The Study of Plasticized Sodium Ion Conducting Polymer Blend Electrolyte Membranes Based on Chitosan/Dextran Biopolymers: Ion Transport, Structural, Morphological and Potential Stability

Abstract

The polymer electrolyte system of chitosan/dextran-NaTf with various glycerol concentrations is prepared in this study. The electrical impedance spectroscopy (EIS) study shows that the addition of glycerol increases the ionic conductivity of the electrolyte at room temperature. The highest conducting plasticized electrolyte shows the maximum DC ionic conductivity of 6.10 × 10⁻⁵ S/cm. Field emission scanning electron microscopy (FESEM) is used to investigate the effect of plasticizer on film morphology. The interaction between the electrolyte components is confirmed from the existence of the O–H, C–H, carboxamide, and amine groups. The XRD study is used to determine the degree of crystallinity. The transport parameters of number density (n), ionic mobility (µ), and diffusion coefficient (D) of ions are determined using the percentage of free ions, due to the asymmetric vibration (υ_as(SO₃)) and symmetric vibration (υ_s(SO₃)) bands. The dielectric property and relaxation time are proved the non-Debye behavior of the electrolyte system. This behavior model is further verified by the existence of the incomplete semicircle arc from the Argand plot. Transference numbers of ion (t_ion) and electron (t_e) for the highest conducting plasticized electrolyte are identified to be 0.988 and 0.012, respectively, confirming that the ions are the dominant charge carriers. The t_ion value are used to further examine the contribution of ions in the values of the diffusion coefficient and mobility of ions. Linear sweep voltammetry (LSV) shows the potential window for the electrolyte is 2.55 V, indicating it to be a promising electrolyte for application in electrochemical energy storage devices.

1. Introduction

Natural solid polymer electrolytes (SPEs) have been widely applied to the development of energy storage devices [1]. Generally, all electrochemical devices, such as dye-sensitized solar cells, supercapacitors (SCs), batteries, and fuel cells, consist of two electrodes (a cathode and an anode) and an electrolyte. SCs or electrical double-layer capacitors (EDLCs) are certified to be one of the important power sources in certain devices, for example, memory back-ups, electrical vehicles, and digital communications, owing to their long cycle life and large power density [2]. ELDCs are prepared using two carbon electrodes separated by an electrolyte. Electrolytes have a crucial role in determining the electrochemical devices’ performance [1,3]. Numerous studies have documented the use of gel-based electrolytes in EDLCs [4,5]. Liquid electrolytes are also employed in lithium batteries [6], however liquid electrolytes have some drawbacks, such as leakage [7] and corrosion [8]. There has been plenty of research done to substitute liquid electrolytes with SPEs. Thus, numerous researchers have focused on SPE developments owing to its benefits, such as low chemical resistivity, stable potential window of more than 1 V, easy processability, good contact between electrodes, and electrolyte, very good mechanical strength, cheap, light in weight, and good ionic conductivity, which are vital for electrochemical energy storage devices [9,10,11].

In addition, the blending of polymers to produce an SPE is considered as an effective method to enhance the durability of an electrolyte [12,13,14,15]. Blending of polymers is a frequently used technique to modify the properties of the polymers which are not available in homo-polymers. Through this method, the degree of crystallinity of the polymers is reduced, due to the intermolecular interaction between blended polymers and increased convenience of site vacancy for ions hopping, which, in turn, increases the ionic conductivity of the electrolytes [12,13,14,15]. This will be beneficial for future energy storage device applications [12,13,14,15]. Natural polymers used in this field will minimally impact the environment, due to their biodegradable and other eco-friendly properties [16]. All these will aid in reducing the weaknesses of conventional batteries, including pollution [17]. In this regard, two biodegradable polymers, chitosan (CS) and dextran, were chosen to be used in this study. CS is obtained through a deacetylation process of chitin and has a few properties, such as biodegradable and biocompatible, which make it a suitable candidate to be explored as a polymer host [18,19]. The hydroxyl, acetamido, and amino groups in the structure of CS provide interaction sites within the electrolyte system [20,21]. Dextran is a natural polymer that is produced by the fermentation process of leuconostocmesenteroides bacteria, which have been widely explored in this area of study [22,23,24]. Moreover, various oxygen groups at the linkages of 1,6,-α-D-glucopyranosidic bond in the polymer chain of dextran help in increasing the conductivity [22]. Normally, dextran is used in the medical area, for example, as a drug carrier, blood substitute, in bone curing, and plasma modification. In the dextran structure, the presence of hydroxyl group ensures the polymer to be used as an ionic conductor [25].

