scans of most ionic conductive polymers 9, 10, 13, 14 and 15 at 70 1C. For all PILs two reversible redox peaks at À0.45 V and between À0.05 and 0.30 V vs. Li + /Li were observed that are associated with the reversible lithium plating and stripping at the copper electrode surface. Generally plating/stripping depends on the number of Li + ions that are able to reach the surface of the Cu electrode. In its turn, this process is primarily affected by the lithium ion transport 54 and secondarily by the overall conductivity, which instead considers the movement of all charges (anions and cations). In the studied systems the intensity of the peaks was directly dependent on the ionic transport in polymers. The higher is the overall conductivity of PIL and, respectively, the ion movement, the more intense were the lithium plating and stripping processes. Fig. 2 suggests that the cathodic limit potential is mainly determined by the reduction of the respective cations. The irreversible oxidation peak at 1.5 V vs. Li + /Li found for polymer 15 (Fig. 2c) can be attributed to the partial degradation of the 1,2,3-triazolium cations as was observed previously. 26 The increased cathodic stability up to À0.4 V vs. Li + /Li and observation for Li stripping and platting in comparison with previously reported 1,2,3-triazolium-based PILs 26 may on one hand arise from the presence of the oxyethylene chain that could contribute to preventing the full reduction of the 1,2,3triazolium cation. A similar influence of CH 2 CH 2 O groups on the cathodic limit of 1,2,3-triazolate anions was recently reported. 55 On another hand, the cathodic stability of 1,2,3triazolium-based PILs can be improved by the presence of LiTFSI as was noted formerly for pyrrolidinium ILs and PILs. 6,56 It was previously observed that 1,2,3-triazolium cations exhibit less cathodic stability than quaternary ammonium and imidazolium cations. 57 Following these observations for ILs, imidazolium-based polymer 10 shows better cathodic stability in comparison with 15 and reveals no oxidation peaks until Li plating at À0.41 V (Fig. 2b and c). An ammonium-based polymer 9 demonstrates one additional marked oxidation peak at ca. 1.5 V (Fig. 2a). Although in PIL 9 the ammonium cation is separated from the 1,2,3-triazole ring by a methylene group, these peaks can probably be attributed to the cleavage of the ring by Dimroth rearrangement. 58 Interestingly, the presence of ammonium and imidazolium cations in heterocationic PILs 13 and 14 fully suppresses the reduction of 1,2,3-triazolium cations, thus increasing the electrochemical stability of PILs ( Fig. 2a and b). Additionally, the couple of reversible peaks at 0.7 and 0.9 V versus Li + /Li may be attributed to a redox process involving oxide species at the electrode surface. The other couple of small peaks observable in the potential range between 1.5 and 2.7 V is most likely associated with the multistep decomposition of some impurity traces in PILs such as solvents. Indeed, these peaks disappear in the subsequent voltammetric cycles, which clearly states for the non-reproducibility of the processes and their insignificance for the overall performance of the system.
A solution of propargyl bromide (9.13 g, 76.8 mmol) in anhydrous CH 3 CN (10 mL) was added dropwise to a solution of N,N,N 0 ,N 0 -tetramethyl-1,6-hexanediamine (3.78 g, 21.9 mmol) in anhydrous CH 3 CN (20 mL) maintained at 0-5 1C under an inert atmosphere. After stirring for 5 minutes the start of the precipitation of a beige powder was observed. Stirring was continued for 1 h at 0-5 1C, then for 1 h at 25 1C and finally for 10 h at 55 1C. The reaction mixture was centrifuged for 5 min at 5000 rpm, the mother liquor was decanted and a fresh portion of CH 3 CN was added to the precipitate. After intense shaking the suspension was again centrifuged and this procedure was repeated three times. N,N,N 0 ,N 0 -Tetramethyl-N,N 0dipropargyl-hexane-1,6-diammonium bromide was isolated by filtration as a white-beige powder and dried for 8 h at 70 1C/1 mmHg (hereinafter with a special flask filled with P 2 O 5 and introduced into the vacuum line). Yield: 8.64 g (96%); m.p. = 204-206 1C.
