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Effect of morphological change of copper-oxide fillers on the performance of solid polymer electrolytes for lithium-metal polymer batteries

Solid polymer electrolytes (SPEs) for Li-metal polymer batteries are prepared, in which poly(ethylene oxide) (PEO), lithium bis(trifluoromethylsulfonyl)imide (LiTFSI), and copper-oxide fillers are formulated. Their structural and electrochemical properties are analyzed when the morphology of the copper-oxide fillers has been modulated to spherical or dendritic structure. The ionic conductivity obtained by electrochemical impedance spectroscopy (EIS) has been increased to 1.007 × 10−4 S cm−1 at 30 °C and 1.368 × 10−3 S cm−1 at 60 °C, as the 5 wt% dendritic fillers have been added to the SPEs. This ionic conductivity value is 1.3 times higher than that of 5 wt% spherical filler-contained SPEs. The analyses of differential scanning calorimetry (DSC) and X-ray diffraction (XRD) indicate that the increase of ionic conductivity is due to the remarkable decrease of crystallinity upon the addition of copper-oxide filler into PEO matrix of SPEs. The fabricated SPEs with the dendritic copper-oxide fillers present a total ionic transference number of 0.99 and a lithium-ion transference number of 0.38. More importantly, it presents a stable potential window of 2.0–4.8 V at 25 °C and high thermal stability up to 300 °C. The specific discharge capacity of the prepared cell with the dendritic filler-contained SPEs is measured to be 51 mA h g−1 and 125 mA h g−1 under 0.1 current-rate (C-rate) at 25 °C and 60 °C, respectively. In this study, the ionic conductivity and the electrochemical performance of the PEO-based polymer electrolyte have been evaluated when morphologically different copper-oxide fillers have been incorporated into the PEO matrix. We have also confirmed the safety and the flexibility of the prepared solid polymer electrolytes when they are used in flexible lithium-metal polymer batteries (LMPBs).


Introduction
In recent years, the lithium-ion batteries have been used in energy storage devices as a power source for the operation of portable electronics and other energy storage systems (ESS), because they present high energy density and relatively stable power density. [1][2][3][4][5] In commercial lithium-ion batteries, however, there is the critical safety issue related to the explosion of nonaqueous liquid electrolytes when they are exposed to water vapor in the air. To solve this safety problem in lithium batteries, many researchers have turned to solid polymer electrolytes (SPEs) as an alternative electrolyte, which can replace liquid electrolytes for the next-generation lithium batteries. [6][7][8][9] The solid polymer electrolytes (SPEs) have several advantages including good stability during the charge-discharge cycles, light weight, wide working temperature range, high energy density, and non-ammability. [10][11][12] Furthermore, various designs of lithium batteries with these solid polymer electrolytes can be implemented due to their exible property. [13][14][15][16] Recently, some solid polymer electrolytes have been developed with several types of polar polymers such as polyethylene oxide (PEO), polyvinyl acetate (PVA), polycarbonate (PC), polyvinylidene uoride (PVdF), and so on. [17][18][19][20][21] So far, polyethylene oxide (PEO) is the most widely used polymer matrix in the SPEs for the Li-metal batteries, due to its high chain exibility. 22,23 In addition, the PEO can effectively dissolve the various lithium salts in it by organizing lithium ion with ether oxygen of PEO through the coupling effect. 24 In the PEO, the migration of lithium ion generally occurs in the amorphous region, which facilitates higher segment motion of PEO matrix, because of low barriers to rotating ions in the main matrix. 25 At ambient temperatures, however, the PEO has low ionic conductivity due to the limited segment motion of the matrix. It represents that the intrinsic PEO contains the high crystalline region, which heavily hinders lithium ion mobility, leading to low ionic conductivity. 26 Therefore, the crystalline region in the PEO should be reduced to improve ionic conductivity of the SPEs. [27][28][29] To enhance ionic conductivity of the solid polymer electrolytes, one of the approaches is the addition of the organic or ionic liquid into the SPEs as a plasticizer. [30][31][32][33] With these plasticizers, however, the SPE itself becomes weak in mechanical strengths and ammable. Another approach is the addition of inorganic materials as a ller, which seems to be better method to enhance ionic conductivity and interfacial stability because the mechanical strength of SPE has been maintained. The inorganic llers, such as metal oxides, clays, metal-organic frameworks (MOFs), and carbon nanotubes (CNTs), have been proposed and reported that they present the improvement of ionic conductivity and electrochemical performance in Libattery application, due to the several benecial effects as an inorganic ller. [34][35][36][37][38] One is that the inorganic llers physically prevent the PEO from recrystallization of its chain, resulting more amorphous region produced. 39 The inorganic ller also accelerates the dissociation of PEO segment and makes more free anions, which increases lithium ion mobility, according to the Lewis acid-base interactions between the inorganic llers and the lithium salt. 40 The other effect is that the inorganic ller forms the Li + ion conducting pathways on the inorganic ller itself. 41 Because of these benecial effects, the use of inorganic llers in the SPEs has been considered for the application in Limetal polymer batteries (LMPBs). [42][43][44][45][46] In this work, we use the copper oxides of different morphologies as an inorganic ller and identify the morphological effect of the inorganic ller on the electrochemical performance of the solid polymer electrolytes. The SPEs are prepared with a blending method using polyethylene oxide (PEO) as a polymer matrix, bis(triuoromethanesulfonyl)imide (LiTFSI) as a lithium salt, and inorganic llers of either spherical or dendritic copper-oxide powders, respectively. The dendritic copper-oxide powders used in this work have been prepared with the spontaneous galvanic displacement reaction, of which details are noted in our previous work. 47 These highsurface-area powders of dendritic morphologies are supposed to interact more with the PEO matrix than the spherical particles, which results the reduction of crystalline phase in PEO. Hence, the structural effect of the inorganic llers on the ion conductivity and the electrochemical performance of the fabricated polymer electrolyte have been analyzed and evaluated for the use in Li-metal batteries.