Meanwhile, the selection of proton providers is also important to enhance the ionic conductivity of the system because the good performance of energy devices is highly reliant on the conductivity value of the electrolyte. Sodium-based salt is also found to give an equivalent overall performance in terms of conductivity (~10⁻⁴ S/cm) and stability as the salt that contains NH₄⁺ ion [1,12] and Mg²⁺ ion [26,27], and it can also be an alternative to lithium-based salts that might affect the environment [28]. The addition of sodium triflate (NaTf) salt was reported to increase the conductivity of polyvinyl alcohol-based electrolytes from 4.87 × 10⁻⁶ S/cm to 2.31 × 10⁻³ S/cm at room temperature [29]. Poy et al. [30] also studied the effect of sodium-based salt on their two different electrolyte systems (sodium trifluoromethanesulfonimide (NaTFSI) and sodium trifluoromethanesulfonate (NaOTF)) and found that the conductivity of the systems was increased from 2.34 × 10⁻⁴ S cm⁻¹ to 1.79 × 10⁻³ S cm⁻¹ as the concentration of salt increased from 10 wt. % to 50 wt. %. Our previous work reported a study on dielectric properties and relaxation dynamics of the CS-NaTf electrolytes, and it was revealed that rising temperature from 303 K to 363 K could also enhance the conductivity of CS-NaTf electrolytes [31]. Furthermore, the incorporation of plasticizer can also further increase the ionic conductivity, as well as other significant parameters, such as the amorphous and thermal properties [32]. This is because the plasticizer, such as glycerol, promotes dissociation of ions, which contributes to a high performance of the electrolytes, especially for future applications [33,34]. The glycerol can dissociate more salts and disrupt hydrogen bonding between polymer chains. Thus, this improves the amorphous phase of the prepared samples, which acts as a pathway for ions conduction [24,28]. Additionally, more free ions will be available for conduction [33,34]. Glycerol also has been acknowledged and proven to be a good plasticizer for polymer electrolytes [26,35,36]. Herein, the blend of CS –dextran (60:40) wt.% is selected to be the polymer host in the present work, due to the promising characteristics discussed earlier in this section [24,37]. This work is focusing on the effect of different concentrations of glycerol on the chitosan /dextran-NaTf electrolyte system by using several characterization techniques.

Table 1. Symbols and their corresponding physical significances.

Symbols	Physical Significances
SPE	Solid polymer electrolyte
EDLC	Electric double-layer capacitor
CPE	Constant phase element in F
Rb	Bulk resistance in Ω
tion	Ion transference number
te	Electron transference number
σ	DC ionic conductivity in S/cm
t	Thickness of the sample in cm
A	Area of the sample in cm2
NA	Avogadro’s number
M	Number of moles of glycerol
T	Temperature in K
KB	Boltzmann constant in J/K
VTotal	Total volume of the polymer electrolytes
D	Diffusion coefficient of ions in cm2 s−1
µ	Mobility of ions in cm2 V−1 s−1
n	Number density of ions in cm−3
P	Deviation from the axes
C	Capacitance in F
ω	Angular frequency in Hz
Co	Vacuum capacitance in F
ε′	Dielectric constant
ε″	Dielectric loss
Ii	Initial current
Iss	Steady state current
µ+	Mobility of cations in cm2 V−1 s−1
µ−	Mobility of anions in cm2 V−1 s−1
D+	Diffusion coefficient of cations in cm2 s−1
D−	Diffusion coefficient of anions in cm2 s−1

lists symbols and their corresponding physical significances.

2. Methodology

2.1. Sample Preparation

All reagents used in this work were obtained from Sigma-Aldrich (Kuala Lumpur, Malaysia) and used to prepare electrolyte samples without further purification. Firstly, dextran (0.4 g) and CS (0.6 g) were separately dissolved in 1 wt.% of acetic acid (50 mL) for about 1.5 h at room temperature. The dextran and CS solutions were then mixed together homogeneously for 3 h. Sodium triflate (NaTf) salt (40 wt.%) was added to the dextran-CS blend solution and constantly stirred until the salt has completely dissolved. Glycerol, as a plasticizer in the system, was added at a specific concentration according to those tabulated in

Table 2. Designation of the polymer electrolytes with different amounts of glycerol.

Glycerol (wt.%)	Designation
12	B1
28	B2
42	B3

and then correspondingly designated as those in Table 2 as well. Next, a solution casting technique was employed to obtain polymer electrolyte films. In this technique, polymer electrolytes were placed in Petri dishes for drying of samples. Then, the further drying process was carried out by keeping the Petri dishes in a desiccator with blue silica gel to produce solvent-free samples at ambient temperature. The sample preparation processes were carried out at room temperature with ~50% relative humidity. The thickness of the electrolyte samples was in the range of 0.028–0.031 cm, which was measured using a high accuracy micrometer (Mitutoyo, Coventry, UK).

2.2. Impedance, Morphology, and Fourier Transform Infrared Analyses

Successfully prepared electrolytes were firstly tested using an LCR meter (HIOKI 3531 Z Hi-tester, Nagano, Japan) to study their impedance properties and measure the real (Z_r) and imaginary (Z_i) parts of impedance. The measurement took place at room temperature with a frequency range of 50 Hz to 5 MHz. The DC potential for the experiment was 0.04 V. In this measurement, the polymer electrolyte samples with 2 cm in diameter (measure with a Vernier) were kept between two stainless-steel blocking electrodes under spring pressure. Field emission scanning electron microscopy (FESEM) was employed using a Hitachi SU8220 (Tokyo, Japan) at 500× magnification. The morphology of the samples was studied using the FESEM technique. On the other hand, the study on the interaction of the different components of the electrolytes, including polymers, salt, and plasticizer, was conducted using Fourier transform infrared (FTIR) spectroscopy. A Spotlight 400 Perkin–Elmer spectrometer was employed for this analysis with a resolution of 1 cm⁻¹ (450–4000 cm⁻¹). A deconvolution technique was used to extract any overlapping peaks. Correction of baseline and curve fitting were performed based on a Gaussian-Lorentzian function.

