Introduction

From the last few decades, the demand for high-performance energy storage devices for practical applications in electronics, wearable devices etc. are increased. To design this flexible device, gel polymer electrolytes (GPE) plays a significant role. GPEs are ionically conducting membranes that can replace the conventional liquid electrolyte which is used as a separator in electrochemical devices [1, 2]. A good polymer electrolyte for energy storage devices particularly supercapacitors and batteries is the one which comprises properties like good ionic conductivity, high electrochemical stability window (ESW), proper interfacial contacts, good thermal and mechanical stability [3, 4]. Most of the above requirements are satisfied by using GPEs [5,6,7]. To design a novel polymer electrolyte, an effort has been put to increase the amorphicity in the polymer which in turn facilitates the fast ion motion while maintaining its mechanical stability [8, 9].

In the recent few years, there has been increasing a large interest in the ionic liquid (ILs) based polymer electrolytes for electrochemical applications. Ionic liquids (ILs) with ample available charged ion species, chemically stable over a practical range of temperature, non-hazardous and having low vapor pressure offer a better option for electrochemical double layer (EDL) capacitors [10, 11]. Generally, ionic liquids are molten salts which typically consist of cations and anions of dissimilar size. The physical properties of ILs like the relative size of ions and viscosity strongly affect the ionic conductivity of electrolyte which is one of the main parameters to design electrochemical devices [12, 13], as high viscosity of ILs lowers the power density of energy storage devices, particularly supercapacitors. Krause et al. [14] has reported that the mixture of 1-butyl-1-methylpyrrolidinium bis{(trifluoromethyl)sulfonyl}imide ([Pyrr14][TFSI]) and propylene carbonate (PC) exhibits higher conductivity and lower viscosity at 298 K than those of neat ([Pyrr14][TFSI]) and still the operating voltage was as high as 3.5 V. Similarly, high viscosity of commonly used ionic liquid such as EMImBF4 (37.7 cP), BMImBF4 (233 cP) and EMImTFSI (28 cP) reduce the conductivity of the gel polymer electrolyte which limit the performance of the devices [15]. Motivated by the above interesting studies by using an ionic liquid, in the present studies, 1-ethyl-2, 3-dimethylimidazoliumtetrafluoroborate (EDiMIM)(BF4) was used. (EDiMIM)(BF4) is chosen because of the small size of cations and high ionic conductivity which offers promising physicochemical properties and displays good performance as an electrolyte in terms of specific capacitance, energy density, and cycle life. The choice of host polymer determines whether the gel polymer electrolyte has an excellent matrix or not. Various polymers like polyacrylonitrile (PAN) [16, 17], polyethylene oxide (PEO) [18, 19], polymethylmethacrylate (PMMA) [20, 21], polyvinylidene fluoride (PVDF) [22] and poly (vinylidene fluoride-co-hexafluoropropylene) (PVDF-HFP) [23, 24] has been used. In the present studies, PVdF-HFP has been chosen because of its strong electron-withdrawing functional groups (-C-F-), high dielectric constant (\(\varepsilon\) = 8.4) which is suitable for the dissolution of magnesium salt to keep a high concentration of charge carriers. PVdF-HFP also contains more amorphous domains that are capable of trapping a large amount of liquid electrolyte and hence it is considered as one of the most promising polymer matrices for gel polymer electrolytes [24, 25].

Nowadays, the world is progressing towards high performance and environmentally friendly energy storage devices [26, 27]. It is also a known fact that lithium-ion is incorporated in most of the commercially available batteries because of its high capacity and excellent cycle life [3, 28, 29]. But the risk of limited lithium supply which results in its significant increase in the price cannot be ignored [2]. Consequently, its high time to develop long term sustainable solutions by using the materials which are abundantly available and at effective cost. There can be many alternatives like magnesium, sodium and calcium, but just like lithium, sodium metal also has a tendency to dendritic growth [7]. However, magnesium seems to be less prone to dendritic growth, which may be because of the lower self-diffusion barrier [8,9,10]. There are couple of advantages of using this light metals like natural abundance, low cost and safety. Moreover, magnesium ion is divalent and it accounts for a twofold increase in achievable energy density with respect to Li+ ion or Na+ ion for equal amount of reacted ions. Hence, in the present studies, magnesium ion based gel polymer electrolyte was developed.

