Optical and Structural Analysis of TiO2–SiO2 Nanocomposite Thin Films Fabricated via Pulsed Laser Deposition Technique

TiO2–SiO2 nanocomposite thin films have gained the attention of the scientific community due to their unique physical and chemical properties. In this paper, we report on the fabrication and characterization of a TiO2–SiO2 nanocomposite disk-shaped target. The target was used for the deposition of TiO2–SiO2 nanocomposite thin films on fluorine-doped tin oxide/glass substrates using the pulsed laser deposition (PLD) technique. The thicknesses of the thin films were fixed to 100 nm, and the deposition temperature ranged from room temperature to 300 °C. As revealed by the microstructural and morphological characterizations revealed, the TiO2–SiO2 nanocomposite thin films are amorphous and display homogeneous distribution. The determined values of the indirect optical band gap range from 2.92 to 3.07 eV, while those of the direct optical band gap lie between 3.50 and 3.55 eV. Additionally, as the deposition temperature decreases, the light transmission increases in the visible and in the ultraviolet ranges, which is suitable for flexible perovskite solar cells. This research can uncover new insights into the fabrication of amorphous TiO2–SiO2-based nanostructured thin films using the PLD technique for perovskite solar cell technology.


Introduction
Titanium dioxide (TiO 2 ) and silicon dioxide (SiO 2 ) are semiconductor materials that are widely studied as thin films due to their unique properties. On one hand, TiO 2 has a wide bandgap of 3.2 eV in its anatase phase and 3.0 eV in its rutile phase [1,2], a high refractive index [3], and excellent photocatalytic activity, making it a good choice for optical applications, especially solar cells [4]. Amorphous TiO 2 thin films can have smooth surface morphologies and optical properties similar to crystalline anatase TiO 2 owing to their similar electronic structures [2]. On the other hand, SiO 2 exhibits exceptional mechanical properties and excellent chemical and thermal stabilities, making it ideal for applications that require high durability and reliability [5,6]. Moreover, SiO 2 is used as a dielectric material in microelectronic circuits. Several techniques have been used to deposit TiO 2 and SiO 2 thin films, including chemical vapor deposition (CVD) [7,8], molecular beam epitaxy [9,10], plasma-enhanced chemical vapor deposition [11,12], the sol-gel process [13,14], and pulsed laser deposition (PLD) [15,16], etc. PLD is a physical vapor deposition technique that uses high-energy laser pulses to ablate the target's material to obtain, via vapor condensation on a substrate, thin films with excellent structural and optical properties. This technique is powerful and versatile, allowing for the precise control of the thin film's thickness, stoichiometry, and composition, making it an excellent method for the synthesis of complex structures and composites [17][18][19].
The TiO 2 -SiO 2 nanocomposite thin films display better characteristics when compared to individual TiO 2 and SiO 2 materials. In fact, the combination of TiO 2 and SiO 2 results in enhanced mechanical, thermal, and optical properties [20]. TiO 2 -SiO 2 nanocomposite films exhibit enhanced performance in terms of charge transport and stability, making them particularly suitable for electron transport layers (ETLs) in perovskite solar cells (PSCs) [21,22]. The design and development of TiO 2 -SiO 2 nanocomposite thin films is a very promising research topic that could lead to development of more efficient and stable PSCs. In addition, TiO 2 -SiO 2 amorphous films cover a wide range of possible refractive indices, and they exhibit a high dielectric constant and a low leakage current [23]. For instance, a study by Zhao et al. [24] reported the synthesis of TiO 2 -SiO 2 hybrid films with a tunable refractive index using the sol-gel technique. Another study by Mitronika et al. [25] investigated the effect of SiO 2 content on the optical and electrical properties of TiO 2 -SiO 2 nanocomposite thin films in which they showed that the best compromise results in terms of dielectric permittivity improvement, charge injection, and transport behavior were obtained in the case of a Ti 0.33 Si 0.66 O 2 nanocomposite. Wang et al. [26] reported that a value of x = 0.5 in the Ti x Si 1-x O 2 nanocomposite results in the highest average transmittance. However, there are very few studies that have demonstrated the successful fabrication of TiO 2 -SiO 2 composite thin films using pulsed laser deposition [27], and there are still some limitations that must be addressed, such as the optimization of the parameters and deposition conditions, as well as the identification of the best composition and structure for TiO 2 -SiO 2 nanocomposite thin films.
In this paper, we report the fabrication of a TiO 2 -SiO 2 nanocomposite target and investigate its morphological and microstructural properties. Raman spectroscopy and X-ray diffraction (XRD) analyses confirmed the presence of two phases, anatase (TiO 2 ) and quartz (SiO 2 ), in the target. We used the PLD technique to develop TiO 2 -SiO 2 nanocomposite thin films. The microstructural characterization of the nanocomposite thin films deposited on a fluorine-doped tin oxide (FTO)/glass substrate showed that the FTO grains were overlaid by 100 nm thick nanocomposite thin films. An analysis of their optical properties revealed that the nanocomposite nanofilms exhibit indirect optical band gaps of 3.00 eV, 3.06, 3.07, and 2.92 eV for thin films deposited at 25 • C, 200 • C, 250 • C, and 300 • C, respectively. The direct optical band gaps were found to be equal to 3.50 eV, 3.53, 3.55, and 3.51 eV for thin films deposited at 25 • C, 200 • C, 250 • C, and 300 • C, respectively. The purpose of this research is to investigate the properties of TiO 2 -SiO 2 nanocomposite thin films for perovskite solar cell applications. The findings of this study will contribute to the development of TiO 2 -SiO 2 nanocomposite thin films for the next generation of optoelectronics, photonics, and photovoltaics.

