Nature-Derived Cellulose-Based Composite Separator for Sodium-Ion Batteries

Introduction

Lithium-ion batteries (LIBs) have received significant attention worldwide as major energy sources for electric vehicles and mobile devices, and the demand for LIBs is expected to increase in the near future (Mizushima et al., 1980; Amatucci et al., 1996; Winter et al., 1998; Mishra and Ceder, 1999; Sun et al., 2009; Jo et al., 2015). However, the cost increase of lithium resources resulting from their limited supply will make satisfying this demand difficult; thus, the development of post-LIB battery systems is essential (Pan et al., 2013; Nithya and Gopukumar, 2015; Park et al., 2017; Jo et al., 2018a,b; Jo J. H. et al., 2018; Vaalma et al., 2018). Recently, sodium-ion batteries (SIBs) have been highlighted as attractive alternatives to LIBs for energy storage for both economic and scientific reasons; namely, sodium reserves are abundant and the reaction chemistries adopting a monovalent charge carrier are similar (Kim et al., 2015; Choi et al., 2018; Konarov et al., 2018). However, one shortcoming of SIBs is the slightly higher standard electrode potential of sodium [−2.7 V vs. the standard hydrogen electrode (SHE)] relative to that of lithium (−3.04 V vs. SHE), which has motivated the development of high-energy-density cathode materials and high-capacity anode materials (Yabuuchi et al., 2012, 2013; Guignard et al., 2013; Vassilaras et al., 2013). There have been many reports on high-energy-density cathode materials with surface modification to prevent particle damage from the changing volume during charge/discharge, anode materials with high reversible capacity, and stable electrolytes under oxidizing environments (Yu et al., 2015; Hwang et al., 2017; Åvall et al., 2018; Kim et al., 2018; Sato et al., 2018; Suharto et al., 2018; Choi et al., 2019; Jo et al., 2019; Lee et al., 2019; Wang et al., 2020). In most of these studies, glass fibers (GF) have been widely used in most SIBs because of their advantages over excellent wettability for ethylene carbonate and propylene carbonate, indicating high porosity (66%), large electrolyte uptake (360%), high ionic conductivity of electrolyte soaked in separator (3.8 mS cm⁻¹), sodium ion transfer number ($t_{\text{Na}}^{+}$ = 0.79) than polypropylene membrane (Zhu et al., 2016; Arunkumar et al., 2019). Apart from the acceptable physical properties, cost and thickness of GF separator may impede their adoption to commercial SIBs at present. Therefore, finding an alternative to GF separators is urgent for commercialization of SIBs (Suharto et al., 2018). For these reasons, there have been few studies using polyolefin membranes modified by oxides or polymers (Kim et al., 2001, 2004, 2009; Jeng and Kim, 2004). Separators must provide adequate (1) porosity, (2) wettability, (3) chemical and thermal stability, and (4) ionic conductivity of electrolyte soaked in separator. Polypropylene (PP) and polyethylene (PE) separators are not suitable as a separator for batteries, because the separators exhibit very low wettability for cyclic carbonate-based electrolytes such as ethylene carbonate (EC) and propylene carbonate (PC), which are used as electrolytes for SIBs (Suharto et al., 2018). Their low thermal property is considered as another difficulty to apply them for SIBs (Xu, 2004; Kim et al., 2014; Zhu et al., 2016). The advantages of cellulose-based membranes for LIBs include their electrolyte uptake, thermal stability, and high ionic conductivity of electrolyte soaked in separator, which lead to high rate capability (Chiapponea et al., 2011). Chen et al. reported the suitability of cellulose acetate separators in SIBs for long-term cycling (Chen et al., 2018). Herein, we propose a new cellulose–polyacrylonitrile–alumina composite as a SIB separator (Scheme 1). Cellulose nanofibers are easily obtained from plants and are composed of close-packed polysaccharide chains with β- (1 → 4) -D-glucopyranose repeating units (Siró and Plackett, 2010). Cellulose nanofibers provide advantages in the process of separating membranes owing to their excellent dispersing properties in various solvents and inherent porous nanostructure, good thermal stability (melting point ≥ 250°C), hydrophilicity, and chemical stability (Chun et al., 2011). However, the cellulose membrane, which is thinner than that of a glass fiber, can be vulnerable to dendrite growth of sodium metal; thus, the mechanical strength must be improved for the application of cellulose as a separator. To overcome this issue, a commercial cellulose–PAN membrane was compositized with Al₂O₃ particles by dip coating, where the addition of Al₂O₃ was anticipated to provide thermal stability and functionality during the electrochemical reaction with the electrolyte. In addition, PAN is known to improve not only the mechanical properties but also the ionic conductivity of electrolyte soaked in separator. As designated, the present cellulose–PAN–Al₂O₃ composite separator exhibits acceptable physico-chemical properties, namely, a Gurley value of 153.3 s, ionic conductivity of electrolyte soaked in separator of 0.751 mS cm⁻¹, transference number of sodium ions of 0.78, contact angle of 0°, puncture strength of 2.22 MPa, and thermal stability up to 300°C without shrinkage. The applicability of the cellulose–PAN–Al₂O₃ composite separator was verified in full cells fabricated with a NaCrO₂ cathode // hard carbon anode in a conventional carbonate electrolyte for long-term cycling, resulting in capacity retention of 82% at a rate of 10 C for 500 cycles. Our findings suggest that the cellulose–PAN–Al₂O₃ composite separator is eminently suitable for use in SIBs.

