Manipulating the Structure and Characterization of Sr1−xLaxTiO3 Nanocubes toward the Photodegradation of 2-Naphthol under Artificial Solar Light

Effective La-doped SrTiO3 (Sr1−xLaxTiO3, x = 0–0.1 mol.% La-doped) nanocubes were successfully synthesized by a hydrothermal method. The influence of different La dopant concentrations on the physicochemical properties of the host structure of SrTiO3 was fully characterized. X-ray photoelectron spectroscopy (XPS) and X-ray diffraction (XRD) revealed that the Sr2+ in the crystal lattice of SrTiO3 was substituted by La3+. As a result, the absorption region of the Sr1−xLaxTiO3 could be extended to visible light. Scanning electron microscopy (SEM) images confirmed that their morphologies are associated with an increased surface area and an increased La-doping concentration. The decrease in the photoluminescence (PL) intensity of the dopant samples showed more defect levels created by the dopant La+3 cations in the SrTiO3 structure. The photocatalytic activities of Sr1−xLaxTiO3 were evaluated with regard to the degradation of 2-naphthol at typical conditions under artificial solar light. Among the candidates, Sr0.95La0.05TiO3 exhibited the highest photocatalytic performance for the degradation of 2-naphthol, which reached 92% degradation efficiency, corresponding to a 0.0196 min−1 degradation rate constant, within 180 minutes of irradiation. Manipulating the structure of Sr1−xLaxTiO3 nanocubes could produce a more effective and stable degradation efficiency than their parent compound, SrTiO3. The parameters remarkably influence the Sr1−xLaxTiO3 nanocubes’ structure, and their degradation efficiencies were also studied. Undoubtedly, substantial breakthroughs of Sr1−xLaxTiO3 nanocube photocatalysts toward the treatment of organic contaminants from industrial wastewater are expected shortly.


Introduction
To date, 2-naphthol, or β-naphthol, is one of the most important industrial chemicals, and it is used extensively in dyestuff manufacturing, pharmaceutical production, and some biogeochemical processes [1]. This compound is preserved in industrial wastewater and is quite slowly and incompletely biodegradable, which may have a negative effect The powder X-ray diffraction patterns of SrTiO 3 samples at different heating durations (12, 24, 48, and 72 h)   . The obtained results reveal that a cubic phase of SrTiO 3 could be synthesized by a hydrothermal method at 130 • C. As shown in Figure 1, as the hydrothermal duration increases, the intensities of the corresponding samples also increase, implying an increase in the rate of crystallization. This phenomenon could be attributed to the Ostwald ripening process, which is due to smaller particles being less stable, and the growth of larger particles being energetically favourable [59].
Catalysts 2021, 11,564 3 of 20 application of Sr1−xLaxTiO3 nanocubes for the degradation of 2-naphthol has been reported. Thus, it is useful to explore how Sr1−xLaxTiO3 materials technologically enhance environmental remediation. Furthermore, the reusability of photocatalysts has been investigated in terms of the stability of photoactivity and X-ray diffraction. Sr1−xLaxTiO3 exhibited promising photocatalytic performance for the visible-light-driven degradation of 2-naphthol.

The Influence of Heating Durations
The powder X-ray diffraction patterns of SrTiO3 samples at different heating durations (12, 24, 48, and 72 h)   . The obtained results reveal that a cubic phase of SrTiO3 could be synthesized by a hydrothermal method at 130 °C. As shown in Figure 1, as the hydrothermal duration increases, the intensities of the corresponding samples also increase, implying an increase in the rate of crystallization. This phenomenon could be attributed to the Ostwald ripening process, which is due to smaller particles being less stable, and the growth of larger particles being energetically favourable [59].  Table  1, implies a high sample crystallinity. The calculated average crystal sizes of the SrTiO3 samples suggest that the crystallinity of SrTiO3 increases with an increasing hydrothermal duration.  The crystal sizes of SrTiO 3 NPs synthesized at various hydrothermal durations were calculated using the Scherrer formula, D (100) = K B cos , according to the full width at half maximum (FWHM) of the (110) crystal plane. A small value of FWHM, as shown in Table 1, implies a high sample crystallinity. The calculated average crystal sizes of the SrTiO 3 samples suggest that the crystallinity of SrTiO 3 increases with an increasing hydrothermal duration. The specific surface area was measured using the Brunauer-Emmett-Teller (BET) method, as presented in Table 1. The specific surface area decreases with an increasing hydrothermal duration from 12 h to 48 h. This result suggests that the increase in the hydrothermal duration fosters the tendency of agglomeration. Moreover, the specific surface area of all of the SrTiO 3 synthesized in this research by the hydrothermal method is higher than that of samples synthesized by the solid-state reaction (i.e., 1.6 m 2 /g) [60,61] or even the sol-gel hydrothermal procedure (i.e., 17.1 m 2 /g) [62], which are appropriate hydrothermal methods for the preparation of SrTiO 3 for photocatalytic applications.  [63]. However, the relatively low-intensity peaks of La-doped samples observed at 27.74 • , 36.56 • and 44.12 • are due to the formation of TiO 2 (JCPDS files 21-1272 and 21-1276). The reduced intensity of the Sr 0.9 La 0.1 TiO 3 (x = 0.1) sample is also recognized, which may be due to the formation of a higher concentration of impurity phases. The specific surface area was measured using the Brunauer-Emmett-Teller (BET) method, as presented in Table 1. The specific surface area decreases with an increasing hydrothermal duration from 12 h to 48 h. This result suggests that the increase in the hydrothermal duration fosters the tendency of agglomeration. Moreover, the specific surface area of all of the SrTiO3 synthesized in this research by the hydrothermal method is higher than that of samples synthesized by the solid-state reaction (i.e., 1.6 m 2 /g) [60,61] or even the sol-gel hydrothermal procedure (i.e., 17.1 m 2 /g) [62], which are appropriate hydrothermal methods for the preparation of SrTiO3 for photocatalytic applications. Figure 2 shows the XRD diffraction pattern of La-doped SrTiO3 (Sr1−xLaxTiO3) samples with different La-dopant concentrations synthesized at 130 °C for 48 h. We found that the diffraction peaks of the samples (at 22.84, 32.0, 40.0, 46.5, 57.5, 68.0, and 77.0°) are indexed well to the cubic lattice of perovskite SrTiO3 (JCPDS 35-0734), suggesting that the crystal structure of SrTiO3 does not influence the substitution of La [63]. However, the relatively low-intensity peaks of La-doped samples observed at 27.74°, 36.56° and 44.12° are due to the formation of TiO2 (JCPDS files 21-1272 and 21-1276). The reduced intensity of the Sr0.9La0.1TiO3 (x = 0.1) sample is also recognized, which may be due to the formation of a higher concentration of impurity phases. The estimated average crystal sizes of the Sr1−xLaxTiO3 (x = 0, 0.03, 0.05, 0.1) samples were calculated based on the Scherrer formula and tabulated in Table 2. The obtained results show that the crystal size of Sr1−xLaxTiO3 is smaller than that of their parent SrTiO3 crystals, confirming that La doping can inhibit the growth of SrTiO3 crystals. Moreover, at high La doping concentrations (x = 0.1), the intensity of the sample was significantly reduced, which was associated with an increasing amount of impurity, providing an unnecessary amount of impurity, which can cause some adverse effects. Besides this, with an increasing La doping amount, the (100) diffraction peak shifts to a higher 2θ value, and the crystallinity decreases. These results indicate that crystals with a high doping concentration are distorted and contain an internal strain, or maybe the different valences of La 3+ and Sr 2+ ions, which can cause lattice defects in SrTiO3 when La 3+ is substituted for Sr 2+ [64].  Table 2. The obtained results show that the crystal size of Sr 1−x La x TiO 3 is smaller than that of their parent SrTiO 3 crystals, confirming that La doping can inhibit the growth of SrTiO 3 crystals. Moreover, at high La doping concentrations (x = 0.1), the intensity of the sample was significantly reduced, which was associated with an increasing amount of impurity, providing an unnecessary amount of impurity, which can cause some adverse effects. Besides this, with an increasing La doping amount, the (100) diffraction peak shifts to a higher 2θ value, and the crystallinity decreases. These results indicate that crystals with a high doping concentration are distorted and contain an internal strain, or maybe the different valences of La 3+ and Sr 2+ ions, which can cause lattice defects in SrTiO 3 when La 3+ is substituted for Sr 2+ [64]. The lattice parameter of Sr 1−x La x TiO 3 as a function of the dopant concentration was calculated from the powder data using the program UnITCell [65]; the results are presented in Table 2. The calculated unit-cell parameter of SrTiO 3 -48 is 3.988 Å, which is slightly higher than that of JCPDS-card no. 35-0734 (3.905 Å). The calculated values of lattice parameter (a = b = c) are 3.988 Å (x = 0), 3.984 Å (x = 0.03), 3.982 Å (x = 0.05), and 3.983 Å (x = 0.1). The lattice parameter continuously decreases with an increasing dopant concentration (from x = 0 to x = 0.05), which can be explained by the replacement of the larger-sized Sr 2+ ions (118 pm) in the A-sites of the perovskite structure with smaller La 3+ ions (103.2 pm) [49].

The Influence of La Doping Concentrations
As shown in Table 2, the surface area was found to increase from 21.7-39.8 m 2 /g as the La content increases in Sr 1−x La x TiO 3 , which is due to the decrease in particle size. These results imply that La is substituted into the SrTiO 3 structure. The porous structure of Sr 1−x La x TiO 3 was explored by nitrogen adsorption-desorption isotherms, as shown in Figure 3a, where all of the samples show type IV adsorption isotherms. The adsorption isotherm in a relative pressure range of 0 < P/P 0 < 0.8 indicates a low affinity for the nitrogen adsorbate and an intrinsically low specific surface area, implying that the sample also possesses some large macropores. The adsorption isotherms of the samples have a vertical rise at a high relative pressure P/P 0 > 0.9), with a type H3 hysteresis loop, thus supporting the presence of micropores in the catalysts [66]. The corresponding pore size is shown in Table 2, which was found in the range 2.38-2.46 nm, revealing that the Sr 1−x La x TiO 3 nanocubes possess mesopores. The value of the pore radius varies slightly, which is associated with a slight increase in the specific surface area.