Target Preparation
The oxide powders TiO 2 (BIOCHEM Chemopharma, Cosne-Cours-sur-Loire, France; product code: 320150500) and SiO 2 (Kojundo Chemical Laboratory Co., Ltd., Tokyo, Japan; SiO 2 quartz), were mixed at a 2.2 weight ratio of TiO 2 to SiO 2 and dried at 100 • C. Then, Nanomaterials 2023, 13, 1632 3 of 12 the mixture was ground in an agate mortar and pressed into a disk shape with a 13 mm diameter and a thickness of 3 mm. The target was sintered at temperature of 800 • C for 4 h with a ramp rate of 10 • C/min.

Substrate Preparation
FTO/glass substrates (10 × 10 × 3.1 mm 3 ; sheet resistance:~7 Ω/sq) were used in this study. The thickness of the FTO layer was 600 nm. The substrates were cleaned successively in ethyl alcohol, acetone, and deionized water for 10 min each. Finally, the substrates were dried with air at room temperature.

Deposition Parameters
TiO 2 -SiO 2 nanocomposite thin films were deposited on an FTO/glass substrate using the PLD method. An Nd:YAG laser with a 2nd harmonic and a wavelength of 532 nm was used, and the pulse duration was fixed at 10 ns with a repetition rate of 10 Hz; the pulse energy was 50 mJ/pulse, and the spot size was approximately 2.5 mm 2 . The laser fluence and deposition pressure were set to 2.0 J/cm 2 and 50 mTorr, respectively. The target-to-substrate distance was fixed at 50 mm, and 10 min was chosen as the deposition time. Finally, four deposition temperatures were chosen: 25 • C, 200 • C, 250 • C, and 300 • C.