SCHEME 1

Scheme 1. Schematic illustration of a cellulose-polyacrlonitrile-alumina separator.

Experimental Section

Preparation of Cellulose-PAN-Al₂O₃ Composite Separator

Al₂O₃ coating solution was provided by the Emerging Industries Institute of Shanghai University. A cellulose/PAN hybrid (cellulose/PAN = 50/50 in weight) electrospun nano-fiber separator (thickness: 21 μm) was obtained from NingBo EneRol Nanotechnology, Inc. For dip coating of the separator, the pristine cellulose–PAN separator was immersed in an Al₂O₃ suspension, composed of polyvinyl acetate (PVAc) as a binder and aqueous Al₂O₃ dispersion, provided by the Emerging Industries Institute of Shanghai University. The coated separators were dried at 60°C for 0.5 h. The composited separators were thickened to 50 μm by repeated dip-coating and drying processes. The composited cellulose–PAN–Al₂O₃ separators were further vacuum-dried at 100°C for 12 h prior to use.

Characterization

X-ray diffraction (XRD; X'Pert, PANalytical) was employed to identify the phases of the coated materials on the cellulose–PAN separator. XRD data collection was performed in the 2θ range of 10-110°. Field-emission scanning electron microscopy (FE-SEM; Hitachi S-4700) was used to examine the morphology and cross-section of the composite separator. The functionality of the coated Al₂O₃ on the cellulose–PAN separator was identified using time-of-flight secondary ion mass spectroscopy (ToF-SIMS; PHI TRIFT V nanoTOF, ULVAC-PHI). The tensile strength of the separator was determined using a JDL-200N tensile tester with a tensile speed of 100 mm min⁻¹.

Contact angle measurements of the cellulose–PAN and cellulose–PAN–Al₂O₃ composite separators were performed using an OCA 15EC optical contact angle measuring device (Data Physics Instruments, Germany) at room temperature using the sessile drop method. The air permeability of the separators was evaluated using a Gurley densometer (UEC, 1012A) that measures the time required for 100 cc of air to pass through the separator. The electrolyte uptake of the separator was calculated using the following equation:

$\text{Electrolyte Uptake }(\text{wt\%})=\frac{\text{w}-{\text{w}}_0}{{\text{w}}_0}\times 100\%,$

where W₀ is the weight of the dry separator and W is the total weight of the separator and soaked liquid electrolyte.

The ionic conductivity (σ) of electrolyte soaked in separator was measured by analyzing the AC impedance spectra of stainless steel (SS)/separator/SS cells on an AutoLab (PGSTAT302N, Metrohm) electrochemical workstation in the range of 0.1 Hz−1 MHz at room temperature using the following equation:

$\sigma \text{=}\frac{\text{L}}{{\text{R}}_{\text{b}}.\text{S}}.$

Here, L is the thickness of the separator, S is the contact area of the separator and stainless-steel electrode, and R_b is the bulk resistance.

The puncture strength of the separator was determined using a Labthink Instrument XLW-PC auto tensile tester at a testing speed of 100 mm min⁻¹.