The light-harvesting ability of Sr 1−x La x TiO 3 photocatalysts was determined from their UV-visible absorption spectra, as shown in Figure 3b. The Kubelka-Munk function was used to calculate the bandgap energy of different photocatalysts by plotting [F(R)-hν] 1/2 with the energy of light (hν) (Figure 3c). The E g values were estimated from the x-axis intercept obtained by the linear fit of the spectra shown in Figure 3c. In general, a progressive redshift of the absorption edge in the visible region is observed with an increasing La doping concentration. In other words, the La doping concentration accordingly affected the bandgap energy of the parent SrTiO 3 material, which is the lower bandgap energy of pristine SrTiO 3 samples. The bandgap energies decrease from 3.19 eV to 2.94 eV (Table 2) when the La doping concentration is increased from 0 to 5 mol.%. The bandgap energy of the Sr 1−x La x TiO 3 photocatalysts decreased with an increasing La doping level. In previous studies, Surendar et al. and Wu et al. reported that La-doping would introduce the electron donor levels in the lattice structure of SrTiO 3 , leading to the shifting of the Fermi level into the conduction band [67,68]. As a result, the bandgap energy of SrTiO 3 would be reduced and could be activated under visible light irradiation. However, at a higher La doping concentration, x = 0.1, the bandgap energy of the Sr 0.90 La 0.1 TiO 3 sample increases (3.07 eV), which may be due to the presence of impurity phases, as shown in Figure 2. Finally, the substitution of La dopant in the mesoporous SrTiO 3 nanocrystal photocatalyst dramatically contributes to the increase in light-harvesting within the visible light region (λ > 400 nm). The light-harvesting ability of Sr1−xLaxTiO3 photocatalysts was determined from their UV-visible absorption spectra, as shown in Figure 3b. The Kubelka-Munk function was used to calculate the bandgap energy of different photocatalysts by plotting [F(R)-hν] 1/2 with the energy of light (hν) (Figure 3c). The Eg values were estimated from the x-axis intercept obtained by the linear fit of the spectra shown in Figure 3c. In general, a progressive redshift of the absorption edge in the visible region is observed with an increasing La doping concentration. In other words, the La doping concentration accordingly affected the bandgap energy of the parent SrTiO3 material, which is the lower bandgap energy of pristine SrTiO3 samples. The bandgap energies decrease from 3.19 eV to 2.94 eV (Table 2) when the La doping concentration is increased from 0 to 5 mol.%. The bandgap energy of the Sr1−xLaxTiO3 photocatalysts decreased with an increasing La doping level. In previous studies, Surendar et al. and Wu et al. reported that La-doping would introduce the electron donor levels in the lattice structure of SrTiO3, leading to the shifting of the Fermi level into the conduction band [67,68]. As a result, the bandgap energy of SrTiO3 would be reduced and could be activated under visible light irradiation. However, at a higher La doping concentration, x = 0.1, the bandgap energy of the Sr0.90La0.1TiO3 sample increases (3.07 eV), which may be due to the presence of impurity phases, as shown in Figure 2. Finally, the substitution of La dopant in the mesoporous SrTiO3 nanocrystal photocatalyst dramatically contributes to the increase in light-harvesting within the visible light region (λ > 400 nm).
As shown in Figure 3d, the PL spectra of SrTiO3 contain three characteristic peaks, including a weak peak at 383 nm, a strong peak at 440 nm, and a broad peak in the range of 460-650 nm [69,70]. Furthermore, the broad green band emission in the PL spectra of Sr1−xLaxTiO3 photocatalysts demonstrates the successful doping of La +3 cations in the parent lattice of SrTiO3. The lower PL emission intensity at a higher La doping concentration indicates that more defect levels are created by the increasing La doping concentration As shown in Figure 3d, the PL spectra of SrTiO 3 contain three characteristic peaks, including a weak peak at 383 nm, a strong peak at 440 nm, and a broad peak in the range of 460-650 nm [69,70]. Furthermore, the broad green band emission in the PL spectra of Sr 1−x La x TiO 3 photocatalysts demonstrates the successful doping of La +3 cations in the parent lattice of SrTiO 3 . The lower PL emission intensity at a higher La doping concentration indicates that more defect levels are created by the increasing La doping concentration [66], according to Equation (1). This emission is due to the O 2p valance band, which corresponds to the defect level created by the oxygen deficiency. Moreover, related studies on SrTiO 3 have reported the influence of doping on photocatalytic properties, which suggests that the dopants create more impurity defects and quench the recombination process of exciting holes and electrons [66,71,72], resulting in the improvement of the overall photocatalytic activity.
