Quasi-Solid-State SiO2 Electrolyte Prepared from Raw Fly Ash for Enhanced Solar Energy Conversion

Quasi-solid-state electrolytes in dye-sensitized solar cells (DSSCs) prevent solvent leakage or evaporation and stability issues that conventional electrolytes cannot; however, there are no known reports that use such an electrolyte based on fly ash SiO2 (FA_SiO2) from raw fly ash (RFA) for solar energy conversion applications. Hence, in this study, quasi-solid-state electrolytes based on FA_SiO2 are prepared from RFA and poly(ethylene glycol) (PEG) for solar energy conversion. The structural, morphological, chemical, and electrochemical properties of the DSSCs using this electrolyte are characterized by X-ray diffraction (XRD), high-resolution field-emission scanning electron microscopy (HR-FESEM), X-ray fluorescence (XRF), diffuse reflectance spectroscopy, electrochemical impedance spectroscopy (EIS), and incident photon-to-electron conversion efficiency (IPCE) measurements. The DSSCs based on the quasi-solid-state electrolyte (SiO2) show a cell efficiency of 5.5%, which is higher than those of nanogel electrolytes (5.0%). The enhancement of the cell efficiency is primarily due to the increase in the open circuit voltage and fill factor caused by the reduced electron recombination and improved electron transfer properties. The findings confirm that the RFA-based quasi-solid-state (SiO2) electrolyte is an alternative to conventional liquid-state electrolytes, making this approach among the most promising strategies for use in low-cost solar energy conversion devices.


Introduction
In recent years, the recovery of SiO 2 from industrial and agricultural waste (e.g., rice husk ash, semi-burned rice straw ash, bagasse ash, corn cob ash, coal fly ash, and bottom ash) has been extensively investigated due to the potential applications of SiO 2 in chemical sensors and drug delivery, and as absorbents and catalyst supports [1][2][3][4][5]. Among the silica-enriched wastes, coal fly ash (FA) is generated at 1200-1700 • C during the combustion of coal in power plants and contains many metal oxides such as SiO 2 , Al 2 O 3 , Fe 2 O 3 , CaO, MgO, TiO 2 , Na 2 O, and K 2 O [6]. In order to address challenges associated with the large-scale production of FA (750 million tons per year) and its harmful impacts on the environment, a new reutilization strategy was developed to recover SiO 2 from FA and use it in various applications. One study reported a combined organic acid/inorganic alkali/ultrasonication-assisted process for the extraction of SiO 2 from FA; the prepared SiO 2 showed good adsorption capacity toward methylene blue and malachite green [7]. Mesoporous silica (MCM-41) was prepared from FA using cetyltrimethylammonium bromide (CTAB) as a template; this FA-derived MCM-41, impregnated with polyethyleneimine, exhibited higher uptakes of CO 2 than commercial silica products [8]. FA-derived mesoporous CdS/Al-MCM-41 composites were synthesized using the Si and Al extracted from FA, then applied as a photocatalyst for hydrogen production by the decomposition of H 2 O under visible light [9]. However, there is limited knowledge on the application of FA-derived SiO 2 in solar energy conversion of renewable industrial applications.
Since the development of dye-sensitized solar cells (DSSCs) by the Grätzel group, DSSCs have received immense attention as a promising high-efficiency, low-cost energy source for solar energy conversion [10]. DSSCs comprise a transparent conductive substrate, a photoanode, sensitizers, electrolytes, and a counter electrode [11][12][13][14][15][16][17][18]. Electrolytes are a vital component of DSSCs, as they provide electrons that allow the sensitizers to return from an excited state to the ground state, thereby completing sensitizer regeneration. However, conventional liquid electrolytes in DSSCs present drawbacks that mostly stem from solvent leakage or evaporation issues and lower the stability of devices. Therefore, many studies have focused on replacing the conventional liquid electrolytes used in DSSCs with ionic liquids, hole-transport materials, and quasi-solid-state electrolytes in order to reduce the risk of leakage and environmental hazards [19][20][21]. Among them, the quasi-solid-state electrolytes based on low-molecular-weight polymers and inorganic nanomaterials exhibit ionic conductivities close to those of a conventional liquid electrolyte but maintain their quasi-solid-state electrolyte structures, thereby reducing solvent leakage and evaporation problems and enhancing mechanical properties. The excellent penetration of low-molecularweight polymers into the photoanode is attributed to the improved interfacial contact between the photoanode/sensitizer surface and the quasi-solid-state electrolytes, which enables effective utilization of the sensitizer. Further, quasi-solid-state electrolytes offer advantages for electrochemical devices such as rechargeable batteries and supercapacitors in avoiding solvent leakage or evaporation and stability issues. Hence, it is expected that they can provide the same benefits when used with DSSCs as well.