The Na⁺ transference number (${\mathrm{\text{t}}}_{{\mathrm{\text{Na}}}^{\mathrm{\text{+}}}}$) was measured using a combination of chronoamperometry and electrochemical impedance spectroscopy (EIS) of the sodium metal/separator–electrolyte/sodium metal cell using the following equation:

${\text{t}}_{{\text{Na}}^{\text{+}}}\text{=}\frac{{\text{I}}_{\text{s}}(\Delta {\text{V}-\text{I}}_{\text{0}}{\text{R}}_0)}{{\text{I}}_0(\Delta {\text{V}-\text{I}}_{\text{s}}{\text{R}}_{\text{s}})}.$

Here, ΔV is the potential difference set as 10 mV; I₀ is the initial current obtained; I_s is the steady-state current; and R₀ and R_s are the initial and steady-state interfacial resistance after polarization, respectively.

The thermal shrinkage ratio (TSR) was used to evaluate the thermal stability of the separators:

$\text{TRS(\%)}=\frac{{\text{S}}_0-\text{S}}{{\text{S}}_0}\times 100\%,$

where S₀ and S are the area of the separator before and after thermal treatment for 0.5 h at different temperatures, respectively. Thermogravimetric analysis (TGA) and differential scanning calorimetry (DSC) were performed by heating from 30 to 800°C in a nitrogen (N₂) atmosphere using a Netzsch simultaneous thermal analyzer (STA 449 F1 Jupiter).

Electrochemical Characterization

To fabricate a cathode, carbon-coated NaCrO₂ (C-NaCrO₂) was blended with conducting materials (a mixture of Super P carbon black and Ketjen black in a 1:1 ratio) and polyvinylidene fluoride (PVDF) in an 8:1:1 weight ratio in N-methyl pyrrolidone (NMP) solution. The obtained slurry was applied on Al foil, dried at 80°C for several hours to remove the NMP, and then heated at 120°C overnight under vacuum. Electrochemical cell tests were performed after assembling R2032 coin-type cells using Na metal or hard carbon as the negative electrode separated by the cellulose–PAN–Al₂O₃ composite separator. The assembly was performed in an argon-filled glove box. The electrolyte solution was 0.5 mol dm⁻³ NaPF₆ in ethylene carbonate (EC):dimethyl carbonate (DMC) (1:1 by volume), in which fluoroethylene carbonate (FEC) was added at a ratio of 3 vol.% vs. the EC:DMC solvent (Komaba et al., 2011). For full cell preparation, hard carbon anodes were pre-sodiated via electrochemical cycling of the anode in the range of 0.01–2 V, to minimize the first irreversible capacity of cathode and form solid electrolytic interphase on the hard carbon anode. Before cycling for hard carbon anode, it first was pre-potassiated through direct contact with potassium metal in 0.5 mol dm⁻³ NaPF₆ electrolyte for 1 h to minimize the irreversibility during sodiation process. Loading levels of active material were 3.0 mg cm⁻² for the cathode and 1.3 mg cm⁻² for the anode, which approaches to a N/P ratio of 1.2.

Results and Discussion

The cellulose–PAN separator was fabricated to achieve randomly arranged smooth fibers by electrospinning a homogeneous solution of a 1:1 mixture of cellulose and PAN, forming a non-woven separator. The cellulose itself was floppy with large pores; fabricating composite with PAN was expected to provide mechanical strength to the separator. In addition, the reinforced mechanical strength enabled the shape of the separator to be maintained, preventing the generation of an electrical short-circuit between the cathode and anode to enable facile diffusion of charge carriers (Figure 1a). Insulating and thermally stable Al₂O₃ powders with submicron size (<500 nm) were coated onto the cellulose–PAN separator to improve the thermal stability and ensure the porosity of the separator, namely, fabrication of a cellulose–PAN–Al₂O₃ composite separator with a thickness of 50 μm (Figure 1c) and EDX mapping image presented the presence of Al₂O₃ together with the cellulose–PAN separator (Figure 1c). The cellulose-PAN-Al₂O₃ separator was punctured by a needle to check the laminated structure of the separator (Figures 1d,e). The separator is composed of cellulose (> 1 μm thickness fiber), polyacrylonitrile (PAN, < 1 μm thickness fiber), and Al₂O₃, in which both fibers are non-woven together but presented together (Figure 1d). Therefore, it is thought that the presence of tensile PAN is likely to improve the mechanical strength of the cellulose in the cellulose-PAN separator. Based on SEM with EDX image, the side of separator presented clear distribution of Al, C, and O elements as shown in Figures 1d,e. In other words, it demonstrated that the cellulose, PAN, and Al₂O₃ coexist uniformly in the separator, as shown in Scheme 1. Furthermore, XRD pattern confirmed the presence of Al₂O₃ together with the cellulose–PAN separator (Figure 1f), and ToF-SIMS analysis provided further information on the presence of Al–O chemical bonding, which was attributed to the AlO⁺ fragment (m = 42.97) (Figure 1g).

