*Article* **Preparation, Microstructural Characterization and Photocatalysis Tests of V5+-Doped TiO2/WO<sup>3</sup> Nanocomposites Supported on Electrospun Membranes**

**Michel F. G. Pereira <sup>1</sup> , Mayane M. Nascimento <sup>1</sup> , Pedro Henrique N. Cardoso <sup>1</sup> , Carlos Yure B. Oliveira <sup>2</sup> , Ginetton F. Tavares <sup>3</sup> and Evando S. Araújo 1,\***


**Abstract:** Metal oxide nanocomposites (MON) have gained significant attention in the literature for the possibility of improving the optical and electronic properties of the hybrid material, compared to its pristine constituent oxides. These superior properties have been observed for TiO<sup>2</sup> — based MON, which exhibit improved structural stability and photoactivity in environmental decontamination processes. In addition, the use of polymer membrane-supported MON is preferable to prevent further aggregation of particles, increase the surface area of the semiconductor in contact with the contaminant, and enable material reuse without considerable efficiency loss. In this work, V 5+-doped TiO2/WO<sup>3</sup> MON nanostructures were prepared by the sintering process at 500 ◦C and supported in electrospun fiber membranes for application as photocatalyst devices. Microstructural characterization of the samples was performed by XRD, SEM, EDS, Raman, and DSC techniques. The reflectance spectra showed that the bandgap of the MON was progressively decreased (3.20 to 2.11 eV) with the V5+ ions doping level increase. The fiber-supported MON showed photoactivity for rhodamine B dye degradation using visible light. In addition, the highest photodegradation efficiency was noted for the systems with 5 wt% vanadium oxide dispersed in the fibers (92% dye degradation in 120 min of exposure to the light source), with recyclability of the composite material for use in new photocatalysis cycles. The best results are directly related to the microstructure, lower bandgap and aggregation of metal oxide nanocomposite in the electrospun membrane, compared to the support-free MON.

**Keywords:** metal oxide nanocomposites; microstructural analysis; electrospinning; polymer substrate; photodegradation

## **1. Introduction**

The increase in industrial activity associated with the accelerated growth of the world population in recent decades is one of the main factors that contribute to the pollution of the physical and biological components on earth. In particular, the inappropriate disposal of by-products from the production of medicines, agrochemicals, heavy metals, and dyes can contaminate aquatic environments, due to its toxic and carcinogenic components resulting from the decomposition of its molecules. The scarcity of effective and low-cost procedures that ensure large-scale discarding and treatment of industrial waste contributes to intensifying this current problem [1,2].

Although the advanced water treatment technologies, such as sedimentation, coagulation, aerobic-activated sludge-based treatment, and nitrification–denitrification have been widely used after conventional primary and secondary treatments, they have some

**Citation:** Pereira, M.F.G.;

Nascimento, M.M.; Cardoso, P.H.N.; Oliveira, C.Y.B.; Tavares, G.F.; Araújo, E.S. Preparation, Microstructural Characterization and Photocatalysis Tests of V5+-Doped TiO2/WO<sup>3</sup> Nanocomposites Supported on Electrospun Membranes. *Inorganics* **2022**, *10*, 143. https://doi.org/ 10.3390/inorganics10090143

Academic Editor: Roberto Nisticò

Received: 2 August 2022 Accepted: 14 September 2022 Published: 19 September 2022

**Publisher's Note:** MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

**Copyright:** © 2022 by the authors. Licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution (CC BY) license (https:// creativecommons.org/licenses/by/ 4.0/).

drawbacks, such as high energy consumption, carbon emission, excess sludge discharge, ineffectiveness in removing contaminants, such as organic dyes, and considerable additional cost [3,4]. In this sense, the search for new technologies and functional materials for water treatment that are able to meet current needs, with lower cost and environmental impact, is an open field of research today [2,5–7].

Metal oxides (semiconductors that respond to external stimulus—light, electric potential, pressure, among others) have received increased attention from academic researchers and industrial developers as potential materials for the production of efficient and environmentally friendly devices for the remediation of organic-contaminated water [8–10]. This ability is directly related to their intrinsic properties, such as high chemical and structural stability, high surface area/volume ratio, excellent electrical/electronic response, surface interactions with contaminant molecules, and the possibility of reusing the material in new decontamination cycles [8].