In the present studies, gel polymer electrolytes using PVdF(HFP) as host polymer, ionic liquid, and magnesium perchlorate has been synthesized and optimized. The structural, electrical and electrochemical properties were discussed in detail in the result and discussion section. The synthesized polymer electrolyte was suitable for supercapacitor applications and it was already reported in our previous work [30].

Experimental

Preparation of gel polymer electrolytes

The ionic liquid 1-Ethyl-2,3-dimethylimidazoliumtetrafluoroborate (EDiMIM)(BF4), host polymer poly(vinyldeneflouride-co-hexafluoropropylene) [PVdF (HFP)] (PVdF(HFP), average MW ∼ 400,000), and the salt magnesium perchlorate Mg(ClO4)2 were obtained from Sigma Aldrich, propylene carbonate (PC) as plasticizer from Loba Chemie and acetonitrile (ACN) as an intermediate solvent from Merck, Germany was used to prepare ionic liquid-based gel polymer electrolyte films. All the chemicals were used without further purifications. All the experiments were carried out in ambient atmosphere. The ionic liquid-based gel polymer electrolyte films [PVdF(HFP)—(EDiMIM)(BF4)—PC-Mg(ClO4)2] were prepared by using "Solution Cast" method. In the process, initially, the liquid electrolyte was prepared by dissolving different concentrations of magnesium salt, Mg(ClO4)2 in propylene carbonate (PC) at RT. The different weight percent of the polymer, PVdF(HFP) and (EDiMIM)(BF4) were dissolved by using magnetic stirrer separately in common solvent acetonitrile (ACN) at 45 °C for ~ 7 to 8 h. The optimized composition of liquid electrolyte was then mixed with the optimized solution of PVdF(HFP)- (EDiMIM)(BF4)-ACN in different weight ratios and stirred thoroughly for ~ 8 h at 70 °C. The final optimized composition was [{PVdF(HFP)—EDiMIM(BF4)}(7:3)] (20 wt%)—[PC—Mg(ClO4)2 (0.3 M)] (80 wt%). The obtained viscous mixture was then cast over glass petri-dishes and allowed the films to dried slowly in room temperature, thereafter, free-standing gel polymer electrolyte films (400–500 µm) were obtained (Fig. 1).

Fig. 1
figure 1

Photograph of optimized gel polymer electrolyte film

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Instrumentation details

X-ray diffraction (XRD) patterns of the synthesized films were recorded using Bruker D8 Advance diffractometer with Cu-Kα radiation over the Bragg angle (2θ) range of 10–60°. The scan rate was fixed at 5° min−1. The surface morphology of the gel polymer electrolyte is studied with the help of a scanning electron microscope (JEOL JXA—8100 EPMA). Fourier transforms infrared (FTIR) spectra of the polymeric systems were recorded using Bruker vertex 70 spectrophotometers. The thermal analysis of the polymer gel systems was carried out by using differential scanning calorimetry (DSC) from -70 to 175 °C at a heating rate of 10 °C min-1 in presence of nitrogen atmosphere with the help of Mettler Toledo DSC 822E. The electrical conductivity of gel polymer electrolytes was measured by using complex impedance spectroscopic techniques and it is carried out using LCR Hi-Tester (HIOKI-3522–50, Japan) over the frequency range of 100 kHz to 1 Hz with a signal level of 10 mV. The samples were cut into the proper size and sandwiched between two stainless steel electrodes for taking the conductivity measurements. The ionic transport number and electrochemical stability of the gel polymer electrolytes were carried out by CHI 608C, CH Instruments, USA.