Thin Film Characterizations
The thicknesses of the as-deposited TiO 2 -SiO 2 nanocomposite thin films were determined to be 100 nm in all samples through the use of a Dektak XT stylus profilometer (Bruker, Paris, France). Morphological characterizations of the target and the films were performed using a scanning electron microscope (SEM) (Quanta 450, FEI, Thermo Fisher Scientific, Hillsboro, OR, USA) coupled with an energy dispersive X-ray detector (EDS) (EDAX, AMETEK Inc., Berwyn, PA, USA). The EDS analysis was performed using the TEAM version V4.1 system (EDAX Inc.); calibration was carried out using a standard AlCu sample (Cu foil on an Al grid). In map analysis mode, an average number of 50,000 frames was used with a dwell of 200 ms. The XRD patterns with 2θ ranged from 20 to 80 • and were obtained using a Shimadzu LabX XRD-6000 diffractometer (Shimadzu, Kyoto, Japan) with CuKα radiation (λ = 1.54 Å). Raman spectroscopy measurements were performed using an InVia confocal Raman Microscope (Renishaw, Wotton-under-Edge, UK). We used the open-source software Image J, version 1.53t, for the particle size distribution determination from the SEM micrographs of the target FTO/glass substrate and the TiO 2 -SiO 2 nanocomposite thin films. Finally, an Avantes UV-vis spectrometer (AvaSpec 2048, Schiphol, The Netherlands) was used for the optical characterizations. The optical bandgaps (E g ) of the nanocomposite thin films were determined from the absorption spectra via Tauc plots. Figure 1a presents an SEM image of the fabricated target, obtained at an acceleration voltage of 20 kV; the scale of the image is 1µm. As can be seen from the image, the nanoparticles were homogeneously dispersed, and the TiO 2 and SiO 2 phases cannot be distinguished. The EDX analysis of the sintered TiO 2 -SiO 2 nanocomposite target is represented in Figure 1b (1) was carried out on the sintered TiO2-SiO2 nanocomposite target after it was used for the deposition of the thin film, and we found that carbon was present as an impurity even after cleaning the target surface, as can be seen in the inset of Figure 1b. The average particle size in the target was determined from the SEM images to be 132 nm, as shown in Figure 1c. The relatively large size of the nanoparticles can be attributed to the limitations of the mechanical grinding method used for target preparation. The Raman spectra of the sintered TiO2-SiO2 nanocomposite target are presented in Figure 2a. The target exhibits peaks at 142.2, 195.9, 395.1, 513.6, and 637.5 cm -1 which belong to the TiO2 in its anatase form [28,29]. The peaks correspond to the Eg, Eg, B1g, A1g, and Eg modes, respectively. It should be noted that the peaks corresponding to the rutile TiO2 are absent. The XRD diagram of the target is shown in Figure 2b. It reveals that the diffraction peaks correlate well with anatase TiO2 according to Anatase-TiO2-PDF 98-002-4276, tetragonal, and with quartz SiO2 according to Quartz low-SiO2-PDF 98-006-2406, hexagonal. High-purity TiO2 anatase phase is confirmed, and there was a good agreement between the Raman spectroscopy and XRD results. However, the presence of SiO2 quartz in the target was detected only from the analysis of the XRD pattern. The absence of a Raman shift corresponding to SiO2 may have been caused by the low Raman signal of SiO2 nanoparticles. According to Equation (1), x was determined to be approximately 0.72; therefore, our nanocomposite had the following composition: Ti 0.72 Si 0.28 O y . We note that the EDX analysis was carried out on the sintered TiO 2 -SiO 2 nanocomposite target after it was used for the deposition of the thin film, and we found that carbon was present as an impurity even after cleaning the target surface, as can be seen in the inset of Figure 1b. The average particle size in the target was determined from the SEM images to be 132 nm, as shown in Figure 1c. The relatively large size of the nanoparticles can be attributed to the limitations of the mechanical grinding method used for target preparation.