In particular, the use of metal oxide nanocomposites (MON) (resulting from the mixture between two or more selective nanoscale metal oxides [11,12] has been preferable for these applications, due to the possibility of having better decontamination performance when compared to the use of their constituent oxides, in isolation. Currently, among the environmentally friendly techniques for removing contaminants using MON, heterogeneous photocatalysis (HP) stands out [13,14].

Heterogeneous photocatalysis is a photochemical process for the formation of free radicals, such as the hydroxyl HO·, which is a highly oxidizing agent, and degrades organic substances present in water. When the semiconductor in solution is exposed to a light source with sufficient energy to activate it, the absorption of photons with higher energy than the semiconductor bandgap occurs. At the electronic level, this process causes an electron (e−) to be transferred from the valence band to the conduction band of the material, leaving a hole (h<sup>+</sup> ) in the valence band. These holes generate HO· free radicals from the water adsorbed on the metal oxide surface, which are used in the organic contaminant oxidation reactions [14].

Titanium dioxide in its allotropic anatase form (anatase TiO2, ~3.2 eV bandgap) is one of the most widely used oxides in HP using MON, due to its non-toxicity, high chemical stability, excellent photoactivity and photostability, and lower cost than other oxides [15,16]. A limitation for photocatalytic processes using anatase is the demand of ultraviolet radiation as a light stimulus. The light source must have a higher energy than the material bandgap energy, so that electrons from its valence band can be ejected into its conduction band, which would not occur using visible light. Advances in this field of research involve the incorporation of selective metal oxides into TiO2, such as tungsten, zinc, indium, copper, niobium, and vanadium oxides, in order to increase the process efficiency [1,15,17,18].

Tungsten trioxide (WO3, 2.6–2.8 eV bandgap) has excellent electrical charge transfer properties, broadens the excitation wavelength range of the final material, in addition to promoting effective photocharge separation of the composite catalyst and inhibiting electron-hole recombination, which significantly improves the MON photocatalytic activity [19,20]. The interaction of WO<sup>3</sup> with TiO<sup>2</sup> increases the conductivity of the TiO2/WO<sup>3</sup> system in comparison to pure TiO<sup>2</sup> [21,22], while TiO<sup>2</sup> doping with niobium pentoxide (Nb2O5) [23] or vanadium pentoxide (V2O5) [24] delays the phase transition from anatase to rutile (phase with less active surface) and improves the electronic properties of the resulting material [17]. In addition, the combined action between TiO2, WO3, and V2O<sup>5</sup> results in nanocomposites with superior performance (sensitivity, electric and electronic properties, catalysis and phase stability), which demonstrate the emerging possibilities of using this MON configuration for environmental decontamination applications [21,25,26].

Its particles must be available in a small enough size to provide a large surface area of action, in order to enhance the MON photocatalytic activity. In practice, as the concentration of nanoparticles in solution increases, the tendency of these particles to agglomerate can also increase [27], which is the opposite of what is expected. In these studies, the impossibility of filtration or complete removal of oxide particles from the aqueous environment after the reaction is observed. This represents a limitation for the reuse of the functional material in new photocatalysis cycles (or even to prevent water contamination) [28]. In recent years, these limitations have motivated the development of supported nanoparticles [29,30]. In this configuration, different types of substrates are used, such as porous glasses, lamellar compounds, zeolites, and polymer membranes, in order to disperse and stabilize the metal oxides [29,30]. The advantages of using an inert polymeric matrix as support for photocatalysts are the possibility of having flexible devices, as well as the ease of oxides removal from the aqueous environment, without significant loss of photocatalyst for reuse [29,31].