Preparation of dendritic copper oxide ller
Dendritic copper powders are synthesized using the spontaneous galvanic displacement reaction, of which process steps are as follows. At rst, the aluminum plate (8 cm Â 7 cm) is immersed in 1 M KOH solution for 3 min to remove the oxide layer. This pre-treated aluminum plate has been put into the aqueous solution of 0.1 M CuSO 4 $5H 2 O, 1 M NaCl, and 0.2 M HCl for 30 min, in which the dendritic copper powders is synthesized with the galvanic displacement reaction between the aluminum and copper ions on the plate. The obtained dendritic copper powders are then rinsed with DI water and ethanol for several times until solution become neutral. Aer drying in vacuum at 70 C for 12 h, the fabricated copper powders are grinded with mortar then oxidized at 200 C for 2 h in air.

Preparation of the solid polymer electrolytes (SPEs)
Lithium bis(triuoromethylsulfonyl)imide (LiTFSI) and polyethylene oxide (PEO, M.W. 4.0 Â 10 5 ) with a molar ratio of 1 : 15, respectively, are dissolved in acetonitrile (anhydrous, >99.8%) solvent and stirred for 24 h at 50 C. The dendritic or the spherical copper-oxide powders of 5 wt% is added and dispersed well into the solution. The homogeneous solution is spilled on a Teon dish and then placed in an oven at 50 C for 12 h. Subsequently, the lm is further dried in vacuum at 50 C for 48 h until the solvent is completely evaporated. To be assembled in battery cells, the dried electrolyte lm is cut into a disk (Ø 18 mm) using the punching tool.

Preparation of the electrode and the cell
In a slurry for cathode preparation, the LiFePO 4 of 70 wt% as active materials, the Super-P of 20 wt% as conducting materials, the polyvinylidene uoride (PVdF) of 10 wt% as a polymer binder, and the N-methyl-2-pyrrolidone (NMP) as a solvent are used. The slurry is uniformly pasted onto an aluminum foil using a Doctor's Blade and then dried in vacuum at 110 C for 24 h. Aer the simple mechanical pressing, the prepared cathode is ready to be assembled in a battery cell, on which active material is loaded with 1.6 mg cm À2 . As an anode, lithium metal foil of 300 mm is used. The CR2032 battery cells of [Li|the solid polymer electrolyte|LiFePO 4 ] are assembled in a glovebox under argon environment.