In this work, FA_SiO 2 was prepared from acetic acid-treated non-magnetic raw fly ash (RFA) and used as a quasi-solid-state electrolyte in DSSCs to improve their solar energy conversion efficiency. Detailed characterizations were conducted by X-ray diffraction (XRD), high-resolution field-emission scanning electron microscopy (HR-FESEM), X-ray fluorescence (XRF), diffuse reflectance spectroscopy, electrochemical impedance spectroscopy (EIS), and incident photon-to-electron conversion efficiency (IPCE) measurements. To the best of our knowledge, there has been no report on such a quasi-solid-state electrolyte based on FA_SiO 2 from RFA for solar energy conversion applications.

Synthesis of FA_SiO 2 from RFA
The overall synthetic procedures are illustrated in Scheme 1. An exact amount of raw fly ash (RFA) (50.0 g) was added to a glass beaker containing 500 mL of DIW and mechanically stirred at 500 rpm for 1 h. After 1 h of water-washing, magnetic iron-rich fly ash (IRFA) particles were separated by placing a parafilm-wrapped neodymium magnet into the RFA-DIW suspension; the parafilm was detached from the magnet to collect the separated magnetic IRFA. This process was performed repeatedly until no more magnetic particles were attached to the parafilm-wrapped magnet. The separated IRFA and nonmagnetic fly ash (NMFA) were washed with DIW three times by centrifugation (7000 rpm, 3 min) and oven-dried at 105 • C for 24 h. NMFA was pre-treated with acetic acid to remove minor impurities. An exact amount of NMFA (20.0 g) was mixed with 5 M acetic acid (200 mL) under continuous stirring (700 rpm) for 2 h at room temperature. After the pretreatment, the mixture of NMFA and acetic acid was centrifuged for solid-liquid separation. The supernatant was removed, and the acetic-acid-treated NMFA particles were washed with DIW three times and dried in an oven at 105 • C for 24 h. The acetic acid-treated NMFA (5.0 g) was mixed with 6.25 M of NaOH solution (mass ratio of 1:5) to extract silica, and this mixture was treated at 100 • C for 2 h, resulting in the formation of sodium silicate solution (SiO 2 + 2NaOH → Na 2 SiO 3 + H 2 O). After 2 h, this mixture was filtrated to attain a transparent filtrate of sodium silicate (water glass). Subsequently, 90.0 mL of the filtrate was mixed with 100.0 mL of DIW under magnetic stirring (1000 rpm) and preheated at 80 • C, which was constant for the duration of silica precipitation. Sodium silicate was then slowly neutralized with diluted HCl solution to pH 8 to precipitate silica (Na 2 O·xSiO 2 + 2HCl → xSiO 2 ↓ + 2NaCl + H 2 O). At this pH and a temperature of 80 • C, the mixture was additionally stirred for 2 h. The precipitated silica was collected and washed with DIW three times (7000 rpm, 3 min). Lastly, the solid was dried in an oven at 105 • C for 24 h and ground to obtain a white fly ash SiO 2 (FA_SiO 2 ) powder.

Preparation of Nanogel and Quasi-Solid-State (SiO 2 ) Electrolytes
Particular attention was paid to 2 types of electrolytes for the fabrication of DSSCs: (1) a nanogel electrolyte consisting of PEG, MPII, LiI, and I 2 in acetonitrile; (2) a quasi-solidstate electrolyte consisting of FA_SiO 2 , PEG, MPII, LiI, and I 2 in acetonitrile. The mole ratio of ether oxygen (EO) to MPII, LiI was fixed at 20, the I 2 content was fixed at 10 wt% with respect to the salt, and the FA_SiO 2 content was fixed at 9 wt% with respect to PEG. (See Table S1) In addition, for the DSSC based on 2 types of electrolytes, the electrolyte loading was about 0.05 mg cm −2 .