In this work, V <sup>5</sup>+-doped TiO2/WO<sup>3</sup> (1/1 in mol) nanostructures were prepared with different dopant concentrations, dispersed in a fibrous membrane (with high surface area to volume ratio) from the electrospinning process and tested as photocatalyst device. The materials microstructure was characterized by scanning electron microscopy (SEM), energy dispersive spectroscopy (EDS), X-ray diffraction (XRD), Raman spectroscopy, differential scanning calorimetry (DSC), and UV–vis with diffuse reflectance spectroscopy (DRS) methods, and their properties were related to the results obtained in photocatalysis tests, from the degradation of rhodamine B (RhB) model dye in aqueous solution. The results indicated that the interaction between the constituent oxides and their dispersion in the electrospun membrane were factors that significantly improved the efficiency of the degradation process using visible light, in addition to enabling the reuse of these functional materials in new photocatalysis cycles.

#### **2. Results and Discussion**

#### *2.1. Microstructural Analysis*

The XRD data of the TW, TWV3, and TWV5 MON are shown in Figure 1. The X-Pert HighScore software was used to identify the crystal phases of the studied materials. The crystallographic parameters were obtained from the International Center for Diffraction Data (ICDD). The tetragonal crystal phase of the anatase TiO<sup>2</sup> (a = b = 3.7821 Å, c = 9.5022 Å, and α = β = γ = 90◦ lattice constants [32], 01-071-1166 ICDD card) and monoclinic WO<sup>3</sup> (a = 7.306 Å, b = 7.540 Å, c = 7.692 Å, α = γ = 90◦ and β 6= 90◦ [33], 01-083-0951 ICDD card) were detected by XRD measurements. This demonstrates that the oxide mixture sintering (with the selected parameters) has not resulted in a phase change or crystalline solid solution formation in the resulting MON.

In addition, no diffraction peaks of V2O<sup>5</sup> were detected in the XRD spectra of the TWV3 and TWV5 composites, in comparison to the TW sample [34]. The V2O<sup>5</sup> nanopowders were used with low weight percentages and are uniformly dispersed in the TiO2/WO<sup>3</sup> base mixture. This corroborates that the crystallographic planes of V2O<sup>5</sup> (concentrated in the region of 2θ = 20–35◦ [35]) were superimposed by the peaks of TiO<sup>2</sup> and WO<sup>3</sup> (with higher intensities).

All sintered oxide mixtures show similar values of WO<sup>3</sup> parameters, with a = 7.30 Å, b = 7.53 Å, c = 7.68 Å, α = γ = 90◦ , and β = 90.59◦ , with no changes in comparison to lattice constants of the starting material.

The TiO<sup>2</sup> crystal constants in the TW sample (Table 1) also show similar results to the pristine material (a = b = 3.783 Å, c = 9.509 Å, and α = β = γ = 90◦ [22]), since the 1:1 in mol TiO2:WO<sup>3</sup> configuration (WO<sup>3</sup> wt% close to that of TiO2) provides a greater surface interaction between the oxides [34]. On the other hand, the a, b, and c values increased in vanadium-doped samples, in comparation to the TW sample (Table 1). This also demonstrates an increase in the TiO<sup>2</sup> unit cell volume (with no significant difference in this variable from TWV3 to the TWV5 sample). This suggests an atomic interaction degree, directly proportional to the dopant concentration. In fact, the ionic radius of the V <sup>5</sup><sup>+</sup> ions (0.68 Å [36]) is approximate to the T <sup>4</sup><sup>+</sup> ions, which step up the occurrence of vanadium ions doping in the atomic structure of anatase, because of the sintering process.

**Figure 3.** XRD spectra of the TW, TWV3 and TWV5 nanostructures. The colored bars represent the crystallographic planes described in the TiOଶ and WOଷ ICDD cards. **Figure 1.** XRD spectra of the TW, TWV3 and TWV5 nanostructures. The colored bars represent the crystallographic planes described in the TiO<sup>2</sup> and WO<sup>3</sup> ICDD cards.