Structural characterization
The morphologies of copper-oxide llers and SPEs are characterized using eld-emission scanning electron microscope (FE-SEM, JSM7000F, JEOL), and the particle size of the llers are analyzed with the particle size analyzer (PSA, Malvern, MS3000_MV&LV). The crystal structures and the chemical states of llers are also evaluated with the powder X-ray diffraction (PXRD, SmartLab, Rigaku) using Cu Ka radiation (l ¼ 1.5418 A) between 10 and 80 of 2q with 2 min À1 . Separately, the additional characterization on the crystalline nature of SPEs has been also characterized with high-resolution X-ray diffraction (HRXRD, SmartLab, Rigaku) and differential scanning calorimetry (DSC, DSC7020, SEICO INST.). In the DSC measurement, the sample has been heated in 80-100 C at 10 C min À1 under nitrogen ambient.

Thermal analysis
Thermal stability of solid polymer electrolytes is measured by the thermogravimetric analysis (TGA, TG/DTA 7300, SEICO INST) in the temperature range between 25 C and 500 C with the heating rate of 10 C min À1 under nitrogen. The thermal durability of the solid polymer electrolytes is also evaluated at 300 C.

Electrochemical characterization
The ionic conductivity of the SPEs is analyzed by electrochemical impedance spectroscopy (EIS) technique using ZIVE SP1 analyzer supplying 10 mV of voltage amplitude in the frequency range of 1 Hz to 1 MHz at various temperatures. In the measurement, the prepared SPEs are sandwiched in between two blocking electrodes (stainless steel, Ø 16 mm), and the ionic conductivity (s) of SPEs is estimated with the following equation: where l is the thickness of the SPEs, A is the area of blocking stainless steel, R p is the resistance of the electrolyte that is related to the intersection of straight line onto the x-axis in an electrochemical impedance spectrum. 48 The ionic transference number (t ion ), lithium-ion transference number (t Li +), and the linear sweep voltammetry (LSV) studies are gured out using WMPG 1000S analyzer managed by WMPG 3.3 soware (Wonatech). The ionic transference number (t ion ) is analyzed using DC polarization technique at 25 C. The two stainless-steel blocking electrodes are used as same as in ionic conductivity measurement, and the current is monitored as a gure of time at 10 mV for 1 h. The ionic transference number (t ion ) is calculated with the following equation: where i T is total current, and i e is residual current. 49 On the other hands, the lithium-ion transference number (t Li + ) is calculated using AC/DC polarization technique at 25 C. At this time, two lithium metal electrodes are used, and the prepared SPEs are placed between these two Li electrodes. The currents are monitored when the 10 mV has been applied for 4 h. The resistances are studied before and aer polarization by the AC impedance technique. The lithium-ion transference number (t Li + ) of prepared SPE is calculated with the Bruce-Vincent's equation: where I 0 and I s.s is initial and steady-state current value, respectively, and R 0 and R s.s is resistance of the cell before and aer polarization, respectively. 50 The electrochemical stability window of the prepared SPEs is determined using linear sweep voltammetry (LSV) from 2 V to 6 V at the voltage rate of 1 mV s À1 at 25 C. Prepared SPEs are again sandwiched in between a working electrode of stainless steel and a counter electrode of lithium metal. 51 The galvanostatic charge-discharge (GCD) cycling test in CR2032 cells (Li|solid polymer electrolyte|LiFePO 4 ) is also carried using WMPG 1000S analyzer. Aer the 24 h heat treatment at 80 C for the solid contact between electrodes and the SPE lm, the GCD cycles are performed from 2.8 V to 4.2 V at various current rates (1C ¼ 150 mA h g À1 ) at various temperatures.