Fabrication of DSSCs
The FTO glass was sonicated for 30 min before all fabrication methods with ethanol, acetone, and DIW. Spin-coating and the doctor-blade procedure were used to make a photoanode. Spin-coating the titanium diisopropoxide bis(acetylacetonate) solution (2 wt percent in 1-butanol) on the conducting side of the FTO glass at 1500 rpm for 20 s, followed by calcination at 450 • C for 30 min, resulted in a compact, thin TiO 2 blocking layer on the FTO glass. The blocking layer was cast using commercial TiO 2 paste using the doctor-blade process. A 3M sticky tape was used to adjust the film thickness. In order to prevent cracking during calcination, the substrate was warmed for 1 hour at 80 • C. A nanocrystalline TiO 2 layer with a thickness of 7 µm was produced after calcination at 450 • C for 30 min. The TiO 2 film layer was sensitized for 3 h in a dark environment using a 10 −4 M ruthenium solution in ethanol. After that, the dye-sensitized photoanodes were submerged in 100% ethanol for 5 min to remove any remaining dye. Spin-coating an H 2 PtCl 6 solution (1 wt percent in isopropyl alcohol) on the conducting side of the FTO glass at 1500 rpm for 20 s, followed by sintering at 450 • C for 30 min, yielded a platinum counter electrode. The photoanode and counter electrode were immediately cast with a quasi-solid-state electrolyte-based solution in acetonitrile for the DSSCs. Both electrodes were then overlaid and squeezed between two glass plates to allow the solvent and a thin Materials 2022, 15, 3576 4 of 12 electrolyte layer to evaporate slowly. According to previously documented techniques, the cells were placed in a vacuum oven for one day to allow the solvents to evaporate completely before being sealed with epoxy glue [22][23][24]. for 20 s, followed by sintering at 450 °C for 30 min, yielded a platinum counter electrode. The photoanode and counter electrode were immediately cast with a quasi-solid-state electrolyte-based solution in acetonitrile for the DSSCs. Both electrodes were then overlaid and squeezed between two glass plates to allow the solvent and a thin electrolyte layer to evaporate slowly. According to previously documented techniques, the cells were placed in a vacuum oven for one day to allow the solvents to evaporate completely before being sealed with epoxy glue [22][23][24]. Scheme 1. Diagram of FA_SiO2 synthesis from raw fly ash for the enhancement of solar energy conversion.

Characterization
HR-FESEM (SU8010, Hitachi High Technologies Corporation, Tokyo, Japan) with EDS was used to characterize the morphology of the produced FA SiO2 particles. XRD (JP/MAX-3C, Rigaku) was used to examine the mineral phases in RFA and FA SiO2 at 10-90° (2°/min). XRF (PANalytical, psilon3-XL) was used to examine the chemical components of RFA and FA SiO2. With a Brunauer-Emmett-Teller (BET) surface analyzer, the specific surface areas of the FA SiO2 samples were determined by nitrogen adsorption and desorption at -196 °C (3Flex, Micromeritics, Norcross, GA, USA). A spectrophotometer (Mega-900, Scinco) was used to produce UV-vis spectra in the range of 300-800 nm. Under one solar illumination, the photovoltaic properties of the cells were determined (100 mWcm −2 , 150 W xenon lamp, measured from −0.1 V to 0.8 V). EIS measurements were Scheme 1. Diagram of FA_SiO 2 synthesis from raw fly ash for the enhancement of solar energy conversion.