The TiOଶ crystal constants in the TW sample (Table 1) also show similar results to **Table 1.** Lattice constants and crystallite size of titanium dioxide in TW, TWV3, and TWV5 MON.

degree, directly proportional to the dopant concentration. In fact, the ionic radius of the Vହା ions (0.68 Å [36]) is approximate to the Tସା ions, which step up the occurrence of vanadium ions doping in the atomic structure of anatase, because of the sintering process. **Table 1.** Lattice constants and crystallite size of titanium dioxide in TW, TWV3, and TWV5 MON. The crystallite average sizes (D) of the WO<sup>3</sup> and TiO<sup>2</sup> in the sintered MON were calculated by the modified Scherrer equation (MSE). By the equation, D = λ/(3β cos(θ)) [37], where λ is the wavelength of X-ray radiation, β is the width at half height of the peaks detected in the XRD spectrum, θ is the half of the diffraction angle in these crystallographic planes, and 1/3 is the correction factor for the limit of application of the Sherrer law [38].

 (Å) , () MON a=b c TW 3.783 9.509 20.23(±2.09) TheWO<sup>3</sup> presentedDvalues of 15.67 (±1.22) nm, 15.84 (±1.04) nm, and 15.91 (±1.62) nm for the TW, TWV3, and TWV5 samples, respectively. In addition, in these systems, the crystallite size values for TiO<sup>2</sup> (Table 1) were 20.23 (±2.09) nm, 25.31 (±2.64) nm, and 25.43 (±2.67) nm, in increasing order of V2O<sup>5</sup> concentration.

TWV3 3.803 9.704 25.31(±2.64) TWV5 3.804 9.708 25.43(±2.67) The crystallite average sizes (D) of the WOଷ and TiOଶ in the sintered MON were calculated by the modified Scherrer equation (MSE). By the equation, D = λ ⁄ (3βcos(θ)) [37], where λ is the wavelength of X-ray radiation, β is the width at half height of the The results for the hypothesis test of means equality (n = 3) demonstrated that the average size of the WO<sup>3</sup> crystallite does not indicate significant changes in the three MON configurations. On the other hand, in MON doped with 3 wt% and 5 wt% of vanadium oxide, a significant increase in TiO<sup>2</sup> crystallite size is confirmed when compared to the TW sample. There is no statistical difference between the D values calculated for these last two systems.

peaks detected in the XRD spectrum, θ is the half of the diffraction angle in these crys-

The Raman spectra of MON are presented in Figure 2. The spectrum of pristine anatase TiO<sup>2</sup> was also analyzed in order to compare with composite samples. In Figure 2a is shown that the molecular vibration bands of anatase (141, 196, 397, 514, and 638 cm−<sup>1</sup> wavenumbers [39]) occur in all spectra of the metal oxide nanocomposites, although shifted to lower wavenumbers (redshift), by 7–11 cm−<sup>1</sup> . In addition, the monoclinic WO<sup>3</sup> bands were determined, typically at 268, 319, 710, and 802 cm−<sup>1</sup> , with no wavenumber variation in comparison to the pure oxide [34,40]. *Inorganics* **2022**, *10*, x FOR PEER REVIEW 6 of 19

**Figure 2.** (**a**) Raman spectra of the metal oxide nanocomposites compared to pristine anatase TiO; (**b**) representative Raman mapping of MON samples, with indication of TiO and WO vibrational bands. **Figure 2.** (**a**) Raman spectra of the metal oxide nanocomposites compared to pristine anatase TiO2; (**b**) representative Raman mapping of MON samples, with indication of TiO<sup>2</sup> and WO<sup>3</sup> vibrational bands.

The redshift effect occurs due to the process of surface relaxation, distortions, and additional vibration energy in the crystal lattice (phonon confinement) of the material [41]. In particular, the occurrence of this phenomenon in the MON Raman spectra indicates that W and V ions occupied vacancies of available Ti atoms in the crystal lattice of anatase (as previously expected). The occupation of these sites by W and V spe-The redshift effect occurs due to the process of surface relaxation, distortions, and additional vibration energy in the crystal lattice (phonon confinement) of the material [41]. In particular, the occurrence of this phenomenon in the MON Raman spectra indicates that W6<sup>+</sup> and V <sup>5</sup><sup>+</sup> ions occupied vacancies of available Ti atoms in the crystal lattice of anatase (as previously expected). The occupation of these sites by W and V species allows