Nanocomposite Target Properties
The Raman spectra of the sintered TiO 2 -SiO 2 nanocomposite target are presented in Figure 2a. The target exhibits peaks at 142.2, 195.9, 395.1, 513.6, and 637.5 cm −1 which belong to the TiO 2 in its anatase form [28,29]. The peaks correspond to the E g , E g , B 1g , A 1g , and E g modes, respectively. It should be noted that the peaks corresponding to the rutile TiO 2 are absent. The XRD diagram of the target is shown in Figure 2b. It reveals that the diffraction peaks correlate well with anatase TiO 2 according to Anatase-TiO 2 -PDF 98-002-4276, tetragonal, and with quartz SiO 2 according to Quartz low-SiO 2 -PDF 98-006-2406, hexagonal. High-purity TiO 2 anatase phase is confirmed, and there was a good agreement between the Raman spectroscopy and XRD results. However, the presence of SiO 2 quartz in the target was detected only from the analysis of the XRD pattern. The absence of a Raman shift corresponding to SiO 2 may have been caused by the low Raman signal of SiO 2 nanoparticles.

SEM Morphological Analysis
The SEM images of the FTO/glass substrate and the nanocomposite thin films ited on FTO/glass substrates at different temperatures are shown in Figure 3. As seen in Figure 3a, the FTO displays irregularly shaped grains. After the depositio thin film, the FTO grains remained visually recognizable; however, they transition sharp and angular shapes into smoother and not-sharp shapes, as can be seen in 3b-e, confirming that the FTO grains were overlaid by the nanocomposite thin film ilar behavior was reported in the work of Z. Jiang et al. [30] in which the surface m ogy of an FTO substrate changed from a pyramidal morphology to a non-stereo morphology after the deposition of TiO2 thin films via magnetron sputtering. Su e reported the overlaying of FTO irregular grains with TiO2 nanohole array thin fi tained via the electrodeposition technique. A high degree of homogeneity of the sition was confirmed by the absence of a clear distinction between the TiO2 and S noparticles.

SEM Morphological Analysis
The SEM images of the FTO/glass substrate and the nanocomposite thin films deposited on FTO/glass substrates at different temperatures are shown in Figure 3. As can be seen in Figure 3a, the FTO displays irregularly shaped grains. After the deposition of the thin film, the FTO grains remained visually recognizable; however, they transitioned from sharp and angular shapes into smoother and not-sharp shapes, as can be seen in Figure 3b-e, confirming that the FTO grains were overlaid by the nanocomposite thin films. Similar behavior was reported in the work of Z. Jiang et al. [30] in which the surface morphology of an FTO substrate changed from a pyramidal morphology to a non-stereotypical morphology after the deposition of TiO 2 thin films via magnetron sputtering. Su et al. [31] reported the overlaying of FTO irregular grains with TiO 2 nanohole array thin films obtained via the electrodeposition technique. A high degree of homogeneity of the composition was confirmed by the absence of a clear distinction between the TiO 2 and SiO 2 nanoparticles.
The size distribution of the nanoparticles was determined from the SEM micrographs by using particle size histograms, as shown in Figure 4. The average size of the nanoparticles in the FTO/glass substrate was determined to be 237 nm. After the deposition of the nanocomposite thin films, the as-determined nanoparticle sizes were found to be 258, 234, 242, and 247 nm for the thin films deposited at 25 • C, 200 • C, 250 • C, and 300 • C, respectively. We should note that the measured nanoparticle diameters in Figure 4b-e correspond to the FTO grains covered by a thin layer of TiO 2 -SiO 2 , and the increase in diameter after deposition indicates the overlaying of FTO grains. ilar behavior was reported in the work of Z. Jiang et al. [30] in which the surface morphology of an FTO substrate changed from a pyramidal morphology to a non-stereotypical morphology after the deposition of TiO2 thin films via magnetron sputtering. Su et al. [31] reported the overlaying of FTO irregular grains with TiO2 nanohole array thin films obtained via the electrodeposition technique. A high degree of homogeneity of the composition was confirmed by the absence of a clear distinction between the TiO2 and SiO2 nanoparticles. The size distribution of the nanoparticles was determined from the SEM micrographs by using particle size histograms, as shown in Figure 4. The average size of the   Figure 5 shows the EDX spectra of the nanocomposite thin films. As can be seen from the figure, oxygen, silicon, titanium, and tin (originating from the TiO2-SiO2 thin film/FTO/glass substrate) are the main elements. In addition, carbon was detected in all samples as well as in the sintered target (Figure 1b), originating from the oil contamination of the PLD vacuum system [32], while nitrogen was found as trace. We should note that we could not deduce the structural composition of the thin films from the EDX results and by using Equation (1) because the silicon atomic percentage measured was present in the thin films as well as in the glass substrates. The atomic percentage of tin was approximately the same in all samples, however, the titanium atomic percentage was different, and it depended on the deposition temperature.  Figure 5 shows the EDX spectra of the nanocomposite thin films. As can be seen from the figure, oxygen, silicon, titanium, and tin (originating from the TiO 2 -SiO 2 thin film/FTO/glass substrate) are the main elements. In addition, carbon was detected in all samples as well as in the sintered target (Figure 1b), originating from the oil contamination of the PLD vacuum system [32], while nitrogen was found as trace. We should note that we could not deduce the structural composition of the thin films from the EDX results and by using Equation (1) because the silicon atomic percentage measured was present in the thin films as well as in the glass substrates. The atomic percentage of tin was approximately the same in all samples, however, the titanium atomic percentage was different, and it depended on the deposition temperature.