Results and discussion
3.1 Characterization of dendritic copper-oxide powders used as llers The dendritic copper powders are fabricated by the spontaneous galvanic displacement reaction, of which process steps are reported elsewhere in detail. 47,52 The dendritic copper powders are then oxidized with the annealing at 200 C for 2 h. As observed in Fig. 1a, the morphology of the dendritic particles has not been changed even aer the oxidation at 200 C. The prepared dendritic powders are D 50 ¼ 2.81 mm in size, based on the analysis results of particle size analyzer (cf. Fig. 1b).
The oxidation states and crystallinity of the dendritic powders are also characterized a little more in detail using the X-ray diffraction (XRD) patterns shown in Fig. 1c. Aer the oxidation step, the prepared dendritic powders show XRD peaks at several 2q values, such as 35.5 , 37.1 , 38.8 , and 63.2 . Compared with Cu (no. 04-0836), Cu 2 O (no. 05-0667), and CuO (no. 45-0937) of JCPDS indexes, the peaks identied with Cu 2 O (b) and CuO (g) are evident without any apparent peaks of metallic Cu (a), which conrms that the prepared powders are mostly oxidized into Cu 2 O and CuO, while their dendritic structures are maintained.

Morphology and crystallinity
In the fabrication of solid polymer electrolyte, the P(EO) 15 LiTFSI lm has been prepared with polyethylene and LiTFSI, of which molar ratio is 15 : 1 in this work. The FE-SEM images in Fig. 2 show the morphologies of intrinsic P(EO) 15 LiTFSI without llers, 5 wt% spherical ller-contained P(EO) 15 LiTFSI, and 5 wt% dendritic ller-contained P(EO) 15 LiTFSI, respectively. In the image of intrinsic P(EO) 15 LiTFSI lm, the isolated semicrystalline spherulitic morphology is very remarkably evident, which indicates the existence of crystalline PEO. 53 As shown in Fig. 2b, these spherulitic features are reduced and get smaller on the surface of the spherical ller-contained P(EO) 15 LiTFSI than that on the intrinsic P(EO) 15 LiTFSI, due to the suppression of recrystallization by the inorganic ller particles in the PEO matrix. 54 Notably, for the dendritic llercontained P(EO) 15 LiTFSI, the spherulitic morphology signicantly disappears on the surface (see Fig. 2c), which represents that dendritic particles are highly impeding the recrystallization of PEO by the sufficient interaction with PEO matrix at their hierarchical structures of high surface area. Such recrystallization features in PEO matrix are also conrmed by XRD and DSC analyses (vide infra). To elucidate the degree of recrystallization of the PEO matrix, the XRD patterns are carefully analyzed, based on the addition of lithium salt (LiTFSI) and copper-oxide llers. Fig. 3 presents the XRD patterns of pure PEO, recrystallized intrinsic P(EO) 15 LiTFSI, 5 wt% spherical ller-contained P(EO) 15 LiTFSI, and 5 wt% dendritic ller-contained P(EO) 15 LiTFSI.
In Fig. 3a, two strong XRD peaks at 2q ¼ 19.2 and 23.4 are appeared due to its semi-crystalline nature of PEO, which are assigned to the (1 2 0) and (1 1 2), respectively. 55 As the reduction of peak intensities noticed in Fig. 3, this semi-crystalline feature has been suppressed during the recrystallization step, once it has been dissolved and recrystallized aer the addition of   15 LiTFSI, (b) 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and (c) 5 wt% dendritic fillercontained P(EO) 15 LiTFSI.
This journal is © The Royal Society of Chemistry 2019 LiTFSI and inorganic llers. During the recrystallization, the Li + , TFSI À , and inorganic llers are incorporated into the PEO matrix, which causes the reduction of crystalline phase and the increase of amorphous region in the recrystallized PEO.
In the cases of ller-contained SPE lm, the patterns of copper oxide additionally appear at 2q ¼ 35.7 and 37.5 . In addition, the morphological difference of inorganic llers makes the degree of re-crystallinity different, as noticed in Fig. 3c and d. The high-surface-area dendritic llers reduce the crystalline peak intensities at 2q ¼ 19.1 and 23.2 more than the spherical llers, even when the same amount has been added in weight. It is possibly because the inorganic llers hinder the dissolved PEO from recrystallization at the interface of organic and inorganic materials surface. Therefore, the sufficient interaction between the high-surface-area dendritic llers and the dissolved PEO results less crystalline phase and more amorphous region in the recrystallized matrix, which is consistent with the microscopic images (vide ante).
The differential scanning calorimetry (DSC) is also performed to investigate the phase change behavior of SPEs, such as glass transition temperature (T g ), melting temperature (T m ), and degree of crystallinity (c c ). All of the measurement data are summarized in Table 1, which are evaluated from the DSC data obtained during the 2 nd heating to remove any thermal history. The DSC thermos grams of pure PEO, intrinsic P(EO) 15 LiTFSI, 5 wt% spherical llercontained P(EO) 15 LiTFSI, and 5 wt% dendritic llercontained P(EO) 15 LiTFSI are presented in Fig. 4.
An endothermic peak of melting temperature (T m ) of the crystalline state of pristine PEO is obtained at the temperature of 66.48 C, while the transition from rigid to exible phase of PEO (T g ) is observed at the temperature of À54.2 C (see Fig. 4a). When the LiTFSI has been added into PEO matrix, the glass transition temperature (T g ) rises to À47.61 C, because the mobility of EO segment is lowered. As also shown in Fig. 5b, the T m of this intrinsic P(EO) 15 LiTFSI is decreased to 51.15 C due to  15 LiTFSI, (c) 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and (d) 5 wt% dendritic fillercontained P(EO) 15 LiTFSI. Table 1 Glass-transition temperature (T g ), melting temperature (T m ), melting enthalpy (H m ), and the degree of crystallinity (c c ) values of pure PEO, intrinsic P(EO) 15 LiTFSI, 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and 5 wt% dendritic filler-contained P(EO) 15 LiTFSI   15 LiTFSI, (c) 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and (d) 5 wt% dendritic filler-contained P(EO) 15 LiTFSI.
the strong electron-withdrawing group (-SO 2 CF 3 ) and the highly dissociated ions from LiTFSI in the PEO segment caused by highly exible segment (-N(SO 2 ) 2 ). 22 When two different llers are incorporated into the intrinsic P(EO) 15 LiTFSI, the T g and the T m are moved towards lower temperatures as well, due to the interaction between PEO segment and copper-oxide llers (cf. Fig. 4c, d and Table 1). Decrease in T g and T m of copper-oxide ler-contained PEO highlights the exible matrix of PEO. It attains the exible partial movement of ions in PEO matrix resulting to higher ionic conductivity of SPEs. The degree of crystallinity (c c ) of SPEs is analyzed using the values of the melting enthalpy (DH m ) of prepared SPEs and the melting enthalpy (DH PEO ¼ 213.7 J g À1 ) of 100% crystalline PEO, as noted in the following equation: 56 As listed in Table 1, the degree of crystallinity (c c ) was decreased from 57.55% to 24.00% when the LiTFSI was added into pure PEO. It was drastically reduced down to 13.89% and 13.43% when the spherical and the dendritic copper-oxide llers were dispersed into the intrinsic P(EO) 15 LiTFSI, respectively. On the comparison between the spherical and the dendritic morphologies of copper-oxide llers, it has been found that the dendritic llers interact more with the PEO matrix and form more amorphous structures in the SPEs than the spherical llers, resulting in the decrease of the crystallinity of the SPEs.