FIGURE 1

Figure 1. (a) SEM image and photograph of cellulose–PAN separator; (b) SEM image of cellulose–PAN–Al₂O₃ composite separator; (c) SEM image and EDX mapping data (Al, C, O elements) of cellulose–PAN-Al₂O₃ composite separator; (d) SEM image on side for cellulose–PAN-Al₂O₃ composite separator (inset: SEM image of cellulose–PAN-Al₂O₃ composite separator at pierced point). (e) The magnified SEM image of cellulose–PAN-Al₂O₃ composite separator with EDX mapping result for Al, C, and O elements. (f) XRD pattern of bare and cellulose–PAN-Al₂O₃ composite separator; (g) ToF-SIMS data of cellulose–PAN-Al₂O₃ composite separator for AlO⁺ (m = 42.97) fragment.

Separators must have intimate contact with both the cathode and anode; thus, good flexibility, and tensile strength are important prerequisites for separators in batteries. As shown in Figures 2a–c, the as-prepared cellulose–PAN–Al₂O₃ composite separators could be twisted, rolled, and folded without damage under various bending conditions. Evaluation of the stress–strain behavior of the cellulose–PAN–Al₂O₃ composite separator confirmed its high tensile strength; specifically, 16.15 MPa for the cellulose–PAN separator and 20.83 MPa for the cellulose–PAN–Al₂O₃ composite separator (Figure 2d). This result is much higher than conventional GF separators (3.12 MPa) (Zhang et al., 2019). Furthermore, the cellulose–PAN–Al₂O₃ composite exhibited a higher puncture strength (2.22 MPa) than the bare separator (0.76 MPa) (Figure 2e). Since tensile and puncture strengths depend on the bonding strength between the alumina particles, they are susceptible to the composition of the alumina and polyvinyl acetate used as a binder in the alumina dip coating process. Thus, we proceeded to the process with a fixed composition.

FIGURE 2

Figure 2. (a) Twisting, (b) rolling, and (c) folding test results for cellulose–PAN-Al₂O₃ composite separator; (d) stress–strain curves of uncoated (bare) and cellulose–PAN-Al₂O₃ composite separator; (e) puncture strength curves of uncoated (bare) and cellulose–PAN-Al₂O₃ composite separator.

The wettability was evaluated by contact angle measurements; the cellulose–PAN and as-prepared cellulose–PAN–Al₂O₃ composite separators possessed contact angles of nearly 0° (Figure 3A). The cellulose–PAN separator exhibited excellent wettability, and the Al₂O₃ coating did not affect the wettability. To determine the air permeability of the separators, the elapsed time for blowing 100 cc of air was measured; Gurley values of 8.7 s for the cellulose–PAN separator and 153.3 s for the as-prepared cellulose–PAN–Al₂O₃ composite separator were obtained (Figure 3B), which are higher than that of the reported value (1.48) for GF separator (Arunkumar et al., 2019). These results imply that the submicron-sized Al₂O₃ particles inside and on the surface of the as-prepared cellulose–PAN–Al₂O₃ composite separators blocked the air flow owing to the small pore size, as observed in Figure 1b. The electrolyte uptake, ionic conductivity of electrolyte soaked in separator, and Na transference number were evaluated to confirm the effect of the Al₂O₃ coating on the affinity for the electrolyte. By comparing the weight of the separator before and after soaking in the electrolyte, it was possible to deduce the electrolyte uptake ability of the separators, as shown in Figure 3C. The weight increases for the cellulose–PAN separator was ~205%, and the absorption ability was increased to 286% for the cellulose–PAN–Al₂O₃ composite separator. As seen in Figures 1a–c, the submicron-sized alumina powders were applied on the surface cellulose-PAN layers, and this results the Gurley value higher than cellulose-PAN separator. Since there are many voids between the alumina particles, capillary effect is likely to allow readily penetration of electrolyte, so that contact angle with electrolyte exhibited 0 degree and the electrolyte uptake ratio was comparable to the result of cellulose-PAN separator (Figures 3B,C). Because the electrolyte uptake ability directly affects the ionic conductivity of electrolyte soaked in separator and electrochemical properties, the ionic conductivity and Na⁺ transfer value were subsequently evaluated. The ionic conductivity of electrolyte-soaked separator presented 0.751 mS cm⁻¹ (cellulose–PAN–Al₂O₃ composite separator) and 0.686 mS cm⁻¹ (cellulose–PAN separator) as shown in Figure 3D, which were lower than the ionic conductivity of GF separator (3.215) (Suharto et al., 2018). In addition, the sodium ion transfer number ($t_{\text{Na}}^{+}$) was significantly improved for the cellulose–PAN–Al₂O₃ composite separator ($t_{\text{Na}}^{+}$ = 0.78) compared with that of the cellulose–PAN separator ($t_{\text{Na}}^{+}$ = 0.31) (Figures 3E,F). Furthermore, this value is similar with that ($t_{\text{Na}}^{+}$ = 0.79) of GF separator (Arunkumar et al., 2019). Although the presence of alumina in the separator resulted in a higher Gurley value for the cellulose–PAN separator, the added alumina improved the intrinsic properties of electrolyte uptake, ionic conductivity of electrolyte soaked in separator, and sodium-ion transfer number owing to the high surface area provided by the alumina particles (and thereby the interconnected pore structure).