2.3. Transference Number Measurement (TNM) and Linear Sweep Voltammetry (LSV) Measurement

Electrochemical properties of the SPEs were initially investigated by TNM using a V&A Instrument (DP3003) (V&A Instrument, Shanghai, China) connected with a digital DC power supply. The circuit diagram for the TNM measurement was shown in our previous work, as reported in Reference [38]. This method was used to determine the ionic transference number (t_ion) and the electronic transference number (t_e). A working voltage of 0.20 V was applied at ambient temperature. Moreover, it is also important to identify the electrochemical stability and breakdown voltage of an electrolyte. For this purpose, LSV was conducted using a potentiostat (DY2300) (Neware, Shenzhen, China) with a scan rate of 10 mV/s. Figure 1 shows the schematic illustration of the electrodes and electrolyte arrangement for the LSV analysis, where only the highest conducting electrolyte was utilized. Stainless-steel was used as a reference, working, and counter (auxiliary) electrodes.

3. Result and Discussion

3.1. Ionic Conductivity Studies

Cole–Cole plots of (B1, B2, and B3) at (stainless-steel electrodes) are shown together with the fitted curves in Figure 2. In each case, the electrical impedance spectroscopy (EIS) data were fitted to an equivalent circuit consisting of two capacitors arising from the constant phase element (CPE) of the immobile polymer chains, and a resistor is the bulk resistance (R_b) of the system, as presented in the inset of Figure 2 [39]. For the B1 and B2 electrolytes, the parallel arrangement of R_b and CPE1 yielded a semicircular arc observed in both Cole–Cole plots signify the charge conductivity within the electrolytes. The spike/tail at the low frequency region in the EIS plots represents the charge accumulation during the polarization process, due to the diffusion mechanism of the system [40,41].

The diameter of the semicircle in B1 is found to become smaller with the addition of glycerol and disappeared in the B3 electrolyte. The fall in the R_b value with increasing plasticizer content is interconnected to the ability of glycerol to detach more NaTf salt and disrupt hydrogen bond between polymer chains. This improves the amorphous phase of the polymer electrolyte, which acts as a pathway for ion conduction, and also increases the number of movable ions. Consequently, the R_b value will drop and give rise to the conductivity of the polymer electrolyte. The impedance of CPE (Z_CPE) can be expressed using the following equations [42,43]:

$$Z_{CPE}=\frac{1}{C{\omega }^p}\left[\cos \left(\frac{\pi p}{2}\right)-i\sin \left(\frac{\pi p}{2}\right)\right]$$

(1)

where C is the capacitance of CPE, ω is the angular frequency, and p is the deviation of the plot from the axis. The real and imaginary parts of the impedance, Z_r and Z_i of the B1 and B2 electrolytes, which consist of both semicircle and spike, can be expressed using the following equations.

$$Z_r=\frac{R_b{C}_1{\omega }^{p_1}\cos \left(\frac{\pi p_1}{2}\right)+R_b}{2R_b{C}_1{\omega }^{p_1}\cos \left(\frac{\pi p_1}{2}\right)+R_b^2{C}_1^2{\omega }^{2p_1}+1}+\frac{\cos \left(\frac{\pi p_2}{2}\right)}{C_2{\omega }^{p_2}}$$

(2)

$$Z_i=\frac{R_b^2{C}_1{\omega }^{p_1}\sin \left(\frac{\pi p_1}{2}\right)}{2R_b{C}_1{\omega }^{p_1}\cos \left(\frac{\pi p_1}{2}\right)+R_b^2{C}_1^2{\omega }^{2p_1}+1}+\frac{\sin \left(\frac{\pi p_2}{2}\right)}{C_2{\omega }^{p_2}}$$

(3)

where p₂ and p₁ are the deviation of the spike from the horizontal axis and deviation semicircle from the vertical axis, respectively. The capacitances at high and low frequency are represented as C₁ and C₂, respectively. For the B3 electrolyte that only has the spike and the R_b is connected in series with CPE, the impedance can be expressed as:

$$Z_r=\frac{\cos \left(\frac{\pi p}{2}\right)}{C{\omega }^p}+R_b$$

(4)

$$Z_i=\frac{\sin \left(\frac{\pi p}{2}\right)}{C{\omega }^p}$$

(5)

Equations (1)–(3) were used for fitting the EIS data to an equivalent circuit for the B1 and B2 electrolytes, while Equations (1), (4), and (5) were used for fitting the EIS data to an equivalent circuit for the B3 electrolyte. The equations were also used to determine the fitting parameters (CPE1 and CPE2) and measuring the R_b values precisely. The determined R_b values and calculated CPE values for the B1, B2, and B3 electrolytes are tabulated in

Table 3. Room temperature circuit element for the electrolytes.