Energy Dispersive X-ray Analysis
We conducted EDX mapping in order to determine the elements' distribution within the surfaces of the nanocomposite thin films deposited at 25 • C (Figure 6a

Raman Spectroscopy
Raman spectra of the PLD-deposited nanocomposite thin films are shown in Figure  7. The first observation is that all the peaks detected in the Raman spectra in the sintered TiO2-SiO2 nanocomposite target (Figure 2a) were absent in the TiO2-SiO2 nanocomposite films. Raman spectra corresponding to the FTO/glass substrate are shown in the inset of

Raman Spectroscopy
Raman spectra of the PLD-deposited nanocomposite thin films are shown in Figure  7. The first observation is that all the peaks detected in the Raman spectra in the sintered TiO2-SiO2 nanocomposite target (Figure 2a) were absent in the TiO2-SiO2 nanocomposite films. Raman spectra corresponding to the FTO/glass substrate are shown in the inset of Figure 7a. The substrate exhibits peaks at 472.6, 551.8, 786.7, and 1094.6 cm -1 . The peak at 472.6 cm -1 can be attributed to the Eg mode in the FTO, which is related to the oxygen

Raman Spectroscopy
Raman spectra of the PLD-deposited nanocomposite thin films are shown in Figure 7. The first observation is that all the peaks detected in the Raman spectra in the sintered TiO 2 -SiO 2 nanocomposite target (Figure 2a) were absent in the TiO 2 -SiO 2 nanocomposite films. Raman spectra corresponding to the FTO/glass substrate are shown in the inset of Figure 7a. The substrate exhibits peaks at 472.6, 551.8, 786.7, and 1094.6 cm −1 . The peak at 472.6 cm −1 can be attributed to the E g mode in the FTO, which is related to the oxygen vibration in the oxygen plane [33,34]. The peak around 551 cm −1 may be related to the small size effect of the nanoparticles in FTO thin films [34]. Moreover, the peak located at 787 cm −1 can be attributed to B 2g s, which is related to the expansion and contraction of Sn-O bonds. Finally, the peak at 1094.6 cm −1 can be attributed to the glass substrate [35]. As can be seen in Figure 7a-d, all samples display the same peaks as the substrate, thus indicating that the deposited thin films of TiO 2 -SiO 2 possess an amorphous structure.
7. The first observation is that all the peaks detected in the Raman spectra in the sintered TiO2-SiO2 nanocomposite target (Figure 2a) were absent in the TiO2-SiO2 nanocomposite films. Raman spectra corresponding to the FTO/glass substrate are shown in the inset of Figure 7a. The substrate exhibits peaks at 472.6, 551.8, 786.7, and 1094.6 cm -1 . The peak at 472.6 cm -1 can be attributed to the Eg mode in the FTO, which is related to the oxygen vibration in the oxygen plane [33,34]. The peak around 551 cm -1 may be related to the small size effect of the nanoparticles in FTO thin films [34]. Moreover, the peak located at 787 cm -1 can be attributed to B2gs, which is related to the expansion and contraction of Sn-O bonds. Finally, the peak at 1094.6 cm -1 can be attributed to the glass substrate [35]. As can be seen in Figure 7a-d, all samples display the same peaks as the substrate, thus indicating that the deposited thin films of TiO2-SiO2 possess an amorphous structure.