Thermal properties
Thermal stability of the SPEs was characterized using the thermo-gravimetric analysis (TGA). The thermo-grams of pure PEO, intrinsic P(EO) 15 LiTFSI, 5 wt% spherical ller-contained P(EO) 15 LiTFSI, and 5 wt% dendritic ller-contained P(EO) 15 -LiTFSI are shown in Fig. 5. The weight of SPEs is generally reduced by 4-6% at 150 C, due to the evaporation of moisture in SPEs. 41 The pure PEO has single-step decomposition at around 370 C, whereas the intrinsic P(EO) 15 LiTFSI has two-step decompositions at 380 C and 430 C, as presented in Fig. 5a and b, respectively. For the intrinsic P(EO) 15 LiTFSI, rst decomposition step at around 380 C is related to the noncomplexed PEO, which was slightly shied from 370 C. The second decomposition step at around 430 C is caused by the complex of LiTFSI and PEO matrix. 57 On the other hands, two TGA curves for 5 wt% spherical ller-contained P(EO) 15 LiTFSI and 5 wt% dendritic llercontained P(EO) 15 LiTFSI have three-step decomposition, as noticed in Fig. 5c and d. First decomposition observed at 300 C is related to the complex of copper oxide and PEO matrix. Second step at 380 C and third step at 430 C imply the noncomplexed PEO and the complex of LiTFSI salt and PEO matrix, respectively, as same as those of intrinsic P(EO) 15 LiTFSI. It represents that the prepared SPEs with copper-oxide llers are thermally stable up to 300 C and fairly good for the battery application.  15 LiTFSI, (c) 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and (d) 5 wt% dendritic filler-contained P(EO) 15 LiTFSI.