The combined results of SEM images, XRD (with anatase unit cell volume invariance in V5+−doped MON), and Raman analysis (not detected VO bands, with redshift of TiO bands) indicate that at 5 wt% dopant concentration, a greater amount of the vana-

cies allows a greater degree of local vibrations and facilitates the molecules collective excitation, which favors photocatalysis processes [41,42]. The representative Raman map-

vibration modes in these MON.

a greater degree of local vibrations and facilitates the molecules collective excitation, which favors photocatalysis processes [41,42]. The representative Raman mapping (Figure 2b) of V 5+-doped samples is an important tool that confirms the regular distribution of TiO<sup>2</sup> and WO<sup>3</sup> bands in the materials surface, with no additional active vibration modes in these MON. cies allows a greater degree of local vibrations and facilitates the molecules collective excitation, which favors photocatalysis processes [41,42]. The representative Raman mapping (Figure 4b) of V5+-doped samples is an important tool that confirms the regular distribution of TiOଶ and WOଷ bands in the materials surface, with no additional active vibration modes in these MON.

The redshift effect occurs due to the process of surface relaxation, distortions, and additional vibration energy in the crystal lattice (phonon confinement) of the material [41]. In particular, the occurrence of this phenomenon in the MON Raman spectra indicates that Wା and Vହା ions occupied vacancies of available Ti atoms in the crystal lattice of anatase (as previously expected). The occupation of these sites by W and V spe-

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The combined results of SEM images, XRD (with anatase unit cell volume invariance in V 5+-doped MON), and Raman analysis (not detected V2O<sup>5</sup> bands, with redshift of TiO<sup>2</sup> bands) indicate that at 5 wt% dopant concentration, a greater amount of the vanadium species is arranged in the sites initially unoccupied by titanium atoms, showing the effectiveness of the performed doping process. The combined results of SEM images, XRD (with anatase unit cell volume invariance in V5+-doped MON), and Raman analysis (not detected VଶOହ bands, with redshift of TiOଶ bands) indicate that at 5 wt% dopant concentration, a greater amount of the vanadium species is arranged in the sites initially unoccupied by titanium atoms, showing the effectiveness of the performed doping process.

The study of variations in crystallite sizes in the nanostructured systems was important to determine the doping level in the atomic structure of TiO<sup>2</sup> and their effects for application of these materials as photocatalysts. In fact, when the MON crystallites are in nanometer scale, the movement of electrons and holes in an excited semiconductor also depends on the quantum confinement effect. In other words, the phonons resulting from the doping process also influence material electronic properties [43]. The study of variations in crystallite sizes in the nanostructured systems was important to determine the doping level in the atomic structure of TiOଶ and their effects for application of these materials as photocatalysts. In fact, when the MON crystallites are in nanometer scale, the movement of electrons and holes in an excited semiconductor also depends on the quantum confinement effect. In other words, the phonons resulting from the doping process also influence material electronic properties [43].

Surface micrographs of TWV3 and TWV5 MON (resulting from sintering at 500 ◦C) were obtained by SEM (Figure 3a,b). Initial analysis returns mostly spherical particles (100–230 nm range), with significant overall contact surface, with no significant differences when compared to the dopant-free TW matrix [22]. The EDS mapping of V 5+-doped samples (Figure 3c) confirms the Ti and W metals matrix and vanadium dopant evenly distributed over the entire material structure, which favors the application of these nanostructures as photocatalysts. Surface micrographs of TWV3 and TWV5 MON (resulting from sintering at 500 °C) were obtained by SEM (Figure 5a,b). Initial analysis returns mostly spherical particles (100–230 nm range), with significant overall contact surface, with no significant differences when compared to the dopant-free TW matrix [22]. The EDS mapping of V5+−doped samples (Figure 5c) confirms the Ti and W metals matrix and vanadium dopant evenly distributed over the entire material structure, which favors the application of these nanostructures as photocatalysts.

**Figure 5.** SEM micrographs of (**a**) TWV3 and (**b**) sintered TWV5 MON; (**c**) representative EDS mapping of V5+−doped samples, with indication of Ti, W, and V elements. **Figure 3.** SEM micrographs of (**a**) TWV3 and (**b**) sintered TWV5 MON; (**c**) representative EDS mapping of V5+-doped samples, with indication of Ti, W, and V elements.