Electrolyte	Rb (Ω)	CPE1 (F)	CPE2 (F)
B1	(4.79 ± 1.2) × 103	(4.00 ± 1.3) × 10−9	(2.86 ± 0.7) × 10−6
B2	(3.21 ± 1.0) × 102	(2.86 ± 1.1) × 10−9	(3.70 ± 1.0) × 10−6
B3	(2.53 ± 0.8) × 102	-	(5.41 ± 1.2) × 10−6

. The growth of CPE2 values with the increases of glycerol content clarified the boost of the number of ions in the electrolytes, which increase the availability for electrode polarization, hence, increasing the capacitance value at low frequency [44]. This also contributes to a better dissociation and mobility of ions, which, therefore, increases the ionic conductivity of the electrolytes [45].

Subsequently, the ionic conductivity (σ) values can be calculated using Equation (6) that is beneficial to show the electrical properties of the electrolytes. The calculation involves the R_b values from Table 3 and also the thickness (t) and surface area (A) of the electrolytes. The A of the stainless-steel electrode is 2.01 cm² and the t of the films were shown in Section 2.1.

Table 4. Room temperature ionic conductivity for the electrolytes.

Electrolyte	σ (S/cm)
B1	3.22 × 10−6
B2	4.80 × 10−5
B3	6.10 × 10−5

lists the obtained conductivity values for the electrolytes in this work.

$$\sigma =\frac{t}{A\times R_b}$$

(6)

The conductivity of the B1 electrolyte with 12 wt.% of glycerol is found to increase from 3.22 × 10⁻⁶ S/cm to 6.10 × 10⁻⁵ S/cm when 42 wt.% glycerol was added in B3 electrolyte. According to Marf et al. [46], the ionic conductivity of the electrolytes depends on the flexibility of the polymer chain and also the mobility of ions, and the use of glycerol as a plasticizer for the system would ease these factors. The highest conductivity value obtained by the B3 electrolyte would be appropriate for the ion-conducting device applications, which necessitate an electrolyte with conductivity series from 10⁻³ to 10⁻⁵ S/cm [47].

Field emission scanning electron micrographs were obtained at a 500× magnification for each system to support the EIS results, and the micrograph for each system is shown in Figure 3a–c. The white structures represent the protruding salts within the surface of the samples in Figure 3a–c. When there is the inclusion of 14 and 28 wt.% glycerol into the electrolyte system, few salts appeared within the films’ surface, as discovered in Figure 3a,b. The glycerol decreases the electrostatic force among cations and anions of the salt, and thus, will produce more mobile ions [48]. The existence of a plasticizer can improve the amorphous structure of the electrolyte and improve the conductivity [49]. Thus, the high concentration of glycerol can dissociate more salts into caions and anions. As it can be observed from the field emission scanning electron micrograph in Figure 3c that protruding salt structures are not evidently visible as the glycerol concentration was increased to 42 wt.% (B3 system) in comparison to the B1 and B2 electrolyte systems. The highest plasticized sample has smooth and uniform surface morphology without any phase separation. In our previous work [50], obvious phase separation in CS:PEO blend electrolyte has been detected. The lack of phase separation in Figure 3 is a confirmation for the complete blending of CS with dextran. The field emission scanning electron micrographs are in good agreement with the results of EIS. The white structures decreased in the B3 system, and the R_b value diminished, as seen in the EIS plot, while conductivity increased. It is documented that the smooth morphology appearance is related to the amorphous nature development of the electrolyte systems [51]. In the previous work [50], the combined results of EIS and morphological appearance were used to understand the structure-property relationship. The smooth surface electrolytes can aid conducting ions to transfer easily, and hence, improve the DC ionic conductivity [51].

3.2. FTIR and XRD Studies

The interaction among the elements of the electrolyte, polymers, sodium salt, and glycerol can be identified from the FTIR analysis. The FTIR spectra for the selected band regions are depicted in Figure 4.