Characterization
HR-FESEM (SU8010, Hitachi High Technologies Corporation, Tokyo, Japan) with EDS was used to characterize the morphology of the produced FA SiO 2 particles. XRD (JP/MAX-3C, Rigaku) was used to examine the mineral phases in RFA and FA SiO 2 at 10-90 • (2 • /min). XRF (PANalytical, psilon3-XL) was used to examine the chemical components of RFA and FA SiO2. With a Brunauer-Emmett-Teller (BET) surface analyzer, the specific surface areas of the FA SiO 2 samples were determined by nitrogen adsorption and desorption at −196 • C (3Flex, Micromeritics, Norcross, GA, USA). A spectrophotometer (Mega-900, Scinco) was used to produce UV-vis spectra in the range of 300-800 nm. Under one solar illumination, the photovoltaic properties of the cells were determined (100 mWcm −2 , 150 W xenon lamp, measured from −0.1 V to 0.8 V). EIS measurements were taken with a CompactStat electrochemistry analyzer (Ivium Technologies) at frequencies ranging from 100,000 Hz to 0.1 Hz under one solar illumination and dark circumstances, respectively. A 150 W Xenon arc light source with a filter wheel and a 600 grooves/mm 500 nm blazed wavelength monochromator was used for the IPCE experiments (HS-Technologies). The photovoltaic results were also averaged over three samples.

Characterization of FA_SiO 2
The XRD patterns of RFA and the synthesized FA_SiO 2 are illustrated in Figure 1. The diffraction peaks of RFA are attributed to the occurrence of quartz (SiO 2 ) and mullite (Al 6 Si 2 O 13 ), and a broad hump (2θ = 20-35 • ) indicates the presence of amorphous aluminosilicate glass [25][26][27]. The result showed that RFA mainly consists of SiO 2 and Al 2 O 3 , which is in good agreement with the XRF data for RFA in Table 1. The XRD pattern of the synthesized FA_SiO 2 shows strong broad peaks centered at 2θ = 22-23 • , indicating the characteristic amorphous nature of silica, which is consistent with the characteristics of amorphous silica produced from bentonite clay, rice straw ash, rice husk, and bagasse ash [28][29][30][31][32][33][34].
which is in good agreement with the XRF data for RFA in Table 1. The XRD pattern of the synthesized FA_SiO2 shows strong broad peaks centered at 2θ = 22-23°, indicating the characteristic amorphous nature of silica, which is consistent with the characteristics of amorphous silica produced from bentonite clay, rice straw ash, rice husk, and bagasse ash [28][29][30][31][32][33][34].   The morphology and particle size of the FA_SiO 2 particles were observed by HR-FESEM at different magnifications, as illustrated in Figure 2. The images showed a noncrystalline structure of SiO 2 (Figure 2a,b), which is in good agreement with the XRD pattern of FA_SiO 2 . The images also revealed that the FA_SiO 2 nanoparticles are almost spherical in shape and aggregated to form bigger particles (Figure 2c,d), which is similar to the observations for typical amorphous silica produced from commercial sodium silicate solution [30]. EDS analysis was carried out, as shown in Figure S1. The elemental mapping images showed the location and quantities of the main elements (i.e., Si and O) and impurities contained in the extracted SiO 2 ( Figure S1b-d). Dense and uniform distribution of Si and O was observed throughout all particles, indicating that SiO 2 is the major constituent and relatively small amounts of impurities (i.e., Al, Fe, and Na) were mixed with SiO 2 . The EDS profile also revealed that the synthesized SiO 2 comprised O (54.29%), Si (32. 02%), Al (7.55%), Na (5.53%), and Fe (0.61%). It is suggested that elements such as Al and Fe dissolve to form oxyanions under alkaline conditions during the extraction of Si source from acetic acid-treated NMFA [35]. The BET analysis showed that the specific surface area of the prepared SiO 2 is 18.98 m 2 /g. The low surface area of the prepared FA_SiO 2 in this study can be attributed to the fact that we did not use templates such as CTAB, which is commonly used for synthesizing mesoporous silica.