TEM was employed in order to study the morphology and particle size of samples with various La doping concentrations that were hydrothermally synthesized at 130 • C for 48 h. As illustrated in Figure 4, all of the samples exhibited cubic-like morphology. Moreover, the TEM images of doped samples such as Sr 0.95 La 0.05 TiO 3 and Sr 0.90 La 0.1 TiO 3 show slightly sharp and uniform distributions under the same synthesis conditions as the non-doped sample, which has also been reported elsewhere [42,44]. Besides this, the results clearly show decreasing particle sizes with increasing La doping concentrations, which enhances the surface area of doped SrTiO 3 . The decrease in the particle size plays a vital role in decreasing the recombination of photogenerated electrons and holes, and enhances the photocatalytic activities of the catalysts. Consequently, Sr 1−x La x TiO 3 may perform well in the photocatalysis process under visible light conditions. We note that the particle sizes observed from the TEM were consistently more significant than those calculated from the Scherrer equation. Based on the Scherrer equation, the particle sizes are determined from line broadening. Because both compositional and geometric inhomogeneity, i.e., lattice strain, are affected and dependent on the line broadening [73], the above discrepancy might be attributed to both the compositional and geometric inhomogeneity of Sr 1−x La x TiO 3 .
show slightly sharp and uniform distributions under the same synthesis conditions as the non-doped sample, which has also been reported elsewhere [42,44]. Besides this, the results clearly show decreasing particle sizes with increasing La doping concentrations, which enhances the surface area of doped SrTiO3. The decrease in the particle size plays a vital role in decreasing the recombination of photogenerated electrons and holes, and enhances the photocatalytic activities of the catalysts. Consequently, Sr1−xLaxTiO3 may perform well in the photocatalysis process under visible light conditions. We note that the particle sizes observed from the TEM were consistently more significant than those calculated from the Scherrer equation. Based on the Scherrer equation, the particle sizes are determined from line broadening. Because both compositional and geometric inhomogeneity, i.e., lattice strain, are affected and dependent on the line broadening [73], the above discrepancy might be attributed to both the compositional and geometric inhomogeneity of Sr1−xLaxTiO3.  The chemical compositions of the Sr 0.95 La 0.05 TiO 3 samples were elucidated by XPS analysis ( Figure 5). Figure 5a shows the presence of C, O, Ti, Sr, and La elements in the sample, indicating that La has been introduced into the SrTiO 3 structure. The presence of C 1s with a sharp peak at approximately 284 eV corresponds to the C-C or C-H bond, which is ascribed to the adventitious carbon-based contaminant in the apparatus itself [48,74]. The high-resolution Sr 3d curve in Figure 5b is fitted into two peaks at the binding energy positions of 133.1 and 134.9 eV, belonging to Sr 3d 5/2 and Sr 3d 3/2 [48], respectively. The binding energy positions of the Ti 2d-doublet lines at 458.6 and 464.2 eV (Figure 5c)-based on Gaussian curve fitting-can be assigned to the 2p 3/2 and 2p 1/2 orbitals of Ti 4+ [48,75], respectively, which correspond to Ti with an oxidation state of 4+. As shown in Figure 5d, two observable peaks at 529.3 and 531.8 eV of the high-resolution O 1s spectrum are assigned to the Ti-O or Sr-O, and O-H bands, respectively [76]. As shown in the La 3d spectra (Figure 5e), there are two doublet peaks near 837 and 853 eV. The peaks at 834.8 and 851.5 eV are assigned to La 3d 5/2 and La 3d 3/2 , respectively, which correspond to La 3+ [77], indicating that La 3+ is doped in SrTiO 3 . However, peaks were found at 838.4 and 855.3 eV, which correspond to the shake-up satellite peaks of La 3d 5/2 and La 3d 3/2 [77], respectively. It can be concluded that La 3+ had been successfully doped into SrTiO 3 by substituting La 3+ for Sr 2+ .
trum are assigned to the Ti-O or Sr-O, and O-H bands, respectively [76]. As shown in the La 3d spectra (Figure 5e), there are two doublet peaks near 837 and 853 eV. The peaks at 834.8 and 851.5 eV are assigned to La 3d5/2 and La 3d3/2, respectively, which correspond to La 3+ [77], indicating that La 3+ is doped in SrTiO3. However, peaks were found at 838.4 and 855.3 eV, which correspond to the shake-up satellite peaks of La 3d5/2 and La 3d3/2 [77], respectively. It can be concluded that La 3+ had been successfully doped into SrTiO3 by substituting La 3+ for Sr 2+ .

Photocatalytic Activities
The photocatalytic degradation process of 2-naphthol over photocatalysts synthesized at 130 °C was obtained by measuring the residual 2-naphthol concentration in the solution over time during the irradiation. Generally, the dependence of the 2-naphthol concentration on the irradiation time can be quantitatively estimated by the kinetics of the photodegradation reaction, which is described by the kinetic equation below: where k is the apparent first-order kinetic constant that represents the reaction rate, and Co and C are the concentrations of 2-naphthol before and after irradiation, respectively.