Electrochemical properties
Linear sweep voltammetry (LSV) was carried out to investigate the stable operation voltage and the electrochemical stability of SPEs for the use as an electrolyte in a lithium polymer battery. The LSV curve of the cell (Li|5 wt% dendritic ller-contained P(EO) 15 LiTFSI|stainless steel) obtained at 25 C is shown in Fig. 6(a). The current density recorded in the potential range of 2.0-4.8 V (vs. Li/Li + ) was almost negligible. Though the oxidation occurs drastically at the potential above 5 V (vs. Li/Li + ), the stable operation potential is wide enough for lithium-battery application. For investigating the electrochemical stability of SPE, the cyclic voltammetry measurement was also carried out for 4 cycles at a scan rate of 0.5 mV s À1 in the voltage range up to 5 V, and the respective data is shown in Fig. 6(b). It can be seen from the data that there is no any oxidation and reduction peak in the measured voltage range indicating the good electrochemical stability of SPE.
Ionic conductivity of the SPEs is one of the most important factor for the use in the battery application, because it is directly associated with the major performance of LMPBs. Fig. 7a and b show the Nyquist plots of intrinsic P(EO) 15 LiTFSI, 5 wt% spherical ller-contained P(EO) 15 LiTFSI, and 5 wt% dendritic ller-contained P(EO) 15 LiTFSI monitored at 30 C and 60 C, respectively. Using the values in Nyquist plots, the calculated ionic conductivity (s) at 30 C was 0.7258 Â 10 À4 S cm À1 and 1.007 Â 10 À4 S cm À1 for 5 wt% spherical ller-contained P(EO) 15 LiTFSI and 5 wt% dendritic ller-contained P(EO) 15 -LiTFSI, respectively. These values are more than twice as high as that of intrinsic P(EO) 15 LiTFSI without the llers (s ¼ 0.3623 Â 10 À4 S cm À1 ). The increase of ionic conductivity in the llercontained P(EO) 15 LiTFSI arises from the increase in the amorphous region of the PEO matrix by adding the copper-oxide llers, as explained in the discussions of XRD and DSC data. It is known that more amorphous region of SPEs provides the higher ionic conductivity, as also reported in the literature. 39 Furthermore, the ionic conductivity of 5 wt% dendritic llercontained P(EO) 15 LiTFSI is about 1.3 times higher than that of 5 wt% spherical ller-contained P(EO) 15 LiTFSI at 30 C. It is related to sufficient interaction of PEO matrix with the highsurface-area dendritic llers than the relatively smaller surface-area spherical llers. At 60 C, the ionic conductivity of SPEs was increased to 0.9615 Â 10 À3 S cm À1 and 1.368 Â 10 À3 S cm À1 for 5 wt% spherical ller-contained P(EO) 15 LiTFSI   8 Typical DC polarization curve for the cell of (stainless steel|5 wt% dendritic filler-contained P(EO) 15 LiTFSI|stainless steel) at 25 C. and 5 wt% dendritic ller-contained P(EO) 15 LiTFSI, respectively, whereas the ionic conductivity of intrinsic P(EO) 15 LiTFSI was less increased to 0.457 Â 10 À3 S cm À1 . It is because the ion mobility has been enhanced in the amorphous region of SPEs at higher temperatures.
The Fig. 7c presents temperature dependency of the ionic conductivities of the prepared SPEs in this work. Overall, it shows that ionic conductivity (s) of SPEs has been improved as temperature increases, following the Arrhenius-type activated process. As the temperature approaches up to phase-transition temperature (T trans ) of PEO, the sharp increase in ionic conductivity of SPEs has been monitored, while the ionic conductivity increases slowly as the temperature goes over the T trans of PEO as interpreted by log s vs. 1/T plots of Fig. 7c. The activation energy of temperature-dependent ionic conductivity is obtained according to Arrhenius-type behavior given in the following equation: 41 where s represents the ionic conductivity, s o is the preexponential factor, E a is the activation energy, k is the Boltzmann constant, and T is the absolute temperature in Kelvin. The 5 wt% dendritic ller-contained P(EO) 15 LiTFSI polymer presents the lowest activation energy among all the prepared SPEs, as shown in Fig. 7c, of which lower activation energy provides higher ion mobility. 22 This high ion mobility has been achieved by the abundant amorphous phase in the dendritic ller-contained P(EO) 15 LiTFSI polymer produced with vigorous interaction between llers and PEO matrix. As shown in Fig. 8, the DC polarization curve has been also obtained using the cell of (stainless steel|5 wt% dendritic llercontained P(EO) 15 LiTFSI|stainless steel) at 25 C. The total ionic transference number (t ion ) of dendritic ller-contained P(EO) 15 LiTFSI was then evaluated by the eqn (2). The t ion value was observed to be 0.99, which means that the ionic conductivity has been contributed by almost all the present ions in the polymer. To estimate the specic distribution of Li + ion in LMPBs, the lithium-ion transference number (t Li +) in the llercontained P(EO) 15 LiTFSI are also examined by the AC/DC polarization using the cell of (Li|ller-contained P(EO) 15 -LiTFSI|Li) at 25 C. The lithium-ion transference numbers (t Li + ) were calculated by using the eqn (3). The t Li + value was 0.29 and 0.38 for 5 wt% spherical ller-contained P(EO) 15 LiTFSI and 5 wt% dendritic ller-contained P(EO) 15 LiTFSI, respectively (cf. Fig. 9a and b), whereas the t Li + value of intrinsic P(EO) 15 LiTFSI was only 0.17. 58 The higher t Li + value of the polymer provides the better electrochemical performance as the SPEs, 59,60 which is explained by the increased ion mobility due to the Lewis acidbase effect. Furthermore, the value of t Li + for dendritic llercontained P(EO) 15 LiTFSI is higher than that of spherical llercontained P(EO) 15 LiTFSI, which represents that dendritic ller-contained polymer presents better ion mobility in it. It is consistent with all the results of SEM, XRD, and DSC. Fig. 9 Typical DC polarization curves obtained from (a) 5 wt% spherical filler-contained P(EO) 15 LiTFSI and (b) 5 wt% dendritic filler-contained P(EO) 15 LiTFSI (inset shows Nyquist plots of AC polarization before and after DC polarization at 25 C).