Results and discussion

Structural and morphological studies

Figure 2(a-c) depicts the XRD pattern of pure PVdF(HFP) films, polymer/ionic liquid blend film, and optimized GPE films. It can be seen from Fig. 2(a) that there exist predominant peaks at 2θ = 20.4° and 38° which corresponds to (020) and (021) crystalline peaks of PVdF(HFP) [31]. It confirms the partial crystallization of PVdF units and hence it shows the typical characteristics of a semi-crystalline morphology of the polymer, PVdF(HFP). Moreover, it is clear from Fig. 2(b), that when PVdF(HFP) is blended with the ionic liquid (EDiMIM)(BF4), no additional peak appears, though the intensity of crystalline peak decreases and gets broadened, suggesting a decrease in the crystallinity of the blend system. Finally, when a liquid electrolyte is immobilized in the polymer/ionic liquid blend, the peak at 2θ = 20° gets broadened and intense peak present at ~ 38° disappears, as can be seen from Fig. 2(c).

Fig. 2
figure 2

XRD pattern of (a) Pure PVdF(HFP) film, (b) PVdF(HFP)-EDiMIM(BF4) (7:3) polymer/ionic liquid blend, and (c) [{PVdF(HFP)-EDiMIM(BF4)}(7:3)](20 wt%)-[PC-Mg(ClO4)2(0.3 M)](80 wt%) polymer gel

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This suggests that the ionic liquid-based GPE is predominantly amorphous and its crystallinity gets depressed due to the proper immobilization and blending of liquid electrolyte in the optimized composition of polymer/ionic liquid blend systems at a molecular level. The amorphous nature of gel polymer electrolytes indicates an enhancement in its ionic conductivity, as it is well known that the ionic conduction occurs mainly through the amorphous phase of the polymeric system [31, 32].

Figure 3(a-c) shows the surface morphologies of pure PVdF(HFP) film, PVdF(HFP)/(EDiMIM)(BF4) blend film and optimized GPE film. Figure 3(b) shows the interconnected and uniformly distributed pore structure of the blend system, which can retain the liquid electrolytes solution in them. Further as can be seen from Fig. 3(c) that after addition of liquid electrolytes, homogeneously distributed pore morphology is observed which is capable for the better ion transport through the polymer chain/network of the optimized composition of GPE system which is suitable for energy storage devices like supercapacitors.

Fig. 3
figure 3

(a-c): SEM image of (a) Pure PVdF(HFP) film, (b)[PVdF(HFP)-EDiMIM(BF4)] (7:3) polymer/ionic liquid blend, and (c) [{PVdF(HFP)- EDiMIM(BF4)}(7:3)](20 wt%)-[PC-Mg(ClO4)2 (0.3 M)] (80 wt%) gel polymer electrolytes

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Thermal properties of gel polymer electrolytes were carried out by using differential scanning calorimetry (DSC) technique. DSC studies also confirm the proper blending of electrolyte films. The DSC profile of the pure PVdF(HFP) film, different weight ratios of polymer/ionic liquid blend films PVdF(HFP)-EDiMIM(BF4) and optimized composition of gel polymer electrolyte films are shown in Fig. 4(a-d). The endothermic peak at ~ 142 °C corresponds to the melting point of pure polymer PVdF(HFP). From Fig. 4(b) and (c), it can be seen that the melting point of polymer/ionic liquid blend systems PVdF(HFP)-EDiMIM(BF4) reduces to ~ 118 °C for (7:3) ratio and ~ 116 °C for (6:4) ratio respectively. On addition of optimized composition of liquid electrolyte in blend system, its melting point further decreases to ~ 105 °C, which is the indication of proper interaction of polymer, ionic liquid and salts in gel polymer electrolyte system [PVdF(HFP)-EDiMIM(BF4)-PC-Mg(ClO4)2].