Photocatalytic Activities
The photocatalytic degradation process of 2-naphthol over photocatalysts synthesized at 130 • C was obtained by measuring the residual 2-naphthol concentration in the solution over time during the irradiation. Generally, the dependence of the 2-naphthol concentration on the irradiation time can be quantitatively estimated by the kinetics of the photodegradation reaction, which is described by the kinetic equation below: where k is the apparent first-order kinetic constant that represents the reaction rate, and C o and C are the concentrations of 2-naphthol before and after irradiation, respectively. Figure 6 shows the photocatalytic activity of SrTiO 3 at various synthetic durations for 2-naphthol degradation under simulated natural light irradiation. The samples exhibit a different adsorption capability, which increases with the increasing BET of the sample, as shown in Table 1. Consequently, these samples exhibit quite different photocatalytic activities under simulated natural light irradiation ( Table 3). The sample calcined for 48 h degraded 2-naphthol up to 83% within 240 h of irradiation, exhibiting the highest photocatalytic activity. Moreover, the blank test reveals the stability of 2-naphthol under photolysis conditions, which is degraded by only 2.68% within 240 min of irradiation. This information confirms the outstanding photocatalytic activities of cubic SrTiO 3 photocatalysts. Figure 7 presents the photocatalytic activity of Sr 1−x La x TiO 3 photocatalysts as a function of the La doping concentration over the irradiation time. All of the Sr 1−x La x TiO 3 photocatalysts enhance photocatalytic activities and exhibit much higher photocatalytic activities for 2-naphthol degradation than the parent SrTiO 3 catalyst (Figure 7a). The substitution of higher-valance La 3+ can explain the improved photocatalytic activities of Sr 1−x La x TiO 3 by Sr 2+ in the parent structure of SrTiO 3 , which can act as sites to capture electrons, resulting in the inhibition of the recombination of photogenerated charge carriers and the acceleration of the photocatalytic reaction [48]. With the presence of a small amount of lanthanum (x = 0.03), the photoactivity of Sr 0.97 La 0.03 TiO 3 was obviously enhanced. Furthermore, the photoactivity of Sr 0.95 La 0.05 TiO 3 showed the highest catalytic activity, which was reduced by merely 92% within 180 min, which is higher than that of the parent SrTiO 3 catalyst (83%). The bandgap of Sr 0.95 La 0.05 TiO 3 is the narrowest (Table 2), which enhances its ability to absorb simulated natural light and thus improves its photocatalytic activity. Figure 6 shows the photocatalytic activity of SrTiO3 at various synthetic durations for 2-naphthol degradation under simulated natural light irradiation. The samples exhibit a different adsorption capability, which increases with the increasing BET of the sample, as shown in Table 1. Consequently, these samples exhibit quite different photocatalytic activities under simulated natural light irradiation ( Table 3). The sample calcined for 48 h degraded 2-naphthol up to 83% within 240 h of irradiation, exhibiting the highest photocatalytic activity. Moreover, the blank test reveals the stability of 2-naphthol under photolysis conditions, which is degraded by only 2.68% within 240 min of irradiation. This information confirms the outstanding photocatalytic activities of cubic SrTiO3 photocatalysts.   Figure 7 presents the photocatalytic activity of Sr1−xLaxTiO3 photocatalysts as a function of the La doping concentration over the irradiation time. All of the Sr1−xLaxTiO3 photocatalysts enhance photocatalytic activities and exhibit much higher photocatalytic activities for 2-naphthol degradation than the parent SrTiO3 catalyst (Figure 7a). The substitution of higher-valance La 3+ can explain the improved photocatalytic activities of Sr1−xLax-TiO3 by Sr 2+ in the parent structure of SrTiO3, which can act as sites to capture electrons, resulting in the inhibition of the recombination of photogenerated charge carriers and the acceleration of the photocatalytic reaction [48]. With the presence of a small amount of lanthanum (x = 0.03), the photoactivity of Sr0.97La0.03TiO3 was obviously enhanced. Furthermore, the photoactivity of Sr0.95La0.05TiO3 showed the highest catalytic activity, which was reduced by merely 92% within 180 min, which is higher than that of the parent SrTiO3 catalyst (83%). The bandgap of Sr0.95La0.05TiO3 is the narrowest ( Table 2), which enhances its ability to absorb simulated natural light and thus improves its photocatalytic activity.  According to the corresponding kinetic study, the kinetic curves of the samples for the degradation of 2-naphthol are shown in Figure 7b, which agree with the pseudofirst-order reaction, and the best-fit parameters are listed in Table 4. The rate constant of Sr 0.95 La 0.05 TiO 3 (k = 0.0196 min −1 ) is the highest among the samples, and decreases in the order of Sr 0.95 La 0.05 TiO 3 > Sr 0.97 La 0.03 TiO 3 > Sr 0.9 La 0.1 TiO 3 > SrTiO 3 . At higher La contents (x = 0.1, Sr 0.9 La 0.1 TiO 3 ), the photocatalytic activity decreases. The decrease in photocatalytic activity can be attributed to the enhanced concentration of the impurity phase, which can become the recombination center of electrons and holes [78], thereby reducing the efficiency of the charge separation and resulting in reduced photocatalytic activity. Besides this, the ability of Sr 0.95 La 0.05 TiO 3 nanocubes to degrade 2-naphthol is much better than that of other photocatalysts reported in the literature [79], which was 0.0126 min −1 . It could be concluded that Sr 0.95 La 0.05 TiO 3 enhanced the highest photocatalytic activities, which is mainly due to their higher light absorption capability, narrower bandgap, and lower recombination rate of photogenerated electron-hole pairs. According to the corresponding kinetic study, the kinetic curves of the samples for the degradation of 2-naphthol are shown in Figure 7b, which agree with the pseudo-firstorder reaction, and the best-fit parameters are listed in Table 4. The rate constant of Sr0.95La0.05TiO3 (k = 0.0196 min −1 ) is the highest among the samples, and decreases in the order of Sr0.95La0.05TiO3 > Sr0.97La0.03TiO3 > Sr0.9La0.1TiO3 > SrTiO3. At higher La contents (x = 0.1, Sr0.9La0.1TiO3), the photocatalytic activity decreases. The decrease in photocatalytic activity can be attributed to the enhanced concentration of the impurity phase, which can become the recombination center of electrons and holes [78], thereby reducing the efficiency of the charge separation and resulting in reduced photocatalytic activity. Besides this, the ability of Sr0.95La0.05TiO3 nanocubes to degrade 2-naphthol is much better than that of other photocatalysts reported in the literature [79], which was 0.0126 min −1 . It could be concluded that Sr0.95La0.05TiO3 enhanced the highest photocatalytic activities, which is mainly due to their higher light absorption capability, narrower bandgap, and lower recombination rate of photogenerated electron-hole pairs.   The zero-point charge (pH zpc ) strongly affects the adsorption capability/behaviour of organic compounds on the photocatalyst's surface during a photocatalytic process [80]. The ∆pH = pH final − pH initial was measured for different pH values (from 4 to 10) in order to understand the behaviour of the surface charge of the photocatalysts in aqueous solution. As seen in Table 2, the pHzpc values of the Sr 1−x La x TiO 3 photocatalysts were measured to be approximately 7.78, 7.42, 7.32, and 7.61, respectively, which reveals that the charge on the surface of SrTiO 3 has been modified by La doping. Moreover, the reduction in pHzpc was due to the increase in oxygen vacancies, increasing the surface −OH groups owing to La doping.