FIGURE 3

Figure 3. (A) Wettability, (B) Gurley value, (C) Electrolyte uptake, and (D) ionic conductivity of electrolyte soaked bare and cellulose–PAN-Al₂O₃ composite separator. Sodium transference number of (E) bare and (F) cellulose–PAN-Al₂O₃ composite separator.

Thermal stability is another important property for batteries and is directly related to shrinkage of the separator at elevated temperature, which can result in internal short-circuit. The thermal stability must be satisfactory to ensure safety and to extend the operating temperature range of batteries. According to the TG–DTG results, the cellulose–PAN–Al₂O₃ composite separator experienced a slight weight loss of ~8% from 250 to 350°C, whereas the cellulose–PAN separator experienced a drastic weight loss of over 90% in the same range (Figure 4a). DTG analysis indicated that the maximum evaporation rate was approximately −20.2% min⁻¹ at 359°C for the cellulose–PAN separator; however, the evaporation rate was remarkably reduced to approximately −2.5% min⁻¹ at 302°C for the cellulose–PAN–Al₂O₃ composite separator (Figure 4b). This preliminary result was confirmed by a shrinkage test, as shown in Figure 4c, which was performed up to 300°C after heat soaking for 30 min. The test results are highly reproducible for both cellulose-PAN and cellulose-PAN-Al₂O₃ separators, as we obtained the values in average after tests for 10 times (Figure 4c and Table 1). This improvement is likely associated with the minimized thermal deformation of the cellulose–PAN–Al₂O₃ separator supported by the thermally stable alumina particles (ΔG_f298K = −1582.3 kJ mol⁻¹ for formation at 298 K) bound by PVAc, which is stable up to 300°C (Abu-Saied et al., 2012), on the surface and within the separator. Moreover, thermal stability of the cellulose–PAN–Al₂O₃ composite separator is much better than that of conventional GF separator, which could not keep the initial shape after heat treatment at 300°C for 1 h (Supplementary Figure 1).

FIGURE 4

Figure 4. (a) TGA curves and (b) DTG curves of bare and cellulose–PAN-Al₂O₃ composite separator; (c) thermal shrinkage rate of bare and cellulose–PAN-Al₂O₃ composite separator after heat-treatment in temperature range of 25-300°C.

TABLE 1

Table 1. Thermal shrinking rate.