Fig. 4
figure 4

DSC profile of (a) pure PVdF(HFP) film, (b) polymer/ionic liquid blend film [PVdF(HFP): EDiMIM(BF4)] (7:3), (c) [PVdF(HFP): EDiMIM(BF4)] (6:4), and (d) gel polymer electrolytes film [{PVdF(HFP): EDiMIM(BF4)} (7:3)](20 wt%)-[{PC-Mg(ClO4)2} (0.3 M)](80 wt%)

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The existence of a broader and asymmetrical melting peak indicates the entrapment of the appreciable amount of liquid electrolyte components in the polymer matrix, which causes the enhancement of amorphous content of the gel polymer electrolyte systems and thereby increasing its electrical conductivity accordingly (also confirmed from SEM studies). The sharp peak at about -38 °C has been observed in GPE as can be seen from Fig. 4(d), which indicates the presence of another separate crystalline phase due to the possible interaction of EDiMIM(BF4) with polar PVdF(HFP).

Figure 5(a-f) shows the comparative FTIR spectra of pure PVdF(HFP), polymer-ionic liquid PVdF(HFP)- (EDiMIM)(BF4) blend films, PVdF(HFP)-(EDiMIM)(BF4)-PC-Mg(ClO4)2 polymer gel electrolytes film in the wavenumber region varying from 450–4000 cm−1. It was mainly performed to visualize the interaction of Mg2+ ion and ionic liquid with the host polymer PVdF(HFP) at a microscopic level in the optimized gel polymer electrolyte. It also throws light on the conformational changes by the entrapment of liquid electrolyte PC-Mg(ClO4)2 and ionic liquid (EDiMIM)(BF4) in the polymer matrix.

Fig. 5
figure 5

FTIR Spectra of (a) Pure PVdF(HFP) film, different ratios of polymer/ionic liquid blend films (b) [PVdF(HFP)-EDiMIM(BF4)](8:2), (c) [PVdF(HFP)-EDiMIM(BF4)](7:3), (d) [PVdF(HFP)-EDiMIM(BF4)] (6:4) and polymer gel electrolyte films in different ratios of (e) [{PVdF(HFP)-EDiMIM(BF4)}(7:3)](20 wt%)-[PC-Mg(ClO4)2 (0.3 M](80 wt%) (f) [{PVdF(HFP)-EDiMIM(BF4)}(7:3)] (30 wt%)—[PC-Mg(ClO4)2 (0.3 M)] (70 wt%)

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From Fig. 5(a), it is clear that the spectrum of pure PVdF(HFP) contains the vibrational band at wavenumbers 478, 669, 772, 837, 880, 1185 and 1793 cm−1 that corresponds to vinylidene group, CF2 bending of the vinylidene band, CF3 deformation vibration, C(F)-C(H)-C(F) skeletal bending vibration, CH2 wagging vibration of vinylidene band, out-of-plane C-H bending, -C-F- stretching and CF = CF2 stretching vibration of the vinylidene groups respectively [33,34,35], the important bands are summarized in Table 1. The higher frequencies of 3020 and 2986 cm−1, it is assigned to CH2 asymmetric and symmetric stretching vibration respectively (Table 1).

Table 1 Assignment of important FTIR bands of pure PVdF(HFP), polymer/ionic liquid blend (PVdF(HFP) (EDiMIM (BF4) and optimized gel polymer electrolytes
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Figure 5(b-d) shows some additional bands at 1074, 1545, 1593, and 1635 cm−1, which confirms that ionic liquid is well blended with the host polymer at a molecular level. The bands at 1074 and 1545 cm−1 corresponds to the EDiMIM+ peak and are assigned for CH2(N) bending, N–H bending vibrations respectively [36,37,38]. The peaks observed at 1593 and 1635 cm−1 are attributed to the C = C and C-N stretching vibrations of imidazolium cation.