The morphology and particle size of the FA_SiO2 particles were observed by HR-FESEM at different magnifications, as illustrated in Figure 2. The images showed a noncrystalline structure of SiO2 (Figure 2a,b), which is in good agreement with the XRD pattern of FA_SiO2. The images also revealed that the FA_SiO2 nanoparticles are almost spherical in shape and aggregated to form bigger particles (Figure 2c,d), which is similar to the observations for typical amorphous silica produced from commercial sodium silicate solution [30]. EDS analysis was carried out, as shown in Figure S1. The elemental mapping images showed the location and quantities of the main elements (i.e., Si and O) and impurities contained in the extracted SiO2 ( Figure S1b-d). Dense and uniform distribution of Si and O was observed throughout all particles, indicating that SiO2 is the major constituent and relatively small amounts of impurities (i.e., Al, Fe, and Na) were mixed with SiO2. The EDS profile also revealed that the synthesized SiO2 comprised O (54.29%), Si (32. 02%), Al (7.55%), Na (5.53%), and Fe (0.61%). It is suggested that elements such as Al and Fe dissolve to form oxyanions under alkaline conditions during the extraction of Si source from acetic acid-treated NMFA [35]. The BET analysis showed that the specific surface area of the prepared SiO2 is 18.98 m 2 /g. The low surface area of the prepared FA_SiO2 in this study can be attributed to the fact that we did not use templates such as CTAB, which is commonly used for synthesizing mesoporous silica.  Figure 3a,b show the Nyquist and Bode phase plots of the DSSCs with the nanogel and quasi-solid-state (SiO2) electrolyte, respectively. By fitting the plots with Z-view software according to an equivalent circuit, as shown in Figure 3c, the corresponding electrochemical parameters including series resistance (RS), charge transfer resistance between the counterelectrode and electrolyte interface (Rct1), charge transfer resistance between  Figure 3a,b show the Nyquist and Bode phase plots of the DSSCs with the nanogel and quasi-solid-state (SiO 2 ) electrolyte, respectively. By fitting the plots with Z-view software according to an equivalent circuit, as shown in Figure 3c, the corresponding electrochemical parameters including series resistance (R S ), charge transfer resistance between the counterelectrode and electrolyte interface (R ct1 ), charge transfer resistance between dye-sensitized TiO 2 , the electrolyte (R ct2 ), the Warburg element (Z w ), which indicates ionic diffusion in the electrolyte, minimum angular frequency (ω min ), and a lifetime of electrons for recombination (τ r ) are extracted and summarized in Table 2. The corresponding R S values of DSSCs based on nanogel and quasi-solid-state (SiO 2 ) electrolyte were 13.5 and 13.4, respectively, with no significant difference. On the other hand, a slight decrease in R ct1 and a remarkable decrease in R ct2 were observed in DSSCs based on quasi-solid-state (SiO 2 ) electrolytes compared to the control group. These Nyquist results can be attributed to the increasement in the continuous free volumes related to redox ion mobility resulting from the interaction between the highly crystalline PEG polymer chain and FA_SiO 2 nanoparticle [36]. Moreover, the middle frequencies in the Bode phase plot of nanogel and quasi-solid-state (SiO 2 ) electrolytes shifted to lower frequencies; the corresponding ω min values were 7.94 Hz for nanogel and 3.16 Hz for quasi-solid-state (SiO 2 ) electrolytes. The τ r values for DSSCs with nanogel and quasi-solid-state (SiO 2 ) electrolytes were 20.0 and 50.4 ms, respectively. These results can be explained by the fact that the presence of FA_SiO 2 nanoparticle in quasi-solid-state (SiO 2 ) electrolyte-reduced electron recombination and improved electron transfer properties. By inserting the FA_SiO 2 we obtained in the quasi-solid-state (SiO 2 ) electrolyte, the FA_SiO 2 nanoparticle can "hold" the electrolyte. This inorganic nanoparticle, which contains SiO 2 and a small amount of Al 2 O 3 , weakly attracts Li + ions to the surface due to their acidity. Further, the iodine ions accumulate around Li + to attain electrical neutrality, resulting in the effect of forming a thin double layer [37]. It is assumed that these not only act as a charge transfer pathway, but also increase Voc by preventing the recombination of electrons in the TiO 2 conduction band edge absorbed from the dye. Thus, the charge transfer resistance was reduced due to the role of the electron pathway, which is consistent with the increase in FF.    Figure 4a,b show the IPCE and diffuse reflectance spectra of DSSCs based on nanogel and quasi-solid-state (SiO 2 ) electrolytes, respectively. In general, when an inorganic nanomaterial such as SiO 2 is added to the electrolyte, the inorganic material acts to scatter incident light [38]. The same was expected in this study; however, the IPCE and reflectance spectra results did not indicate scattering effects. These results can be explained by the fact that the prepared FA_SiO 2 nanoparticle was not large enough to cause scattering in DSSCs based on quasi-solid-state (SiO 2 ) electrolytes. Moreover, this hypothesis is consistent with the nanoparticle size obtained from the previous HR-FESEM images.   Figure 4a,b show the IPCE and diffuse reflectance spectra of DSSCs based on nanogel and quasi-solid-state (SiO2) electrolytes, respectively. In general, when an inorganic nanomaterial such as SiO2 is added to the electrolyte, the inorganic material acts to scatter incident light [38]. The same was expected in this study; however, the IPCE and reflectance spectra results did not indicate scattering effects. These results can be explained by the fact that the prepared FA_SiO2 nanoparticle was not large enough to cause scattering in DSSCs based on quasi-solid-state (SiO2) electrolytes. Moreover, this hypothesis is consistent with the nanoparticle size obtained from the previous HR-FESEM images.