The calculated mean sample diameters were 145.7 ± 47.0 nm (n = 135) [20], 160.1 ± 74.1 nm (n = 123), and 169.4 ± 63.1 nm (n = 141), for TW, TWV3, and TWV5 MON, respectively. The equality of means tests results (n = 3) demonstrate that there is no significant difference between the average particle size calculated for these produced MON (*p*-value > α for all comparison of means).

The bandgap energy of the MON semiconductors was calculated from the DRS data (Figure 4a), using the Tauc plot (Figure 4b). By the Tauc relation, the curve of the product of the absorption coefficient (α) and photon energy (E = *hv*) to the power of 1/r, (αhv) 1/r , is plotted as a function of the photon energy (E). The intersection of the auxiliary line in the linearity region of the graph with the x axis represents the measurement of the material optical energy gap (Eg) [44]. Thus, the type of electronic transition (direct or indirect electron mobility from the valence to the conduction band) in a semiconductor is defined by the r value (equal to 1/2 or 2, for direct or indirect bandgap materials, respectively). transition. In other words, for our nanostructured systems, the electrons can be excited from the highest energy state in the valence band to the lowest level in the conduction band, with different momentum values. In this configuration, the electron mobility is facilitated by phonon assistance, which was detected and discussed for the MON samples in the Raman characterization. The E experimental values of the hybrid semiconductors were progressively decreased with the V5+ doping level increase (gap energies estimated at 3.00, 2.94 and 2.11 eV for TW, TWV3, and TWV5 samples, respectively), compared to the pristine TiO2 (a typical indirect bandgap semiconductor [44], with E= 3.2 eV).

The calculated mean sample diameters were 145.7 ± 47.0 nm ( n = 135 ) [20], 160.1 ± 74.1 nm (n=123), and 169.4 ± 63.1 nm (n=141), for TW, TWV3, and TWV5 MON, respectively. The equality of means tests results (n=3) demonstrate that there is no significant difference between the average particle size calculated for these produced

The bandgap energy of the MON semiconductors was calculated from the DRS data (Figure 6a), using the Tauc plot (Figure 6b). By the Tauc relation, the curve of the product of the absorption coefficient (α) and photon energy (E = ℎ) to the power of 1/r, (αhv)ଵ/୰, is plotted as a function of the photon energy (E). The intersection of the auxiliary line in the linearity region of the graph with the x axis represents the measurement of the material optical energy gap (E) [44]. Thus, the type of electronic transition (direct or indirect electron mobility from the valence to the conduction band) in a semiconductor is defined by the r value (equal to 1/2 or 2, for direct or indirect bandgap materials, re-

The diffuse reflectance data of all tested nanostructures were modeled by the Tauc relation with r=2, which indicates that the semiconductor excitation occurs by indirect

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MON (-value> α for all comparison of means).

spectively).

oxides.

**Figure 6.** (**a**) DRS data and (**b**) Tauc plot for bandgap measurements of the nanostructured metal **Figure 4.** (**a**) DRS data and (**b**) Tauc plot for bandgap measurements of the nanostructured metal oxides.

As verified, the progressive introduction of vanadium oxide to the TiO2/WO3 mixture (1/1 in mol) significantly decreased the TiO2 bandgap (3.20 eV to 2.11 eV). It is known that the presence of dopant ions in the system generates an extrinsic-type semiconductor (in which the bandgap can be controlled by purposefully adding impurities to the materials atomic structure). In the case of our nanostructures, the TiO2 (with tetravalent metal) is doped with The diffuse reflectance data of all tested nanostructures were modeled by the Tauc relation with r = 2, which indicates that the semiconductor excitation occurs by indirect transition. In other words, for our nanostructured systems, the electrons can be excited from the highest energy state in the valence band to the lowest level in the conduction band, with different momentum values. In this configuration, the electron mobility is facilitated by phonon assistance, which was detected and discussed for the MON samples in the Raman characterization.

Vହା ions (pentavalent elements), which will result in an n-type extrinsic semiconductor. The E<sup>g</sup> experimental values of the hybrid semiconductors were progressively decreased with the V 5+ doping level increase (gap energies estimated at 3.00, 2.94 and 2.11 eV for TW, TWV3, and TWV5 samples, respectively), compared to the pristine TiO<sup>2</sup> (a typical indirect bandgap semiconductor [44], with Eg= 3.2 eV).