Lithium bis(trifluoromethylsulfonyl)imide (3.53 g, 12.2 mmol) was dissolved in H 2 O (8 mL) and added dropwise to a solution of N,N,N 0 ,N 0 -tetramethyl-N,N 0 -dipropargyl-hexane-1,6-diammonium bromide (2.10 g, 5.12 mmol) in H 2 O (20 mL) at room temperature. The mixture was stirred for 2 h at 25 1C and the precipitation of a yellow powder was observed. The temperature was raised to 70 1C and stirring was continued for 1 h. After cooling down to room temperature the upper aqueous layer was decanted and the residual powder was redissolved in 80 mL of dichloromethane (CH 2 Cl 2 ). The CH 2 Cl 2 solution was washed with water (3 Â 30 mL) and dried over anhydrous MgSO 4 . The magnesium sulfate was filtered off, the decolorizing charcoal was added to the solution and the suspension was stirred at room temperature for another 2 h. The charcoal was filtered off and CH 2 Cl 2 was stripped off under reduced pressure. Bispropargyl monomer 3 was obtained as a white crystalline powder, which was dried at 50 1C/1 mmHg for 4 h. Yield A solution of propargyl tosylate (48.08 g, 228.7 mmol) in anhydrous CH 3 CN (100 mL) was added dropwise to a solution of imidazole (34.2 g, 503 mmol) in anhydrous CH 3 CN (140 mL) at 0-5 1C under an inert atmosphere. Stirring was continued for 1 h at 0-5 1C and then for 2 h at 40 1C. CH 3 CN was evaporated under reduced pressure at room temperature and the residual oil was distilled under vacuum (bp = 62 1C/0.08 mmHg). The obtained colorless oil still contained 10 mol% of imidazole ( 1 H NMR). To remove impurity 1.5 mL of 37 wt% HCl was added to the oil with vigorous stirring at room temperature. Stirring was continued for 15 minutes and CH 2 Cl 2 (100 mL) was added to the solution. The organic layer was separated, washed with H 2 O (3 Â 5 mL) and dried over anhydrous MgSO 4 . The magnesium sulfate was filtered off and CH 2 Cl 2 was evaporated under reduced pressure. N-Propargyl imidazole was obtained as a yellow oil, which was dried at 25 1C/1 mmHg for 4 h. Yield A solution of 1,6-dibromohexane (4.50 g, 18.5 mmol) in anhydrous CH 3 CN (25 mL) was added dropwise to a solution of N-propargyl imidazole (4.29 g, 40.6 mmol) in anhydrous CH 3 CN (25 mL) maintained at 0-5 1C under an inert atmosphere. The stirring was continued for 1 h at 0-5 1C, 2 h at 25 1C, 66 h at 45 1C and 23 h at 60 1C. The precipitation of the light-brown oil was observed and the emulsion was placed in the fridge (5 1C) for 48 h, whereupon the crystallization occurred. The light-brown crystals were filtered, washed with Et 2 O, then thrice with CH 2 Cl 2 , filtered again and smashed into powder with a mortar. 1,1 0 -(Hexane-1,6-diyl)bis(3-propargylimidazolium) bromide was crystallized from a CH 3 CN/H 2 O mixture (150/11 mL) as light-yellow crystals that were dried at 60 1C/1 mmHg for 12 h. Yield: 6.20 g (73%); m.p. = 143-144 1C (139 1C by DSC).
Lithium bis(trifluoromethylsulfonyl)imide (11.30 g, 39.3 mmol) was dissolved in H 2 O (25 mL) and added dropwise to a solution of 1,1 0 -(hexane-1,6-diyl)bis(3-propargyl-imidazolium) bromide (5.98 g, 13.1 mmol) in H 2 O (30 mL) at room temperature. The mixture was stirred for 2 h at 25 1C and the precipitation of a yellow powder was observed. The yellow powder was filtered and dissolved in acetone (60 mL). A solution of LiTFSI (6.50 g, 22.6 mmol) in acetone (15 mL) was added dropwise under stirring to the obtained solution. The reaction continued overnight at room temperature, whereupon the solvent was evaporated and the residual orange oil was extensively washed with H 2 O (5 Â 20 mL). The oil was dissolved in CH 3 CN and dried over anhydrous MgSO 4 . The magnesium sulfate was filtered off, the decolorizing charcoal was added to the solution and the suspension was stirred at room temperature for another 2 h. The charcoal was filtered off and CH 3 CN was evaporated under reduced pressure. Monomer 4 was obtained as a slightly viscous yellow oil, which was dried at 55 1C/1 mmHg for 12 h. Yield: 7.09 g (63%); T g = À56 1C (DSC); 1 H NMR (600 MHz, DMSO-d 6  CuAAC polyaddition of bisalkynes with 1,11-diazido-3,6,9trioxaundecane (6). Synthesis of poly(1,2,3-triazole)s 7-11 Polymers 7-11 were synthesized via AA + BB CuAAC polyaddition and a typical procedure is detailed below by the example of poly(1,2,3-triazole) 10 preparation. Dialkyne 4 (1.01 g, 1.18 mmol), diazide 6 (0.29 g, 1.18 mmol) and N,N-diisopropylethylamine (0.31 g, 2.36 mmol) were dissolved in anhydrous DMF (6 mL) under an inert atmosphere at room temperature. Afterwards CuIP(OEt) 3 (42.2 mg, 0.118 mmol) was added in one portion to the transparent yellow solution and stirring was continued in the dark for 68 h at 80 1C. The resulting brown solution was precipitated into excess of diethyl ether and the brown oil was centrifuged (10 000 rpm, 5 min). The oil was dissolved in CH 3  Iodomethane (0.93 g, 6.54 mmol) was added to a solution of poly(1,2,3-triazole) 10 (0.72 g, 0.654 mmol) in anhydrous DMF (10 mL) at room temperature under an inert atmosphere. Stirring was continued at 60 1C for 90 h, whereupon additional CH 3 I (0.50 g, 3.52 mmol) was added and the solution was further stirred at 80 1C for 72 h. The crude reaction mixture was diluted with DMF and precipitated two times in acetone to yield a dark brown viscous oil which was separated by centrifugation (10 000 rpm, 10 min).