Further, in Fig. 5(e–f), bands at 1052, 930 and 627 cm−1 were observed and it is due to the presence of plasticizer (PC) and anion (ClO4)− in the ionic liquid-based gel polymer electrolytes. The vibrational bands at 1052 and 930 cm−1 are assigned to the C = O stretching and C-O stretching of the plasticizer (PC) [39]. The vibrational frequency at 627 cm−1 is attributed to the ion-pairing of (ClO4)− anions [40, 41]. The increased or decreased pattern of frequency shifting peaks from pure PVdF(HFP) spectra shows the strong interactions of polymer with the ionic liquid and liquid electrolytes respectively in the ionic liquid-based gel polymer electrolytes. However, disappearance of bands associated with crystalline α-phase and broadening of the band of amorphous phase of the polymer indicate a decrease in crystallinity and the increment of amorphous phase in gel polymer electrolyte system which is advantageous from application point of view.

Electrical and electrochemical properties

The optimization and room temperature ionic conductivity of [{PVdF(HFP)-EDiMIM(BF4)(7:3)}(20 wt%)-{PC-Mg(ClO4)2}(80 wt%)] polymer electrolyte system has summarized in Table 2 and the detail discussion and analysis are reported in our previous work [30].

Table 2 Electrical conductivity of optimized ionic liquid electrolyte, polymer/ionic liquid blend, optimized gel polymer electrolytes
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Temperature dependence conductivity studies of the optimized composition of gel polymer electrolytes are shown in Fig. 6 and it reflects the nonlinear behavior and following the Vogel-Tammann-Fulcher (VTF) [43] characteristics of the system which can be expressed as:

Fig. 6
figure 6

Variation of electrical conductivity of optimized gel polymer electrolytes as a function of temperature

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$$\sigma =A{T}^{-1/2}{exp}\left(\frac{-B}{T-{T}_{0}}\right)$$
(1)

where the parameter B has a dimension of energy and is related to the critical free volume for ion transport, A is a pre-exponential factor, which represents the conductivity at infinitely high temperature and T0 is equilibrium glass transition temperature close to the Tg values. These parameters have been evaluated by the non-linear least-squares fitting of the data and are enlisted in Table 3. The increase in the conductivity with the temperature of the gel polymer electrolytes can be explained based on the free volume mechanism as proposed by Kim et.al. [42].

Table 3 Different parameter (A, B and T0) for ionic liquid-based gel polymer electrolyte obtained by nonlinear least-square fitting of conductivity data to VTF equation
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According to this concept, such behavior is observed due to the hopping mechanism between coordinating sites and segmental motion of the polymer matrix. With the increase in temperature amorphous nature increases which is favorable for the hopping of ions within a polymeric network from one chain to another and leads to the enhancement in ionic conductivity [43, 44]. It can also be observed from the plot that the optimized composition of gel polymer electrolyte shows electrical conductivity of the order of ~ 10–3 S cm−1 at room temperature (~ 25 °C) and the order of ~ 10–2 S cm−1 at 100 °C, showing a span of wider temperature range which is beneficial for temperature dependence electrochemical devices.

Dielectric studies were also carried out to study the ionic transport phenomenon of ionic liquid-based gel polymer electrolyte system [45]. The real (εr) and imaginary part (εi) of dielectric studies provide information about the storage and loss of energy in every cycle of the applied electric field. Figure 7(a-b) shows the dielectric constant (εr) and dielectric loss (εi) as a function of frequency at different temperatures for an optimized system. From Fig. 7(a) it can be seen that the values of εr is rising very sharply towards low-frequency region, which can be explained based on the electrode polarization effect [46]. This low-frequency dispersion region is attributed to the high contribution of charge accumulation at the electrode–electrolyte interfaces. In higher frequency regions it was found that the value of εr is almost constant with frequency. It happens so because the periodic reversal of the electric field occurs so fast that the charge carriers will not get sufficient time to orient themselves in the field direction. Hence there is no excess ion diffusion in the direction of the field and it further leads to the decrease in the values of dielectric constant [47]. Again, from Fig. 7(b), it can be seen that the dielectric loss (εi) becomes very large towards the lower frequency region. It is due to the motion of free charge carriers within the material.