Fig. 10
Galvanostatic cycling performance of the Li symmetrical cells with 5 wt% dendritic filler-contained P(EO) 15 LiTFSI polymer electrolyte at a constant current density of 0.1 mA cm À2 . Each half-cycle of charging and discharging step lasts 2 h at 25 C.
This journal is © The Royal Society of Chemistry 2019 3.5 LMPB cell performance Fig. 10 shows the performance of the lithium symmetric cell at 25 C with 5 wt% dendritic ller-contained P(EO) 15 LiTFSI polymer electrolyte. The half cycle of charging and discharging step was 2 hours, respectively. The cell potential was maintained stably during the repeated cycles of charging-discharging at a constant current density of 0.1 mA cm À2 .
The cyclic performances are measured with the coin cell of (Li|5 wt% dendritic ller-contained P(EO) 15 LiTFSI|LiFePO 4 ), in which the capacity evaluation of rst cycle is excluded due to the usual SEI formation process. Fig. 11a presents the galvanostatic charge/discharge curves at various current rates (C-rates) at 25 C. The specic discharge capacities of the cell were 51.03, 35.19, 20.19, 15.94, and 0.8 mA h g À1 at 0.1, 0.2, 0.3, 0.5, and 1 Crate at 25 C, respectively. The specic discharge capacities are observed to decrease with increase in C-rate as usual, which is caused by a large polarization. 61 In general, the LMPBs with the SPEs based on PEO matrix hardly operate at 25 C. However, the prepared LMPB with the dendritic ller-contained SPEs in this work has the discharge capacity of 51.03 mA h g À1 at 0.1 C-rate, because of its high ionic conductivity even at 25 C.
As the cell operating temperature increases to 60 C, the specic discharge capacity has improved drastically to 125, 113, 97, 78, and 52 mA h g À1 at 0.1, 0.2, 0.3, 0.5, and 1 C-rate, respectively (see Fig. 11b). These values of discharge capacities are suitable enough for LMPB application. This improvement is due to the crystallinity changes of PEO matrix in SPEs at different temperatures as discussed in DSC results (cf. Fig. 4).
For further evaluation on the effect of ller morphology in SPEs on the cell performance, the rate capabilities of the cells with intrinsic P(EO) 15 LiTFSI, 5 wt% spherical ller-contained P(EO) 15 LiTFSI, and 5 wt% dendritic ller-contained P(EO) 15 -LiTFSI are compared at different temperatures. The specic Fig. 11 The galvanic charge-discharge profiles of (Li|LiFePO 4 ) cell using 5 wt% dendritic filler-contained P(EO) 15 LiTFSI with various current rates at (a) 25 C and (b) 60 C, and the rate performance of (Li|LiFePO 4 ) cell with intrinsic P(EO) 15 LiTFSI, 5 wt% spherical filler-contained P(EO) 15 LiTFSI, and 5 wt% dendritic filler-contained P(EO) 15 LiTFSI at (c) 25 C and (d) 60 C. capacities at various current rates (C-rates) at 25 C are shown in Fig. 11c. When the intrinsic P(EO) 15 LiTFSI was used in the cell, the specic capacity was 7 mA h g À1 at 0.1 C-rate at 25 C, which means that it is hardly operated at 25 C. On the other hands, the SPEs with the llers were operated reasonably at low current rates even at 25 C. Moreover, the cell performance of the cell with the 5 wt% dendritic ller-contained P(EO) 15 LiTFSI is higher than that with 5 wt% spherical ller-contained P(EO) 15 LiTFSI. Furthermore, the specic capacities of the cell increase drastically at 60 C, as shown in Fig. 11(d). The 5 wt% dendritic ller-contained P(EO) 15 LiTFSI also shows higher performance than the other solid polymer electrolytes, due to its superior ionic conductivity through the amorphous phase of PEO in the SPEs.
To elucidate the merits of solid polymer electrolytes, we have assembled the pouch cell of (Li|5 wt% dendritic ller-contained P(EO) 15 LiTFSI|LiFePO 4 ) operating the light-emitting diode (LED) aer it has been cut and folded as shown in Fig. 12. The cell still works properly and lights the light-emitting diode, which conrms safety and exibility of the Li-metal polymer battery with the prepared solid polymer electrolyte in this work.