As verified, the progressive introduction of vanadium oxide to the TiO2/WO<sup>3</sup> mixture (1/1 in mol) significantly decreased the TiO<sup>2</sup> bandgap (3.20 eV to 2.11 eV). It is known that the presence of dopant ions in the system generates an extrinsic-type semiconductor (in which the bandgap can be controlled by purposefully adding impurities to the materials atomic structure).

In the case of our nanostructures, the TiO<sup>2</sup> (with tetravalent metal) is doped with V 5+ ions (pentavalent elements), which will result in an n-type extrinsic semiconductor. In this case, free electrons are the main charge carriers, since each V <sup>5</sup><sup>+</sup> ion provides an additional electron to the system and thus the total number of electrons becomes greater than the number of holes. In this configuration, the added electrons tend to occupy additional energy levels in the bandgap region, very close to the bottom of conduction band (CB), called donor energy levels. Thus, it can be proposed from our results that the progressive increase in the concentration of vanadium in the nanostructures promoted a significant increase in the doping degree, with additional donor levels, which explains the decrease in the TiO<sup>2</sup> bandgap to 2.11 eV in the TWV5 nanocomposite.

In this sense, for the TWV5 system (with lower indirect bandgap), the electronic transition occurs with a lower photon energy linear, which makes it difficult for electron/hole recombination to occur, and consequently favors photocatalysis processes with visible light. The SEM images and EDS analysis of the MON-loaded fibers are shown in Figure 5. It is noted that there is a predominance of regular diameter fibers, without apparent surface defects, which proves that the parameters of the electrospinning process were properly chosen for the production of TWV3- and TWV5-loaded electrospun membranes The mean diameters of composite fibers were estimated as 5.4 ± 1.7 µm (n = 59) [22], 5.8±2.3 µm (n = 73), and 6.0 ± 1.9 µm (n=69), with a progressive increase in VଶOହ concentration. The population mean difference tests revealed that the MMO-loaded fibers have statistically similar mean diameters (n= 3 samples, -value > α). The EDS mapping and elemental composition of these composite fibers (Figure 7c) confirmed that the Ti, W, and V elements are distributed throughout the fibrous polymer membrane. In other words, the electrospun fiber matrix promotes the dispersion of

In this case, free electrons are the main charge carriers, since each Vହା ion provides an additional electron to the system and thus the total number of electrons becomes greater than the number of holes. In this configuration, the added electrons tend to occupy additional energy levels in the bandgap region, very close to the bottom of conduction band (CB), called donor energy levels. Thus, it can be proposed from our results that the progressive increase in the concentration of vanadium in the nanostructures promoted a significant increase in the doping degree, with additional donor levels, which explains

In this sense, for the TWV5 system (with lower indirect bandgap), the electronic transition occurs with a lower photon energy linear, which makes it difficult for electron/hole recombination to occur, and consequently favors photocatalysis processes with

The SEM images and EDS analysis of the MON-loaded fibers are shown in Figure 7. It is noted that there is a predominance of regular diameter fibers, without apparent surface defects, which proves that the parameters of the electrospinning process were properly chosen for the production of TWV3- and TWV5-loaded electrospun membranes

the decrease in the TiO2 bandgap to 2.11 eV in the TWV5 nanocomposite.

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(Figure 5a,b).

oxides, reducing the particle aggregation.

visible light.

(Figure 7a,b).

**Figure 7.** SEM micrographs of (**a**) TWV3 and (**b**) TWV5 MON-loaded electrospun fibers; (**c**) EDS mapping and elemental composition of V5+-doped samples, with indication of Ti, W, and V elements. **Figure 5.** SEM micrographs of (**a**) TWV3 and (**b**) TWV5 MON-loaded electrospun fibers; (**c**) EDS mapping and elemental composition of V 5+-doped samples, with indication of Ti, W, and V elements.