XRD Characterization
We carried out an XRD analysis to determine whether any TiO2 and SiO2 phases had formed in the nanocomposite thin films deposited by PLD. The corresponding recorded XRD patterns are presented in Figure 8. It can be easily observed that all diffractograms reveal a tetragonal SnO2 structure related to the FTO/glass substrate, which is in good agreement with JCPDS card SnO2-PDF 98-015-4960 [36]. The crystalline structures of TiO2 and SiO2 could not be assessed from the XRD patterns, likely due to the very thin layer of the nanocomposite and/or due to its amorphous structure. The assumption that the TiO2-SiO2 nanocomposite nanofilms exhibit an amorphous structure further supports the results revealed by the Raman analysis [ Figure 7].

XRD Characterization
We carried out an XRD analysis to determine whether any TiO 2 and SiO 2 phases had formed in the nanocomposite thin films deposited by PLD. The corresponding recorded XRD patterns are presented in Figure 8. It can be easily observed that all diffractograms reveal a tetragonal SnO 2 structure related to the FTO/glass substrate, which is in good agreement with JCPDS card SnO 2 -PDF 98-015-4960 [36]. The crystalline structures of TiO 2 and SiO 2 could not be assessed from the XRD patterns, likely due to the very thin layer of the nanocomposite and/or due to its amorphous structure. The assumption that the TiO 2 -SiO 2 nanocomposite nanofilms exhibit an amorphous structure further supports the results revealed by the Raman analysis [ Figure 7].  Figure 9a shows the spectral dependence of transmittance (T) in the four samples. As can be seen from the figure, the transmittance decreases in the ultraviolet and the visible ranges as the PLD deposition temperature increases from 25 to 300 °C. The optical absorption coefficient (α) was determined using Equation (2), with the assumption that the reflection in all samples was negligeable:

Optical Characterization
In the above equation, d represents the thin film thickness. The light absorption was significantly enhanced in the visible region as the PLD deposition temperature increased, as can be seen in Figure 9b, which could be due to the formation of band tail states in the forbidden band gap as the deposition temperature increased.
The absorption coefficient is related to the photon energy (ℎ ) and the optical band gap energy ( ) of the nanocomposite thin films, according to the following equation: where h is the Planck constant, is the light frequency, and A represents a constant that depends on the transition nature indicated by the value of m. Equation (3) can be simplified as follows: The Tauc exponent m can have a value of 0.5 for the direct optical bandgap or a value of 2 for an indirect optical band gap [37]. Thus, we drew the graphs ( ℎ ) 1/2 and ( ℎ ) 2 as functions of the photon energy, as shown in Figure 9c,d, respectively. Both the (ℎ ) = ( ℎ ) 1/2 and (ℎ ) = ( ℎ ) 2 plots showed linear dependence as a function of the incidence photon energy in the UV region. The energies of the direct and indirect possible transitions were determined by extrapolating the linear parts of the previously mentioned curves. The indirect optical band gap energies were calculated and found to be Eg = 3.00, 3.06, 3.07, and 2.92 eV for thin films deposited at 25 °C, 200 °C, 250 °C, and 300 °C, respectively. The obtained band gap energies are close to those reported in crystalline TiO2 [38]. Additionally, the direct optical band gap energies were estimated to be Eg = 3.50, 3.53, 3.55, and 3.51 eV for thin films deposited at 25 °C, 200 °C, 250 °C, and 300 °C, respectively. These match with the values of the direct energy band gaps in TiO2-SiO2 nanocomposite thin films reported by Huong et al. [39].  Figure 9a shows the spectral dependence of transmittance (T) in the four samples. As can be seen from the figure, the transmittance decreases in the ultraviolet and the visible ranges as the PLD deposition temperature increases from 25 to 300 • C. The optical absorption coefficient (α) was determined using Equation (2), with the assumption that the reflection in all samples was negligeable:

Conclusions
A highly nanostructured TiO2-SiO2 nanocomposite disk-shaped target was fabricated which was comprised of nanoparticles with an average size of 132 nm. TiO2-SiO2 nanocomposite thin films were deposited successfully on FTO/glass substrates using the PLD technique at different deposition temperatures. The microstructural characterization of the thin films revealed the amorphous structure and highly homogeneous distribution of the nanocomposites within the surfaces. The thin films under study exhibited indirect optical band gap energies ranging from 2.92 to 3.07 eV, while their direct optical band gap energies lay between 3.50 and 3.55 eV. The nanocomposite thin film deposited at 25 °C In the above equation, d represents the thin film thickness. The light absorption was significantly enhanced in the visible region as the PLD deposition temperature increased, as can be seen in Figure 9b, which could be due to the formation of band tail states in the forbidden band gap as the deposition temperature increased.
The absorption coefficient is related to the photon energy (hν) and the optical band gap energy (E g ) of the nanocomposite thin films, according to the following equation: where h is the Planck constant, ν is the light frequency, and A represents a constant that depends on the transition nature indicated by the value of m. Equation (3) can be simplified as follows: The Tauc exponent m can have a value of 0.5 for the direct optical bandgap or a value of 2 for an indirect optical band gap [37]. Thus, we drew the graphs (αhν) 1/2 and (αhν) 2 as functions of the photon energy, as shown in Figure 9c,d, respectively. Both the f (hν) = (αhν) 1/2 and f (hν) = (αhν) 2 plots showed linear dependence as a function of the incidence photon energy in the UV region. The energies of the direct and indirect possible transitions were determined by extrapolating the linear parts of the previously mentioned curves. The indirect optical band gap energies were calculated and found to be Eg = 3.00, 3.06, 3.07, and 2.92 eV for thin films deposited at 25 • C, 200 • C, 250 • C, and 300 • C, respectively. The obtained band gap energies are close to those reported in crystalline TiO 2 [38]. Additionally, the direct optical band gap energies were estimated to be Eg = 3.50, 3.53, 3.55, and 3.51 eV for thin films deposited at 25 • C, 200 • C, 250 • C, and 300 • C, respectively. These match with the values of the direct energy band gaps in TiO 2 -SiO 2 nanocomposite thin films reported by Huong et al. [39].

Conclusions
A highly nanostructured TiO 2 -SiO 2 nanocomposite disk-shaped target was fabricated which was comprised of nanoparticles with an average size of 132 nm. TiO 2 -SiO 2 nanocomposite thin films were deposited successfully on FTO/glass substrates using the PLD technique at different deposition temperatures. The microstructural characterization of the thin films revealed the amorphous structure and highly homogeneous distribution of the nanocomposites within the surfaces. The thin films under study exhibited indirect optical band gap energies ranging from 2.92 to 3.07 eV, while their direct optical band gap energies lay between 3.50 and 3.55 eV. The nanocomposite thin film deposited at 25 • C displayed the best optical performance in terms of transmittance in the visible range, which is very suitable for application as an electron transport layer for low-temperature and flexible perovskite solar cells. This research aims to uncover new insights into the deposition of amorphous TiO 2 -SiO 2 nanocomposite thin films using the PLD technique for perovskite solar cell technology applications. As a future research objective, we intend to investigate the electrical and transport properties of the TiO 2 -SiO 2 nanocomposite thin films.

Conflicts of Interest:
The authors declare no conflict of interest.