Figure 5A presents the first charge and discharge curves of C-NaCrO₂/Na cells using both cellulose–PAN and cellulose–PAN–Al₂O₃ composite separators. As a cathode material for SIBs, we thought that various evaluations can be carried out using carbon-coated NaCrO₂ for separators because of its excellent cycling performance and thermal stability. When cellulose was used as the separator, the cell could not be operated because of the generation of an internal short-circuit resulting from the large pores of the non-woven cellulose (Supplementary Figure 2). Although the operation voltage was slightly lowered on discharge when the cellulose–PAN–Al₂O₃ composite separator was adopted, the cell exhibited typical charge and discharge capacities of C-NaCrO₂, delivering a capacity of ~107 mAh g⁻¹ at 1C (110 mA g⁻¹) and 97 mAh g⁻¹ at 10C (1.1 A g⁻¹) with satisfactory cycling performance for 200 cycles, with over 94% retention of the initial capacities (Figures 5B,C). Furthermore, the cells were sustained at intermediate currents (Figure 5D). The cellulose–PAN separator employed in the C-NaCrO₂ cell could not be cycled over 40 cycles because of deformation of the separator that caused a short-circuit (Supplementary Figure 3), implying the importance of Al₂O₃ on the surface and in the cellulose-PAN separator. To confirm the temperature dependence, the operation temperature was increased to 80°C (Figure 5E). The observed capacity was ~112 mAh g⁻¹ at 1C with 95% capacity retention for 100 cycles. The slight increase in the capacity resulted from the enhanced ionic diffusivity at elevated temperature (Chandra, 2017). As anticipated from the thermal stability tests that indicated no shrinkage at this temperature (Table 1), operating the cell at 80°C did not induce a short-circuit or abrupt fade in the operation voltage during cycling. Although the cellulose-PAN-Al₂O₃ separator developed in this study exhibited lower values of electrolyte uptake (286%) and ionic conductivity (0.75 mS cm⁻¹) than the values of GF separator in literature shown above, the cell using the cellulose-PAN-Al₂O₃ separator presented the similar electrochemical performance compared to that of cell using glass fiber (Supplementary Figure 4). It thought that Al₂O₃ coating layer on the cellulose-PAN separator improve the electrode performance by preventing HF⁺ attacking (Myung et al., 2005; Zhang et al., 2019).

FIGURE 5

Figure 5. (A) First charge and discharge curve of C-NaCrO₂/Na cells using bare and cellulose–PAN-Al₂O₃ composite separator; (B,C) cycling performance at rates of 1C and 10C for C-NaCrO₂/Na cells using cellulose–PAN-Al₂O₃ composite separator; (D) Rate capability and (E) cycling performance (0.5C) at 80°C for C-NaCrO₂/Na cells using cellulose–PAN-Al₂O₃ composite separator.

Although the cellulose–PAN–Al₂O₃ composite separator was shown to be suitable for cathode application for SIBs, its applicability for full cells is more important to enable its adoption in SIBs. Thus, a pre-sodiated hard carbon anode was paired with the C-NaCrO₂ cathode, with a N/P capacity ratio of 1.2 (Figure 6A). In the operation range of 2.0–3.5 V at a current of 0.5C at 25°C, the fabricated hard carbon // C-NaCrO₂ full cell using the cellulose–PAN–Al₂O₃ composite separator delivered capacity retention of 88% for 300 cycles (Figures 6B,C). Similar to the half-cell results (Figure 5), the full cell also exhibited satisfactory high-rate performance, resulting capacity retention of 82% at a rate of 10 C after 500 cycles (Figure 6D).

FIGURE 6

Figure 6. (A) First charge and discharge curves of C-NaCrO₂ half cell (red), hard carbon half cell (black), and C-NaCrO₂/hard carbon full cell (blue) using cellulose–PAN-Al₂O₃ composite separator; (B,C) cycling performance of C-NaCrO₂/hard carbon full cell (blue) using cellulose–PAN-Al₂O₃ composite separator. (D) Cycling performance at 10 C of C-NaCrO₂/hard carbon full cell (blue) using cellulose–PAN-Al₂O₃ composite separator.

The post-cycled separator was further examined using ToF-SIMS to identify the role of alumina in the cellulose–PAN separator (Figure 7). The NaF⁺ fragment (m = 41.98) was detected for the post-cycled cellulose–PAN–Al₂O₃ composite separator (Figure 7A), which is indicative of decomposition of the NaPF₆ salt in the electrolyte. Furthermore, ${\text{AlF}}_2^{+}$ (m = 45.97, Figure 7B) and AlOF⁺ (m = 61.97, Figure 7C) fragments were detected on the surface of the separator. The appearance of these fragments suggests decomposition of the NaPF₆ salt in the electrochemical environment of Na cells; particularly, the salt can be decomposed in the presence of water molecules that are inevitably contained as an impurity in non-aqueous electrolyte as follows:

$\begin{array}{ll}\text{NaP}{\text{F}}_6\to \text{NaF}+\text{P}{\text{F}}_5& (1)\end{array}$