The photocatalytic degradation of 2-naphthol by the photocatalyst Sr 0.95 La 0.05 TiO 3 in aqueous suspensions prepared at different pH values (pH = 4.1-11.3) was investigated. Figure 8 shows the effect of the initial pH on the 2-naphthol degradation efficiency. The 2-naphthol degradation decreased when the initial pH shifted from 4.1 to 11.3. The degra-dation efficiencies were recorded to be 95, 93, 85, and 74% after 150 min of irradiation at pH 4.1, 6.3, 9.1, and 11.3, respectively. The change in the overall photocatalytic degradation can be explained by the surface charge of the photocatalyst and the dissociation behaviour of 2-naphthol. With the pHzpc for Sr 0.95 La 0.05 TiO 3 being near 7.32, the surface of the Sr 0.95 La 0.05 TiO 3 photocatalyst is predominantly positively charged at pH values below pHzpc, but higher pH values promote the formation of a negative charge on the NPs [81]. However, 2-naphthol is a weak acid with a dissociation constant (pKa) of 9.5 [82]. It exists in neutral forms at pH < pKa and becomes anionic when the solution pH > pKa. Therefore, it is more favourable to adsorb on the surface of the catalyst at pH < 9.5. The higher efficiencies of Sr 0.95 La 0.05 TiO 3 at pH 4.1 and 6.3 may be attributed to the adsorption of neutral 2-naphthol on the positive charge on photocatalyst surfaces resulting in photocatalytic degradation. On the other hand, at higher pH (> 9.5), the surface of Sr 1−x La x TiO 3 becomes negatively charged and 2-naphthol becomes an anionic species, leading to higher electrostatic repulsion between the catalyst and 2-naphthol [83]. Finally, it can be concluded that the degradation rate was higher in acid media than in base media. Similar behaviour was observed by several studies reported in the literature [75,84]. ured to be approximately 7.78, 7.42, 7.32, and 7.61, respectively, which reveals that the charge on the surface of SrTiO3 has been modified by La doping. Moreover, the reduction in pHzpc was due to the increase in oxygen vacancies, increasing the surface −OH groups owing to La doping.
The photocatalytic degradation of 2-naphthol by the photocatalyst Sr0.95La0.05TiO3 in aqueous suspensions prepared at different pH values (pH = 4.1-11.3) was investigated. Figure 8 shows the effect of the initial pH on the 2-naphthol degradation efficiency. The 2-naphthol degradation decreased when the initial pH shifted from 4.1 to 11.3. The degradation efficiencies were recorded to be 95, 93, 85, and 74% after 150 min of irradiation at pH 4.1, 6.3, 9.1, and 11.3, respectively. The change in the overall photocatalytic degradation can be explained by the surface charge of the photocatalyst and the dissociation behaviour of 2-naphthol. With the pHzpc for Sr0.95La0.05TiO3 being near 7.32, the surface of the Sr0.95La0.05TiO3 photocatalyst is predominantly positively charged at pH values below pHzpc, but higher pH values promote the formation of a negative charge on the NPs [81]. However, 2-naphthol is a weak acid with a dissociation constant (pKa) of 9.5 [82]. It exists in neutral forms at pH < pKa and becomes anionic when the solution pH > pKa. Therefore, it is more favourable to adsorb on the surface of the catalyst at pH < 9.5. The higher efficiencies of Sr0.95La0.05TiO3 at pH 4.1 and 6.3 may be attributed to the adsorption of neutral 2-naphthol on the positive charge on photocatalyst surfaces resulting in photocatalytic degradation. On the other hand, at higher pH (> 9.5), the surface of Sr1−xLaxTiO3 becomes negatively charged and 2-naphthol becomes an anionic species, leading to higher electrostatic repulsion between the catalyst and 2-naphthol [83]. Finally, it can be concluded that the degradation rate was higher in acid media than in base media. Similar behaviour was observed by several studies reported in the literature [75,84]. In order to evaluate the stability of the Sr0.95La0.05TiO3 nanocube photocatalytic activities, four photocatalytic experimental runs were carried out by adding recycled Sr0.95La0.05TiO3 photocatalyst to fresh 2-naphthol solutions (10 ppm) with the same catalyst In order to evaluate the stability of the Sr 0.95 La 0.05 TiO 3 nanocube photocatalytic activities, four photocatalytic experimental runs were