Based on Figure 4a, the peak situated at 3331 cm⁻¹ is designated for the O–H band in the B1 electrolyte, which has then slightly shifted to 3332 cm⁻¹ (B2) and 3333 cm⁻¹ (B3). Comparable O–H band peaks were observed in the FTIR spectra of other studies using relatively similar electrolyte components, such as PVA:NaTf system at 3319 cm⁻¹ [27], PVA:dextran: NH₄I at 3332 cm⁻¹ [52], and PVA: CS:ammonium bromide (NH₄Br) at 3324 cm⁻¹ [52]. The intensity variation of this band and its shifting signify a stronger interaction among blended host polymer, salt, and plasticizer in the electrolyte. This is because any changes in the FTIR spectra arise from the modifications in the vibrational and stretching modes, due to the interaction between the electrolyte components [53,54]. This increased interaction is promoting the dissociation of ions, which is beneficial for the enhancement of ionic conductivity of the electrolytes [54]. This intensity increment (see Figure 4) further supports the ionic conductivity trend, as shown in Table 4. Moreover, the C–H stretching band for the B1 electrolyte is noticed to peak at 2908 cm⁻¹. As the concentration of glycerol increases, this band shifted to 2906 cm⁻¹ and 2903 cm⁻¹ when the B2 and B3 electrolyte was used, respectively. This range is in good agreement with 2897 cm⁻¹ in Asnawi et al.’s work [55] involving poly(ethylene oxide) (PEO): Graphene oxide (GO): Ammonium triflate (NH₄CF₃SO₃), and 2920 cm⁻¹ in Liebeck et al.’s work [56] involving cellulose/keratin hydrolysate. According to Aziz et al. [57], the C–H stretching band at this wavenumber region is due to the presence of dextran within the electrolyte, whereby chitosan does not exhibit this band. Furthermore, Figure 4b shows the FTIR spectra in which the carboxamide band and the amine band for the B1 electrolyte are located at 1642 cm⁻¹ and 1557 cm⁻¹, respectively, which have then correspondingly moved to 1643 cm⁻¹ and 1560 cm⁻¹ when the glycerol concentration increased to 42 wt.% in B3 electrolyte. The observed positive shift shows the effect of glycerol concentration on its interaction with polymer-salt complexes. The presence of glycerol with high dielectric constant dissociates more salts to free ions, yielding more ions to interact with oxygen and nitrogen atoms in the polymer blend [54,58]. Aziz et al. [59] prepared solid polymer electrolyte chitosan:dextran:NH₄I and used FTIR technique to study the interaction between the electrolyte elements. The authors reported 1651 and 1554 cm⁻¹ for the carboxamide (O=C–NHR) and amine (NH₂) bands, respectively, for their electrolyte systems.

On the other hand, the region of 950–1320 cm⁻¹ is known to include a few important functional groups, such as asymmetric vibration (υ_as) and symmetric vibration (υ_s), associated with the trifalte anion (CF₃SO₃)⁻ of NaTf salt [60,61]. According to Jeya et al. [60], the two bands at 1259 cm⁻¹ and 1027 cm⁻¹ are attributable to free ions υ_as(SO₃) and υ_s(SO₃). The authors also mentioned that the free ions’ peak will split into two, one at a lower and another at a higher wavenumber. This region is also used to determine the transport parameters; number density (n), ionic mobility (µ), and diffusion coefficient (D) based on the percentage of free ions, and it is highly correlated to the conductivity of the electrolytes [62]. The deconvoluted FTIR spectra for the region of 950–1320 cm⁻¹ are shown in Figure 5. For B1 electrolyte, the free ions’ peak are identified at 1260 cm⁻¹ and 1019 cm⁻¹, while the ion pairs peak are identified at 1228 cm⁻¹ and 1085 cm⁻¹. For B2 electrolyte, the free ions’ peak are observed at 1259 cm⁻¹ and 1020 cm⁻¹; whereas, the ion pairs peak are identified at 1229 cm⁻¹ and 1086 cm⁻¹. For B3 electrolyte, the free ions’ peak are determined at 1259 cm⁻¹ and 1024 cm⁻¹, while the ion pairs peak are observed at 1226 cm⁻¹ and 1095 cm⁻¹. As the intensity of these free ions peaks is increased, the formation of ion pairs will occur. Besides, the υ_as(CF₃) band obtained by the electrolytes in this work, which is at 1169–1173 cm⁻¹ is similar to 1165–1173 cm⁻¹ reported by Ranjana et al. for the Polyvinylidenefluoride-co-hexafluoropropylene: Polymethylmethacrylate:NaTf electrolyte system [61]. The percentage of free ions can be determined using the following relation.

$$\mathrm{Free} \mathrm{ions} \%=\frac{\mathrm{Area} \mathrm{of} \mathrm{free} \mathrm{ions}’ \mathrm{peak}}{\mathrm{Total} \mathrm{area} \left(\mathrm{free} \mathrm{ions} \mathrm{peak}+\mathrm{ion} \mathrm{pairs} \mathrm{peak}\right)}\times 100$$

(7)

The peak intensity of free ions, due to the υ_as(SO₃) and υ_s(SO₃), is observed to increase as the concentration of glycerol increases. The corresponding free ion percentage was 75% for B1 electrolyte, 77% for B2 electrolyte, and 80% for B3 electrolyte. The increase of free ions percentage as the concentration of glycerol is increased, showing a similar trend with the ionic conductivity results achieved by the electrolytes. From the deconvolution of FTIR spectra in Figure 5, the calculated transport parameters using the following equations are tabulated in

Table 5. Transport parameters of the electrolytes at room temperature.

Electrolyte	Number Density, n (cm−3)	Ionic Mobility, μ (cm2 V−1 s−1)	Diffusion Coefficient, D (cm2 s−1)
B1	2.13 × 1022	9.44 × 10−10	2.42 × 10−11
B2	8.96 × 1022	3.35 × 10−9	8.59 × 10−11
B3	1.02 × 1023	3.75 × 10−9	9.61 × 10−11

.

$$n=\frac{M\times N_A}{V_{Total}}\times \left(\mathrm{free} \mathrm{ion} \%\right)$$

(8)

$$\mu =\frac{\sigma }{ne}$$

(9)

$$D=\frac{\mu kT}{e}$$

(10)

where N_A is Avogadro’s number, M represents the number of moles of glycerol, σ is DC conductivity, which is shown in Table 4, T is the temperature (298 K), K is the Boltzmann constant (1.38 × 10⁻²³ J/K), and e is the elementary charge. V_Total is the total volume of the polymer electrolytes.