Photovoltaic Performance of Quasi-Solid-State (SiO 2 ) Electrolyte-Based DSSCs
The current density-voltage (J-V) characteristics were measured to investigate the effect of the quasi-solid-state (SiO 2 ) electrolyte on the photovoltaic properties of DSSCs, as shown in Figure 5, and the results are summarized in Table 3. The Jsc (12.1 mA/cm 2 ) values of the quasi-solid-state (SiO 2 ) electrolyte-based cells were slightly lower than those of the nanogel electrolyte-based cell (12.6 mA/cm 2 ). The reduced Jsc value of DSSCs based on quasi-solidstate (SiO 2 ) electrolyte compared to the control group is presumably because the silica itself absorbs moisture from the atmosphere and is in direct contact with the dye on the TiO 2 surface, causing some of the weakly attached dye to be desorbed [39]. We also observed that the Voc value of the quasi-solid-state (SiO 2 ) electrolyte-based cells (0.73 V) was much larger than that of the nanogel electrolyte-based cell (0.65 V). One possible contribution to the improved Voc value includes the reduced charge recombination, electron back reaction loss by the FA_SiO 2 in quasi-solid-state (SiO 2 ) electrolyte. In addition, the onset of the dark current shifted to a higher forward bias in the presence of the quasi-solid-state (SiO 2 ) electrolyte, compared to the control group, as shown in Figure S2. This supports well that the charge recombination reaction between the photoanode and the redox ions in the quasisolid-state (SiO 2 ) electrolyte is effectively suppressed, which gives rise to an enhancement in the Voc value. In addition, when the electrolyte was prepared with a FA_SiO 2 as the quasisolid-state materials, the FF value was further enhanced from 0.60 to 0.62. The increase in FF is due to the electron-enhanced electron pathway in DSSCs based on quasi-solid-state (SiO 2 ) electrolyte, which results in reduced charge transfer resistance [40]. Upon using FA_SiO 2 as a quasi-solid-state (SiO 2 ) electrolyte, a high energy conversion efficiency of 5.5% at 100 mW/cm 2 could be achieved. Consequently, quasi-solid-state (SiO 2 ) nanoparticles in electrolyte compensated for reduced Jsc value due to their not only enhanced electron pathway but also minimized interfacial charge recombination loss. For reliability, we provided the photocurrent density-photovoltaic curves of DSSCs of the different sets of quasi-solid-state (SiO 2 ) electrolytes ( Figure S3). In addition, the photovoltaic efficiency of the DSSCs based on FA_SiO 2 as a quasi-solid-state (SiO 2 ) electrolyte represents one of the highest values reported for quasi-solid-state electrolyte-based ssDSSCs to date, as shown in Table S2 [41][42][43][44][45]. The photovoltaic properties of DSSCs of FA_SiO 2 with different contents are shown in Figure S4, and the results are summarized in Table S3. The quasi-solid-state (SiO 2 ) 3 and 6 wt% electrolytes-based DSSCs have low redox ion mobility properties due to the small amount of FA_SiO 2 that does not allow the efficiently enhanced free volumes. Meanwhile, higher FA_SiO 2 concentration (12 wt%) in the quasi-solid-state electrolyte significantly decreases solar energy conversion efficiency due to complete solidification of the electrolyte. Moreover, optimizing our suggested quasi-solid-state electrolyte-based DSSC with functionalized scattering layers as a light-harvesting structure results in an increase in the beam path of solar irradiation within the photoanode due to scattering in the device, which we believe improves the light-harvesting efficiency of the DSSCs [46]. Therefore, the RFA-based quasi-solid-state (SiO 2 ) electrolyte was able to improve the solar energy conversion properties based on the reduced electron recombination and enhanced electron transfer properties.