carried out by adding recycled Sr 0.95 La 0.05 TiO 3 photocatalyst to fresh 2-naphthol solutions (10 ppm) with the same catalyst dosage ( Figure 9). As demonstrated in Figure 9a, the photoactivity of the photocatalyst did not show a significant decrease after four cycles of degradation. The yield of 2-naphthol degradation was maintained at nearly 86% after 180 min of irradiation up to the fourth cycle, which is 95% of the original photocatalytic degradation efficiency. Additionally, the degradation rate was observed to be stable after four cycles. The XRD patterns and FTIR spectra that compare the crystal structure and surface absorption bands of the fresh and used Sr 0.95 La 0.05 TiO 3 photocatalyst are illustrated in Figure 9b,c. Clearly, the crystal structure of the used Sr 0.95 La 0.05 TiO 3 photocatalyst did not change after the photocatalytic process. As shown in Figure 9c [32]. In all of the samples, the shoulder around 860 cm −1 represents the SrTiO 3 crystal lattice vibrations [42]. The similarity of the FTIR spectra of the fresh and used photocatalysts is notable. These results further confirm that the synthesized Sr 0.95 La 0.05 TiO 3 nanoparticles could be regenerated easily and reused with good reusability for organic degradation.
feature the possibilities of Sr-O/Ti-O/Cr-O bonds and functional groups. The two characteristic absorption bands, located at about 457 and 610 cm −1 , are ascribed to the vibrations of the metal-oxygen bonds Sr-O/Ti-O/La-O [32,85,86]. The broad and low-intensity absorption bands observed in all of the samples in the range 2850-3440 cm −1 , 1458 cm −1 , and 1618 cm −1 correspond to the stretching and bending vibrations of O-H groups in the physically adsorbed H2O molecules, respectively [32]. In all of the samples, the shoulder around 860 cm −1 represents the SrTiO3 crystal lattice vibrations [42]. The similarity of the FTIR spectra of the fresh and used photocatalysts is notable. These results further confirm that the synthesized Sr0.95La0.05TiO3 nanoparticles could be regenerated easily and reused with good reusability for organic degradation.  Although the conditions for conducting the experiments are different, it is worth comparing the recent studies on the photodegradation of 2-naphthol in terms of degradation efficiency. Table 5 shows several achievements of the photodegradation of 2-naphthol in the literature [31,[87][88][89][90][91][92]. As we can see in the table, photocatalysis could effectively remove 2-naphthol with attractive performance. As an example, MnOx-modified (Ce 0.73 Bi 0.27 )O 2-δ performed an excellent photocatalytic activity at 50 • C, which reached 98% degradation efficiency [88]. In this study, it is achieved 86.6% degradation efficiency at room-temperature conditions over Sr 0.95 La 0.05 TiO 3 photocatalyst.

Synthesis of Sr 1−x La x TiO 3 Nanocubes
The Sr 1−x La x TiO 3 nanocubes were synthesized by a facile hydrothermal method. For the parent SrTiO 3 , 3.9990 g (0.015 mol), SrCl 2 .6H 2 O was dissolved in 40 mL 3 M NaOH at room temperature under vigorous magnetic stirring for 1 h. Next, 1.1985 g TiO 2 (molar ratio Sr:Ti = 1:1) was dispersed into the above solution and stirred for another 1 h before being transferred to the autoclave. The mixture was transferred to a 200 mL Teflon-lined autoclave vessel, sealed, and heated at 130 • C for various durations (from 12 h to 72 h). After the hydrothermal process, the system was cooled to room temperature, and the solid precipitate was removed by centrifugation and washed several times with absolute ethyl alcohol and deionized water in order to remove the sodium hydroxide and residual chemicals. The washing process was repeated three times. Finally, the obtained powder was dried at 80 • C overnight. The samples that were hydrothermally processed at 130 • C for 12, 24, 48, and 72 h were designated SrTiO 3 -12, SrTiO 3 -24, SrTiO 3 -48, and SrTiO 3 -72.
For the La-doped SrTiO 3 (Sr 1−x La x TiO 3 , x = 0.03-0.1), the nanocubes were synthesized using the same procedure as that used for SrTiO 3 . In typically, an appropriate amount of La(NO 3 ) 3 .6H 2 O was dissolved together with the strontium precursor, and the hydrothermal conditions were set to 130 • C for 48 h.