The obtained oil was redissolved in H 2 O (20 mL) and an aqueous solution of LiTFSI (0.69 g, 2.4 mmol in 5 mL of H 2 O) was added dropwise under vigorous stirring at room temperature. The mixture was stirred for 12 h at 40 1C and the precipitation of a viscous brown oil was observed. The aqueous layer was decanted and the oil was washed with H 2 O (3 Â 20 mL), dissolved in acetone (6 mL) and precipitated again into an excess of H 2 O. Polymer 14 was recovered as a brown gummy solid after centrifugation (10 000 rpm, 10 min) and drying at 80 1C/1 mmHg for 12 h. Yield: 0.67 g (69%); T g = À1 1C (DSC); M n = 121.9 kDa, M w /M n = 1.48 (GPC); 1

Methods
NMR spectra were recorded on AMX-400, Avance II 500 MHz and Avance III HD 600 MHz spectrometers (Bruker) at 25 1C in the indicated deuterated solvents and are listed in ppm. The signal corresponding to the residual protons or carbons of the deuterated solvent was used as an internal standard for 1 H and 13 C NMR, respectively. C 6 F 6 was utilized as an external standard for 19 F NMR. IR spectra were acquired on a Nicolet Magna-750 Fourier IR-spectrometer using KBr pellets or on a Bruker Tensor 27 Fourier IR-spectrometer using ATR technology (128 scans, resolution is 2 cm À1 ) and Spectragryph optical spectroscopy software. 64 A 1200 Infinity gel permeation chromatograph (GPC, Agilent Technologies) was used to determine M n , M w and M w /M n of PILs. The chromatograph was equipped with an integrated IR detector, a PL PolarGel-M column and a PL PolarGel-M guard column (Agilent Technologies). The eluent was a 0.1 M solution of LiTFSI in DMF and the flow rate was 1.0 mL min À1 at 50 1C. Polystyrene standards (EasiVial PS-M, Agilent Technologies, M p = 162-500 Â 10 3 g mol À1 ) were used to perform calibration.
For Differential Scanning Calorimetry (DSC) measurements all samples (ionic monomers and PILs) were hermetically sealed in aluminum pans inside an argon-filled glove-box (MBRAUN MB-Labstar, H 2 O and O 2 content o 0.5 ppm). DSC experiments were performed on a DSC3 + STARe System differential calorimeter (Mettler Toledo). For PILs DSC measurements were conducted with a heating rate of 10 1C min À1 in the range of -80 to 150 1C, while for ionic monomers a very low rate of 3 1C min À1 was applied as recommended for highly viscous ionic liquids. 65 Glass transition temperatures (T g ) were determined during the second heating cycle.
Thermal gravimetric analysis (TGA) was carried out in air on a TGA2 STARe System (Mettler Toledo) applying a heating rate of 5 1C min À1 .