The calculated transport parameters in Table 5 show that the addition of glycerol into the electrolyte from B1 to B3 has increased both n and μ by one order of magnitude, and almost a four-fold increase in D. These results are harmonized with the ionic conductivity pattern because the high number density directly contributes to a high conductivity value [63]. Pritam et al. [64] also reported that the dependency of ionic conductivity on the transport parameters in the system of PEO/PVP-NaNO₃ that investigated using the FTIR approach.

XRD for pure CS, CS: dextran, and CS: dextran: NaTf: glycerol at room temperature are shown in Figure 6. The CS has crystalline peaks at the 2θ values of 10.1°, 15.1°, and 20.9° [65,66] (Figure 6a), while dextran possesses two hallows at 2θ values of 18° and 23°, as indicated in the previous work [67]. In the current work, two hallows and smaller crystalline peaks were observed in the XRD pattern of CS: dextran (Figure 6b). It is interesting that (as shown by the broad hallows) CS: dextran is not as crystalline as pure CS and its structure is almost amorphous [68,69]. Based on earlier studies, the amorphous nature of polymer electrolyte is related to broad diffraction peaks [70,71]. To determine the crystallinity degree, it is vital to deconvolute the XRD pattern for each film to find the areas of the crystalline and amorphous peaks [71]. The degree of crystallinity (Xc) was determined using Equation (11), and shown in

Table 6. The degree of crystallinity obtained from deconvoluted XRD pattern.

Electrolyte	Degree of Crystallinity (%)
Pure CS	15.97
CS Dex	13.85
B1	7.96
B3	5.52

[72]:

$$X_c=\left[\frac{A_c}{\left(A_T\right)}\right]\times 100\%$$

(11)

where A_T and A_C are the total area of crystalline and amorphous peaks and crystalline peaks’ area, respectively.

Meanwhile, it has been observed in this study, when glycerol was included, the CS: dextran peaks showed intensity decline, and its wide nature was improved, as shown in Figure 6c,d. Such observations confirm that the polymer electrolyte has an amorphous structure, which improves better conductivity by enhancing ionic diffusivity. Moreover, the NaTf salt experiences full dissociation in the polymer electrolyte that there is not any peak associated with pure NaTf. The hydrogen bonding elimination among the polymer chains is a probable reason for the reduction and broadening in intensity, indicating the amorphous phase prevalence within the samples [73].

3.3. Dielectric and Electric Modulus Analysis

The polarization effects, as well as the conductivity behavior, can be further studied based on dielectric properties, including the dielectric loss (ε″) and dielectric constant (ε′), which represent the amount of energy loss and charge stored, respectively, during the movement of ions [74]. The Z_r and Z_i data were extracted from the EIS data and then used to determine the ε′ and ε″. These dielectric parameters can be calculated using Equations (12) and (13) [26,31].

$$\mathsf{\epsilon }\prime =\frac{Z_i}{\left(Z_r^2+Z_i^2\right)C_o\omega }$$

(12)

$$\mathsf{\epsilon }″=\frac{Z_r}{\left(Z_r^2+Z_i^2\right)C_o\omega }$$

(13)

where C_o stands for the vacuum capacitance and ω is the angular frequency. The plot of ε′ and ε″ for the electrolytes at room temperature can be observed in Figure 7a,b.

Based on Figure 7, the order of dielectric constant and dielectric loss decreases from B3 to B2 to B1 in the low frequency region. The high dielectric values obtained in this work, especially for the B3 electrolyte, explains that the accumulation of charge carriers can cause the polarization of electrodes and also the space charge effect within the system [55,75]. The lack of any peak in Figure 7 due to dielectric relaxation designates the system is predominantly due to polymer relaxation segments in their ionic conductivity [76]. However, the values of ε′ and ε″ for the electrolytes are observed to reduce as the frequency increases and remain at a constant value, which caused by the periodic reversal of the electric field that occurred rapidly between the electrodes [77]. Generally, the dielectric plots show the effects of glycerol concentration in the electrolytes on the ε′ and ε″ values where the employment of glycerol as a plasticizer help to enhance these properties, which are also harmonized with the conductivity and transport parameters trends. The non-Debye model is suitable to represent the conductivity behavior of the electrolytes.