Conclusions
The crystallinity of PEO matrix has been modied by adding the two different morphologies of copper-oxide llers in the fabrication of solid polymer electrolytes (SPEs) for the application of lithium-metal polymer batteries (LMPBs). Both copper-oxide llers of spherical and dendritic morphologies improve the ionic conductivity of the SPEs and their electrochemical performance, due to the generation of amorphous phase in the PEO matrix. The dendritic ller-contained SPE presents better electrochemical performance, of which surface interacts more with the PEO matrix and produces more amorphous phase. The ionic conductivity (s) of the dendritic ller-contained P(EO) 15 -LiTFSI is 1.007 Â 10 À4 S cm À1 and 1.368 Â 10 À3 S cm À1 at 30 C and 60 C, respectively. The dendritic ller-contained P(EO) 15 -LiTFSI is thermally stable up to 300 C and electrochemically stable up to 4.8 V. The (Li/LiFePO 4 ) cell with the copper-oxide ller contained P(EO) 15 LiTFSI shows the enhanced discharge capacity of 125 mA h g À1 under 0.1 C-rate at 60 C, whereas the cell is still operating even at 25 C with 51.03 mA h g À1 . In this work, the dendritic structure of copper-oxide llers delivers better morphological effect on the enhancement of ionic conductivity by producing amorphous phase in the PEO matrix more than the spherical llers. The safety and the exibility of dendritic ller-contained SPEs in LMPBs application are also demonstrated.

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