Ionic conductivity (s DC ) was determined by electrochemical impedance spectroscopy (EIS or complex alternating-current (AC) impedance spectroscopy) with a VSP potentiostat/galvanostat (Bio-Logic Science Instruments). To avoid any influence of moisture/humidity on the ionic conductivity of polymer electrolytes, the latter were preliminary dried at 60 1C/1 mmHg for 12 h in a B-585 oven (Buchi Glass Drying Oven, Switzerland) filled with P 2 O 5 and were transferred under vacuum inside an argon-filled glovebox. Polymers were sandwiched between two stainless steel electrodes. The distance between the electrodes was kept equal to 250 mm using a Teflon spacer ring with an inner area of 0.5 cm 2 . Symmetrical stainless steel/PIL/stainless steel assembly was clamped into the 2032 coin cell and afterwards was taken out from the glovebox. EIS experiments were carried out by applying a 10 mV perturbation in the frequency range from 10 À2 to 2 Â 10 5 Hz at the open circuit potential (OCV). The ohmic resistance (R O ) of the sample, obtained from the Nyquist plot at the low frequency end of the semicircle, was used to calculate the ionic conductivity using the following equation: where l is the sample thickness and A is the electrode area.
The measurements were carried out in the temperature range from 10 to 110 1C. The temperature was controlled using a programmed M-53 oven (Binder, Germany), where cells were allowed to reach thermal equilibrium for at least 30 minutes before each test. Cyclic voltammetry (CV) and VSP potentiostat/galvanostat (Bio-Logic Science Instruments, France) were used to determine the electrochemical stability window of solid polymer electrolytes at 70 1C. Prior to measurement PILs (0.2 g) were dissolved in anhydrous CH 3 CN (2 mL) inside the glovebox and 10 wt% of LiTFSI (0.02 g) were added under stirring until the formation of a clear solution. The solvent was evaporated under reduced pressure in a B-585 oven (Buchi Glass Drying Oven, Switzerland) and gummy samples were further dried there at 60 1C/1 mmHg for 12 h. To avoid moisture or oxygen contamination samples were afterwards transferred under vacuum back to an argon-filled glovebox, where they were used for the two-electrode 2032 coin cell assembly. The two-electrode cells were compiled by sandwiching samples between the working electrode and a lithium metal foil, which served as the reference and the counter electrode, simultaneously. Stainless steel and copper disks were used as working electrodes during anodic and cathodic stability measurements, respectively. To evaluate anodic limits, potential sweeps were carried out between OCV and 5.5 V vs. Li + /Li at a constant rate of 0.5 mV s À1 . To determine cathodic limits, potential sweeps were performed between OCV and À0.5 V vs. Li + /Li at the same constant rate.
The charge density of PILs as the number of charges per gram of material was calculated using the following equation: where n is the number of charges per repeat unit and M is the molar mass of the repeat unit.

Conclusions
The aim of this paper was to obtain polyelectrolytes with enhanced ionic conductivity and electrochemical stability as well as to fill the gap in fundamental knowledge concerning the influence of repeat unit charge density on the structure/ property relationships of PILs. Within this scope a series of TFSI-based cationic PILs was obtained from (1) CuAAC polyaddition using cationic ILMs and (2) subsequent N-alkylation of poly(1,2,3-triazole) intermediates. The synthesized PILs differed by the number of charge carriers per monomer unit (from 1 to 4 ion pairs) and by the nature of cation combinations (1,2,3-triazolium, imidazolium or ammonium as well as 1,2,3-triazolium/imidazolium or 1,2,3-triazolium/ammonium associations). Within the studied PILs thermal stability, heat resistance (glass transition temperature), ionic conductivity and electrochemical stability were all found to be significantly affected by repeat unit charge density. Generally, the higher the repeat unit charge density of PILs the higher their T g and the lower their ionic conductivity and thermal stability. The observed dependences passed through a maximum when PILs had two cations per monomer unit that were separated by alkyl or oxyethylene chains. For almost all combinations, 1,2,3-triazolium-containing PILs showed the highest ionic conductivity. A good cathodic stability on the Li metal electrode was seen when PILs with a mixed type of cation were tested. It is worth noting that the presence of ammonium and imidazolium cations in heterocationic PILs was able to hamper the reduction of 1,2,3triazolium cations and to increase the cathodic limit down to À0.4 V vs. Li + /Li at 70 1C. The highest ionic bulk conductivity (1.8 Â 10 À5 S cm À1 ) and anodic stability (4.8 V vs. Li + /Li at 70 1C) were demonstrated by PIL 15 containing solely 1,2,3-triazolium cations. Such PILs can be potential candidates for the next generation of safe and flexible polymer-based electrochemical devices requiring high conductivity in the solid state, for example supercapacitors, smart windows or actuators. However, when an application demands high electrochemical stability, it is preferred to include more stable cations such as ammonium or imidazolium in the polymer backbone. Therefore, the future application area of PILs with mixed type cations can include Li batteries.

Conflicts of interest
There are no conflicts to declare.