Characterizations
X-ray diffraction (XRD) studies were recorded with a D8 Advance-Brucker diffractometer (Bruker, USA) generating Cu Kα radiation (λ = 0.15418 nm) at a scanning rate of 0.03 • /s and in the scanning range of 20 to 80 • , with a step size of 0.02 • . FTIR spectroscopy was measured at 4 cm −1 spectral resolution between the 400 to 4000 cm −1 range using a Perkin Elmer Frontier 1600 series spectroscope. The transfer behaviour of the photogenerated electrons and holes between various samples was studied using photoluminescence (PL) spectra (HORIBA Jobin YVON iHR 320, (Kyoto, Japan)) with a wavelength range of 350-620 nm. Scanning electron microscopy (SEM) images were taken using a JSM-6500F, JEOL (Tokyo, Japan). The morphology of the obtained nanocubes was observed by transmission electron microscopy (TEM, JEOL-JEM1010, Tokyo, Japan). The bandgap energy of each sample was calculated from diffuse reflectance spectroscopy (DSR), ranging from 850 to 220 nm, with a scanning step of 2 nm at a rate of 400 nm/min using solid UV-vis JASCO V-550 (Tokyo, Japan) equipment. The N 2 adsorption-desorption isotherms of SrTiO 3 were obtained by using a nitrogen adsorption-desorption apparatus (Quantachrome NOVA 1000e Surface Area and Pore Size Analyzer (Boynton Beach, FL, U.S.A.) at a liquid nitrogen temperature of −196 • C. The multipoint Brunauer-Emmett-Teller (BET) equation was applied using the data of the relative pressure (P/P 0 ) to determine the specific surface area. The porosity of the samples was also investigated using DA (Dubinin-Astakhov) models. X-ray photoelectron spectroscopy (XPS), was recorded on ESCALAB 250Xi (Thermo Fisher Scientific, Waltham, MA, USA) to determine the oxidation states of the elements.
The zero point charges (pHzpc) of the photocatalysts were measured in 30 mL portions of NaCl aqueous solution (0.05 mol/L) adjusted to the different pH values by either 0.1 M HCl or 0.1 M NaOH solution. N 2 gas was bubbled through the NaCl solutions in order to remove the dissolved CO 2 until the initial pH was stabilized. After the determination of the initial pH value, the solutions were mixed with 0.090 g of the catalyst sample for 24 h, and the final pH of the solutions was then measured.

Photocatalytic Activity
The photocatalytic process was conducted in a water-jacketed Pyrex photoreactor, which was circulated with water to maintain a temperature of approximately 30 • C. The photoreactor was placed in a black chamber in order to prevent the impact of any external radiation sources. Photocatalytic 2-naphthol degradation was conducted by dispersing 0.10 g photocatalyst powder in 200 mL 2-naphthol solution with an initial concentration of 10 ppm (natural pH 6.3) under Exo Terra Natural Light irradiation (Repti Glo 2.0 Comp Fluor 26 W PT2191-220, Illuminance: 15350 Lux, 400-700 nm) and a stirring speed of 400 rpm. In order to avoid systematic errors, the aforementioned 2-naphthol solution was diluted from the stock 1000 ppm solution. Prior to the visible light illumination, the suspension was magnetically stirred for 2 h in the dark in order to establish adsorption-desorption equilibrium between the photocatalyst and 2-naphthol. The mixture was then exposed to illumination, and at a given irradiation time interval of 30 min, 5 mL of the solution was extracted using a syringe and then filtered through a 0.22 µm cellulose acetate membrane (Millipore Corp. Bedford, MA). A model U-2910 Spectrophotometer from Hitachi, Tokyo, Japan monitored the residual 2-naphthol concentration with the characteristic absorption of 2-naphthol at a wavelength of 223 nm. The photocatalytic degradation efficiency (D e ) of 2-naphthol was calculated by the expression of D e = (1 − A t /A o ) × 100%, where A 0 and A t are the absorbance at 464 nm of the characteristic wavelength of the 2-naphthol solution before and after irradiation at time t, respectively. The blank test was also carried out with the same photocatalytic process procedure for comparison purposes, but without the presence of Sr 1−x La x TiO 3 photocatalysts. The photocatalytic stability was also investigated by evaluating the removal of 2-naphthol as a function of the experimental cycle. At the end of each cycle, the photocatalyst was collected by centrifugation, rinsed with deionized water, and dried at 300 • C for 2 h to remove the 2-naphthol contaminant before its use in the next cycle.

Conclusions
In this study, Sr 1−x La x TiO 3 nanocubes with different La dopant concentrations were successfully synthesized by a hydrothermal method, and their physical properties were investigated. The XRD patterns showed a cubic structure, and the TEM images presented a nanocube morphology with a size range of 40-50 nm. The higher photocatalytic activity of the doped samples compared to pristine SrTiO 3 was attributed to the fact that La-doped SrTiO 3 can harvest irradiation light because of its relatively narrow bandgap energy, create more impurity defects, and quench the recombination process of exciting holes and electrons. The Sr 0.95 La 0.05 TiO 3 nanocubes exhibited the best photocatalytic performance for 2-naphthol degradation under artificial solar light with a 95% degradation efficiency after 180 min and a pseudo-first-order degradation rate constant of 0.0196 min −1 , which are higher than those of pure SrTiO 3 . Importantly, the photocatalytic activity over Sr 0.95 La 0.05 TiO 3 maintained stable efficiency after four cycles. These observations demonstrated that Sr 1−x La x TiO 3 nanocubes could be widely applied in wastewater treatment.