Furthermore, the frequency dependence of dielectric loss tangent (tan δ) can be determined for the electrolytes to further understand the relaxation processes of the electrolytes. As mentioned above, the Z_r and Z_i data have been obtained from the EIS data and then used to find the ε’ and ε” data. The dielectric parameters are used to determine the tan δ. The tan δ is a ratio of energy disperse to energy stored in a periodical field, which is also known as the dissipation factor [78]. The tan δ is determined using the relation below [78].

$$\tan \delta = \frac{{\mathsf{\epsilon }}^{″}}{\mathsf{\epsilon }\text{′}}$$

(14)

The relaxation processes of polymer materials are precisely studied via loss tangent peaks. The dipoles in the polymer electrolytes can be illustrated based on the dielectric relaxation [79,80]. Figure 8 shows the dielectric relaxation of the loss tan δ vs. frequency plot for each film at room temperature. In the figure, there is a shift to a region of the high frequency of the loss tangent peak, showing the occurrence of dielectric relaxation. One finding of this work is that induced or permanent dipoles cause the conductivity and dielectric relaxation peaks. It was also indicated that induced diploes hide the polarization relaxation of mobile charge carriers in the materials [79,80]. The peaks observed in Figure 8 describe the translational ion dynamics that are related to the mobile ions’ conductivity relaxation. This is an advantage for the ions transport in the segmental motion of the electrolytes [80]. The tan δ is noticed to increase when the frequency increases, due to the dominant amount of active element (ohmic) compared to the reactive element (capacitive). Following this event, the reduction of tan δ at a higher frequency is probably due to the independency of the active element to the frequency, which causes the reactive element to increase accordingly [81]. The relaxation process of the electrolytes signified by the tan δ plot proposes the non-Debye behavior of the system [82]. Furthermore, the tan δ value that is located at the highest frequency can be designated as the tan δ maximum, tan δ_max value, which is valuable to control the angular frequency, ω_peak of the relaxation peak. Therefore, the relaxation time (t_r) of each electrolyte can be calculated by inversing the ω_peak (1/ω_peak). The calculated t_r values are listed in

Table 7. The relaxation time, t_r for the electrolytes.

Electrolyte	tr (s)
B1	3.32 × 10−6
B2	5.49 × 10−7
B3	1.81 × 10−7

.

The result of relaxation time is noticed to reduce as the ionic conductivity of the electrolytes increases, as observed in Table 4 and Table 7. This is because the ions are mostly attached to the polymer chain during their movement in the segmental motion that is beneficial for the hopping process between the conduction sites [83]. The lowest relaxation time for the electrolyte with the highest concentration of glycerol verifies the faster ion dynamics within the system [84]. Vahini et al. [85] also reported the low relaxation time, which was responsible for the high ionic conductivity value. In addition, the electrical modulus study can be used to further describe the polarization suppression effect of the system. The real (M′) and imaginary (M″) parts of electrical modulus at room temperature were evaluated using Equation (15) and Equation (16) [86], respectively, and the results are plotted in Figure 9 [86].

$$M\prime =\omega C_o{Z}_i$$

(15)

$$M″=\omega C_o{Z}_r$$

(16)

The electrical modulus analysis [87] can also be used to investigate the dielectric properties caused by the relaxation of ions because the electrode polarization is interrelated to the development of charges near the electrodes. Based on Figure 9, the electrical modulus values are observed to stay near zero at low frequency in both plots. The long tail detected at low frequency proposes the capacitive behavior of the electrolytes where the strong electrode polarization occurs without any dispersion [36,78]. Along with the frequency, the M′ and M″ values of the electrolytes are observed to increase, due to the bulk effect. The highest conducting electrolyte obtained the lowest electrical modulus values at high frequencies. A similar observation is reported by Mustafa et al. [87] and Saminatha Kumaran et al. [88]. The presence of peaks in both modulus plots explained the enhancement of polymer chain flexibility, signifying that the electrolytes are considered as good ionic conductors [89,90]. Furthermore, the plot of M″ versus M′ or also known as Argand plot for the electrolytes at room temperature, is depicted in Figure 10.

The Argand plot in Figure 10 illustrates a single incomplete semicircle, which is extrapolated to suit each electrolytes curve. This deformed semicircle is generally an indicator for the broad relaxation processes within the system and also reveals the non-Debye behavior [91]. The ionic conductivity of the electrolytes is found to be directly influenced with the radius of arc in the Argand plot, where the smaller arc contributes to a higher conductivity value [92]. This relationship is also related to the resistivity of the electrolytes. This is correlated to Equation (16), since the curve of the highest conducting electrolyte, B3 is closer towards the origin [71].

3.4. Electrochemical Investigation

The performance of the highest conducting electrolyte, B3 is further tested using transference number measurement (TNM) and linear sweep voltammetry (LSV) to identify its suitability for the application in energy devices. Firstly, TNM analysis was conducted at room temperature to investigate the contribution of particular charge species within the electrolyte, either ions or electron, which can be determined through the polarization of current against time as plotted in Figure 11.

The plot in Figure 11 exhibits a drastic drop of initial current (I_i) and then reaches a steady state of current (I_ss) at 100th s and onwards. During the initial current drop, the drift of ions is equivalent to the diffusion of ions where the ions are blocked by the characteristics of the stainless-steel electrode [93]. Only electrons are allowed to transport during this phase. The large value of current in the beginning is because the ions and electrons are involved. In the beginning, the cations and anions move in opposite directions toward the surface of the electrodes from the bulk of the electrolyte to form the double-layer at the electrode-electrolyte interfaces, and polarization occurs. The polarization of the cell occurs when it reaches the steady state, while transport of the rest of the currents is only due to electrons [94]. This is why the electron transference number (t_e) can be determined using stainless-steel electrodes. Subsequently, the steady state of current is developed by the formation of diffusion layers on the electrode interface, where a large resistance of a passive ionic layer was produced [79,95]. Therefore, ions were not involved in the current flow in this region [79,95]. When the ions are totally reduced, a steady state of current flow that is due to electrons is obtained [96]. The transference numbers of the ion (t_ion) and electron (t_e) for the B3 electrolyte are calculated using the following equations.