Fig. 7
figure 7

(a) Variation of dielectric constant of gel polymer electrolytes system as a function of frequency at various temperature and (b) Variation of dielectric loss of gel polymer electrolytes system as a function of frequency at various temperatures

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Modulus spectroscopy studies were carried out to understand the bulk properties of the materials which gives the insight of electrode and grain boundaries effect. Figure 8(a-b) shows the real part (Mr) and the imaginary part (Mi) of electrical modulus as a function of frequency at various temperatures for gel polymer electrolytes. It has been observed that the values of Mr and Mi were increased in the high-frequency region and provide a long tail towards lower frequency. The peaks in the modulus formalism at higher frequencies show that the gel polymer electrolyte films are predominantly ionic conductors [48]. It has also been observed from the plots that the values of Mr and Mi decrease towards lower frequencies; it might be because of the electrode polarization phenomenon which makes a negligible contribution, and its effect seems to be vanishing towards lower frequency domain. The increasing peak of Fig. 8(b) can be related to the translational ion dynamics and mirrors the conductivity relaxation of the mobile ions. The shapes of all the plots are identical for all temperatures and show a single relaxation peak in the range of temperature and frequency determined under present studies. The angular frequency,ωc at which the maximum Mi occurs represents the relaxation time, τc and are related to each other by a mathematical τcωc = 1 [49]. Further, it is also observed that Mi shows a slightly asymmetric peak at each temperature. The peak shifts towards higher frequency regions with increasing temperature. The broad nature of peaks can be understood as being the result of distributions of relaxation time. These peaks are broader than the Debye peak, which is treated as an ideal ionic conductor represented by a single parallel RC element.

Fig. 8
figure 8

(a) Variation of real part of modulus of gel polymer electrolytes as function of frequency at various temperature and (b) Variation of imaginary part of modulus of gel polymer electrolytes as a function of frequency at various temperatures

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Figure 9 shows the conductance spectra for ionic liquid-based gel polymer electrolytes, [PVdF(HFP)-EDiMIM(BF4)- PC-Mg(ClO4)2 at different temperatures. The spectra consist of two regions, a low-frequency dispersive region due to electrode–electrolyte interfacial phenomena and the plateau region representing the dc conductivity. As the frequency decreases, more and more charge accumulation occurs at the electrode–electrolyte interfaces which lead to a decrease in the number of mobile ions and eventually to a drop in conductivity towards lower frequency region. In the high-frequency region, the mobility of charge carriers is high and hence the conductivity increases with frequency [50, 51]. It has been observed that the dc conductivity increases with temperature which suggests that the free volume around the polymer chain causes the mobility of ions and polymer segments. The phenomenon of the conductivity dispersion is generally represented by Jonscher's law [50].

Fig. 9
figure 9

Variation of ionic conductivity as a function of frequency with temperature for gel polymer electrolytes system

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Mathematically it can be written as σ(ω) = σdc + A ωn, where σdc is the direct current (dc) conductivity of the sample, A is a constant for a particular temperature and n is the frequency exponent lying in between the range of 0 < n < 1. The values of n represent the degree of interaction between the mobile ions and the environments surrounding them. For ionic conductors this value lies between 0.5 and 1, indicating the ideal long-range pathway diffusion of the ions and can be best explained by hopping models [52]. When the value of n = 0, the motion is completely random and independent Debye like ion hopping mechanism is taking place in the system. The high probability of forward–backward hopping at higher frequencies together with the relaxation of the dynamic cage potential is mainly responsible for the observation of high-frequency dispersion in its conductivity.

The relaxation phenomenon of any gel polymer electrolyte materials can be described by its dielectric tangent loss (tan δ). It provides information about the energy lost or dissipated per cycle to the energy stored. Figure 10 shows the plot of tangent loss as a function of frequency at different temperature for the optimized polymer gel electrolytes, [{PVdF(HFP)-EDiMIM(BF4)}(7:3)](20 wt%)-[{PC-Mg(ClO4)2}(0.3 M)](80 wt%).