Conclusions
This study presents a novel method for the preparation of FA_SiO2 from RFA for use as a quasi-solid-state electrolyte in DSSCs. The condition of the acetic acid-treated NMFA used in the synthesis controls the morphology and crystal structure of the amorphous SiO2, leading to significant differences in their physical, chemical, and electrochemical properties. Compared to the nanogel electrolyte, the quasi-solid-state (SiO2) electrolyte features reduced electron recombination and enhanced electron transfer properties. Accordingly, high solar energy conversion efficiencies of 5.5% were achieved using this electrolyte, corresponding to enhancements of 10% compared to nanogel electrolyte-based DSSCs. The RFA-based quasi-solid-state (SiO2) electrolyte can be an alternative to conventional liquid-state electrolytes, and the approach represents one of the most promising strategies for its use in low-cost solar energy conversion devices. Our experimental results suggest that energy-related solid waste, such as RFA, can be converted into energy-production materials. Additionally, this application for DSSCs fabrication can provide a novel insight that RFA-based Si products can be used to develop cost-effective and innovative active layers for Si solar cells, perovskite solar cells, and organic solar cells with improved photovoltaic performance.
Supplementary Materials: The following supporting information can be downloaded at: www.mdpi.com/xxx/s1, Figure S1: EDS analysis of the prepared FA_SiO2. Figure S2. Photocurrent density-photovoltaic curves in the dark for DSSCs based on nanogel and quasi-solid-state (SiO2) electrolytes. Figure S3. Photocurrent density-photovoltaic curves of DSSCs based quasi solid state (SiO2) electrolytes at 100 mW cm −2 from different batches. Figure S4. Photocurrent density-photovoltaic curves of DSSCs based on quasi solid state (SiO2) electrolytes with different FA_SiO2 content at 100 mW cm −2 . Table S1. DSSCs electrolyte formulations. Table S2. Comparison of photovoltaic parameters of DSSCs fabricated with quasi solid state electrolytes reported in the literature. Table  S3. Photovoltaic properties of DSSCs based on quasi solid state (SiO2) electrolytes with different FA_SiO2 contents under 1 sun illumination. (AM 1.5 G, 100 mW/cm 2 ).

Conclusions
This study presents a novel method for the preparation of FA_SiO 2 from RFA for use as a quasi-solid-state electrolyte in DSSCs. The condition of the acetic acid-treated NMFA used in the synthesis controls the morphology and crystal structure of the amorphous SiO 2 , leading to significant differences in their physical, chemical, and electrochemical properties. Compared to the nanogel electrolyte, the quasi-solid-state (SiO 2 ) electrolyte features reduced electron recombination and enhanced electron transfer properties. Accordingly, high solar energy conversion efficiencies of 5.5% were achieved using this electrolyte, corresponding to enhancements of 10% compared to nanogel electrolyte-based DSSCs. The RFA-based quasi-solid-state (SiO 2 ) electrolyte can be an alternative to conventional liquid-state electrolytes, and the approach represents one of the most promising strategies for its use in low-cost solar energy conversion devices. Our experimental results suggest that energy-related solid waste, such as RFA, can be converted into energy-production materials. Additionally, this application for DSSCs fabrication can provide a novel insight that RFA-based Si products can be used to develop cost-effective and innovative active layers for Si solar cells, perovskite solar cells, and organic solar cells with improved photovoltaic performance.