$\begin{array}{ll}\text{P}{\text{F}}_5+{\text{H}}_2\text{O}\to \text{PO}{\text{F}}_3+2\text{HF}& (2)\end{array}$

$\begin{array}{ll}2\text{PO}{\text{F}}_3+3\text{N}{\text{a}}_2\text{O}\to 6\text{NaF}+{\text{P}}_2{\text{O}}_5(\text{or N}{\text{a}}_{\text{x}}\text{PO}{\text{F}}_{\text{y}})& (3)\end{array}$

In the electrolyte, the produced HF faces the loaded amphoteric Al₂O₃ particles on the separator, resulting in the following reactions:

$\begin{array}{ll}\text{A}{\text{l}}_2{\text{O}}_3+2\text{HF}\to \text{A}{\text{l}}_2{\text{O}}_2{\text{F}}_2+{\text{H}}_2\text{O}& (4)\end{array}$

$\begin{array}{ll}\text{A}{\text{l}}_2{\text{O}}_2{\text{F}}_2+2\text{HF}\to \text{A}{\text{l}}_2\text{O}{\text{F}}_4+{\text{H}}_2\text{O}& (5)\end{array}$

$\begin{array}{ll}\text{A}{\text{l}}_2\text{O}{\text{F}}_4+2\text{HF}\to 2\text{Al}{\text{F}}_3+{\text{H}}_2\text{O}& (6)\end{array}$

leading to fluorination of Al₂O₃ toward AlF₃ via the above scavenging process. Thus, it is beneficial to use alumina with a cellulose–PAN separator to improve the electrode performance. Furthermore, our previous research reported that AlF₃ layer formed by scavenging HF plays an important role to act as a passive layer at high voltage in Na cells (Konarov et al., 2019). Bugga et al. also presented AlF₃ coated separator, demonstrating that the AlF₃ layer also protected separator surface, preventing short-circuit by dendrites and significant impact than Al₂O₃ coating on the cycling stability (Bugga et al., 2018; Sun et al., 2018). For the above reasons, the cell using cellulose-PAN-Al₂O₃ separator presented the good electrochemical performance. The functionality of Al₂O₃ on the cellulose–PAN separator is schematically illustrated in Figure 8.

FIGURE 7

Figure 7. ToF-SIMS data of cellulose–PAN-Al₂O₃ composite separator for (top) fresh and (bottom) cycled separator. (A) NaF⁺ (m = 41.9), (B) ${\text{AlF}}_2^{+}$ (m = 45.97), and (C) AlOF⁺ (m = 71.97) fragments in a Na cell.

FIGURE 8

Figure 8. Schematic illustration for the functionalities of a cellulose-PAN-Al₂O₃ composite separator.

Conclusion

This is the first report on the feasibility of cellulose–PAN–Al₂O₃ composites as separators for SIBs. The electrochemical, thermal, and mechanical performance of the cellulose–PAN separator was extraordinary improved with the addition of alumina. This new type of cellulose–PAN-Al₂O₃ composite separator presented multi-functional abilities with excellent thermal stability at 300°C, a large sodium-ion transport number ($t_{\text{Na}}^{+}$ = 0.78), improved ionic conductivity of electrolyte soaked in separator (0.751 mS cm⁻¹), and HF scavenging ability during electrochemical cycling. Half-cells using the separator delivered a high capacity of 107 mAh g⁻¹ at a rate of 1C with acceptable capacity retention at both 25° and 80°C. Moreover, a full cell using the cellulose–PAN–Al₂O₃ composite separator also exhibited excellent cycling stability of 88% for 300 cycles. Our findings provide insight for the development of alternatives to glass fiber separators for SIBs, which will help enable the commercial availability of SIBs in the near future.

Data Availability Statement

All datasets generated for this study are included in the article/Supplementary Material.

Author Contributions

JJ, C-HJ, LS, ZW, SY, and S-TM designed the whole experiment, and wrote the paper. ZQ performed the experiment for separator. HY conducted ToF-SIMS measurement.

Funding

This research was supported by the Basic Science Research Program through the National Research Foundation of Korea (NRF), funded by the Ministry of Education, Science, and Technology of Korea (NRF-2017R1A2A2A05069634 and NRF-2015M3D1A1069713), Ministry of Science and ICT of Korea (NRF2019H1D8A2106002).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Supplementary Material

The Supplementary Material for this article can be found online at: https://www.frontiersin.org/articles/10.3389/fchem.2020.00153/full#supplementary-material

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