$$t_{ion}=\frac{I_i-I_{ss}}{I_i}$$

(17)

$$t_e=\frac{I_{ss}}{I_i}$$

(18)

The B3 electrolyte achieved a high t_ion value of 0.988, and signifies that ions were dominant in the system [97]. The t_e value obtained is 0.012. According to Shukur et al. [98], the contributor of the carrying charge of a system is due to the ions if the t_ion value is near to unity. A similar observation is reported by Mohan et al. [99] and Tang et al. [100]. The high t_ion value can be used to further examine the contribution of ions in the B3 electrolyte, which can be calculated using the following equations [101]:

$$t_{ion}=\frac{D_{+}}{D_{+}+D_{-}}= \frac{D_{+}}{D}$$

(19)

$$D=\frac{\mu k_{b}T}{e}=D_{+}+D_{-}$$

(20)

$$t_{ion}=\frac{{\mu }_{+}}{{\mu }_{+}+{\mu }_{-}}= \frac{{\mu }_{+}}{\mu }$$

(21)

$$\mu =\frac{\sigma }{ne}={\mu }_{+}+{\mu }_{-}$$

(22)

where D₊ and D₋ represent the diffusion coefficient of cation and anion; while µ₊ and µ₋ are the ionic mobility of cation and anion, respectively. The calculation is based on the transport parameters listed in Table 5. From Equation (19), $D_{+}=t_{ion}\times D$, $D_{+}$ can be calculated and by using Equation (20), $D_{-}=D-D_{+}$, D− can be obtained. The calculated values of D₊ and D₋ for the B3 electrolyte are found to be 9.50 × 10⁻¹¹ and 1.15 × 10⁻¹² cm² s⁻¹, respectively. Similarly, using Equations (21) and (22), ${\mu }_{+}$ and ${\mu }_{-}$ were founded to be 3.70 × 10⁻⁹ and 4.49 × 10⁻¹¹ cm² V⁻¹ s⁻¹, respectively. From these results, it can be concluded that the cationic values are more significant than those of anionic for both D and µ. Therefore, in polymer electrolytes, researchers have mainly focused on cations rather than anions. The ionic conductivity is found to be reliant on these two parameters (D and µ) [6]. Hafiza et al. [102] also reported a similar observation for the influence of ions on D and µ values. The diffusion coefficient values achieved in this work is analogous to the earlier studies where the diffusion coefficient is in the range from 10⁻¹³ to 10⁻⁸ [96,103,104,105]. Furthermore, another vital characteristic of an electrolyte is the maximum working voltage. This measurement is significant to identify the breakdown voltage (V_B) of an electrolyte that can withstand that can be acquired from the LSV analysis [106]. The LSV curve for the highest conducting electrolyte, B3 (at room temperature), is presented in Figure 12 at a scan rate of 10 mV/s.

Based on Figure 12, the LSV curve of the B3 electrolyte does not experience the current density growth before reaching 2.55 V. This illustrates worthy electrochemical stability within the system electrolyte system up to that potential [107]. Therefore, the breakdown voltage of 2.55 V is possessed by the B3 electrolyte. Moreover, Liew et al. were shown that the addition of plasticizer to the PVA-CH₃COONH₄ electrolyte-enhanced the V_B value of the system from 1.80 V to 2.20 V and observed to has a promising performance in the energy devices [108]. The V_B value determined in this work is high enough to be applied in the electrochemical devices that are normally run at the operating voltage of 1.0 V [109].

4. Conclusions

The polymer electrolytes of chitosan/dextran-NaTf with three different glycerol concentrations were been prepared. From the impedance study, the addition of glycerol has increased the ionic conductivity of the electrolyte at room temperature. The B3 electrolyte achieved the highest conductivity of 6.10 × 10⁻⁵ S/cm. It was revealed by the FESEM method that at higher glycerol concentration, that the films have a smooth and homogenous surface morphology. The interaction of the components within the electrolytes was confirmed from the presence of the O-H, C-H, carboxamide, and amine groups. The transport parameters were identified using the percentage of free ions, due to the υ_as(SO₃) and υ_s(SO₃) bands. The determined X_c revealed that the amorphous phase improved with plasticizer addition. The dielectric properties and relaxation time verified the non-Debye behavior of the electrolyte system. This behavior model was further proved by the presence of an incomplete semicircle arc from the Argand plot. The ions ere investigated to be the most dominant element in the B3 electrolyte with a t_ion value of 0.988 and t_e of 0.012. The t_ion value was used to further examine the contribution of ions in the ionic mobility and diffusion coefficient values. From the determined values of D₊, D₋, ${\mu }_{+}$ and ${\mu }_{-}$, it can be concluded that the cationic values were more significant than those of anionic for both D and µ. The breakdown voltage of the B3 electrolyte was observed at 2.55 V from the LSV analysis, which may be a promising electrolyte for the electrochemical energy devices applications.