Fig. 10
figure 10

Variation of loss tangent (tan δ) as a function of frequency at different temperature for gel polymer electrolytes

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It is observed from the plot that the general trend shows the increase in the values of loss tangent with increasing frequency at different temperatures, thereafter it passes through its maxima and finally decreases. Further, it can be seen that by increasing the temperature, the values of loss tangent maxima and peak intensity get shifted towards a higher frequency side. This phenomenon can be understood in terms of relaxation due to the ionic transport processes of the bulk and the grain boundaries [52,53,54].

The linear sweep voltammogram (LSV) curves are recorded for the optimized system at a scan rate of 5 mV s−1 and is depicted in Fig. 11. The working voltage range of the electrochemical device is strongly dependent on the potential window of the GPEs. This is a very important parameter that gives the optimum voltage stability range of the electrolyte materials from the application point of view. In the present studies, the electrochemical stability of polymer gel electrolyte has been measured using linear sweep cyclic voltammetry, by sandwiching the gel electrolytes in between two stainless steel (SS) electrodes. From the figure, it can be seen that the current values increase gradually by an increase in applied voltage across the cell up to a certain voltage and thereafter it increases abruptly. The sudden increase in the value of current shows the decomposition of the electrolyte materials; hence the values of the potential window provide information about the polymeric system up to which it can work safely. In the present studies, ionic liquid-based gel polymer electrolytes show the potential window of ~ 6.0 V, which represents the potential limit up to which any electrochemical device using this electrolyte can work safely without decomposition.

Fig. 11
figure 11

Linear sweep cyclic voltammetry curves of gel polymer electrolytes cell SS| PGE|SS recorded at room temperature at a scan rate 5 mV s−1

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The ionic transport number of gel polymer electrolyte in the present studies has also been calculated by using dc polarization method. Figure 12 shows the dc polarization curve of gel polymer electrolytes, sandwiched between symmetrical SS electrodes. In this method, a typical cell SS | [{PVdF(HFP)-EDiMIM(BF4)} (7:3)] (20 wt%—[{PC-Mg(ClO4)2} (0.3 M)](80 wt%) | SS is being polarized by applying a potential of 1.0 V and its corresponding current has been measured as a function of time. The value of the ionic transport number is found to be 0.97 which confirms that the overall conductivity of ionic liquid-based gel polymer electrolytes using magnesium salt is predominantly ionic.

Fig. 12
figure 12

dc polarization curve as a function of time for polymer gel electrolyte

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The optimized system is already tested for supercapacitor application by using activated charcoal as an electrode material. In that paper, we have reported very promising results like capacitance value of 868 mF cm−2 with energy density of 55 Wh kg−1 and power density of 2 kW kg−1 has been achieved by using activated carbon as electrode with present electrolyte films [30].

Conclusions

An ionic liquid-based and magnesium ion conducting gel polymer electrolyte were prepared and its structural, electrical and electrochemical properties were discussed in detail. It was observed that 20 wt % of polymer/ionic liquid blend, PVdF(HFP)-EDiMIM(BF4) (7:3) is optimized for the synthesis of gel polymer electrolytes having an electrical conductivity of the order of 8.4 × 10–3 S cm−1 at room temperature with acceptable mechanical stability. The SEM and XRD studies confirm the porous and predominantly amorphous nature of the prepared electrolyte material along with the good liquid retention capability which supports the electrical conductivity through its polymer matrix.

FTIR studies show the proper interaction of polymer, ionic liquid and liquid electrolytes at a microscopic level.

The temperature dependence studies for electrical conductivity (σ) show the VTF behavior of the gel polymer electrolytes and its activation energy has been evaluated by the non-linear least squares curve fitting of the data and it is found to be of the order of Ea = 0.33 eV. The highest conducting composition carries a significant electrochemical stability window of ~ 6.0 V which confirms its suitability for electrochemical applications. The ionic transport number for GPE is 0.97, which shows that the charge transport mechanism is predominantly ionic. Dielectric and modulus spectra studies provides the information of electrode polarization as well as dipole relaxation properties of polymeric materials. As it has been mentioned earlier that the electrolyte material was suitable for supercapacitor application using activated carbon as electrode material.