The mean diameters of composite fibers were estimated as 5.4 ± 1.7 µm (n = 59) [22], 5.8 ± 2.3 µm (n = 73), and 6.0 ± 1.9 µm (n = 69), with a progressive increase in V2O<sup>5</sup> concentration. The population mean difference tests revealed that the MMO-loaded fibers have statistically similar mean diameters (n = 3 samples, *p*-value > α).

The EDS mapping and elemental composition of these composite fibers (Figure 5c) confirmed that the Ti, W, and V elements are distributed throughout the fibrous polymer membrane. In other words, the electrospun fiber matrix promotes the dispersion of oxides, reducing the particle aggregation.

Thus, photocatalytic devices can be produced with better performance, due to the greater surface contact area of the MON, with the contaminated aqueous solution. In addition, the immobilization of MON in fibrous template allows the composite material reuse (without considerable material loss) in other photocatalysis cycles. Thus, electrospinning proves to be an effective and low-cost technique for producing potential composites for application in the decontamination of aqueous environments.

In summary, the similarity in morphology (particle size and fiber diameter) with increasing dopant concentration indicates that the better performance of these structures as a photocatalyst should predominantly refer to the interaction degree between the constituent oxides.

The DSC curves of the pristine fibrous membrane and the MON-loaded polymer fibers are given in Figure 6. In MON samples, two broad endotherm peaks are observed in the analyzed temperature range. The first one (centered at 75–90 ◦C) is assigned to the loss of water and the solvent remaining evaporation from the polymer electrospinning process [45,46]. loss of water and the solvent remaining evaporation from the polymer electrospinning process [45,46]. The second peak, centered at 231–234 °C, is related to the melting point of the polymer crystalline phase [46]. This peak is also described in the literature as the relaxation temperature of the polymer chains that follows the glass transition [47].

Thus, photocatalytic devices can be produced with better performance, due to the greater surface contact area of the MON, with the contaminated aqueous solution. In addition, the immobilization of MON in fibrous template allows the composite material reuse (without considerable material loss) in other photocatalysis cycles. Thus, electrospinning proves to be an effective and low-cost technique for producing potential com-

In summary, the similarity in morphology (particle size and fiber diameter) with increasing dopant concentration indicates that the better performance of these structures as a photocatalyst should predominantly refer to the interaction degree between the

The DSC curves of the pristine fibrous membrane and the MON−loaded polymer fibers are given in Figure 8. In MON samples, two broad endotherm peaks are observed in the analyzed temperature range. The first one (centered at 75–90 °C) is assigned to the

*Inorganics* **2022**, *10*, x FOR PEER REVIEW 11 of 18

posites for application in the decontamination of aqueous environments.

**Figure 8.** DSC curves of MON −supported fibers. **Figure 6.** DSC curves of MON-supported fibers.

In addition, the transition temperatures for the constituent oxides are detected at higher temperatures than those observed in the experiment. In resume, the introduction of semiconductors preserves the polymer melting point, without significant changes in The second peak, centered at 231–234 ◦C, is related to the melting point of the polymer crystalline phase [46]. This peak is also described in the literature as the relaxation temperature of the polymer chains that follows the glass transition [47].

the homogeneity and crystallinity degree of the composites. *3.2. Photocatalysis Tests*  During the experiment, aliquots of the RhB solution were removed from the reactor In addition, the transition temperatures for the constituent oxides are detected at higher temperatures than those observed in the experiment. In resume, the introduction of semiconductors preserves the polymer melting point, without significant changes in the homogeneity and crystallinity degree of the composites.

#### at defined time intervals so that variations in the intensity of the dye absorption peak (at *2.2. Photocatalysis Tests*

constituent oxides.

λ = 555 nm) (Figure 9a–c) could be investigated. The photodegradation kinetic curves of Rhodamine B (RhB) dye using MON−loaded fibers, under visible light excitation, are demonstrated in Figure 9d. In the graph, the y-axis represents the change in the relative concentration (C/C) of the dye, where C is the initial concentration and C is the re-During the experiment, aliquots of the RhB solution were removed from the reactor at defined time intervals so that variations in the intensity of the dye absorption peak (at λ = 555 nm) (Figure 7a–c) could be investigated. The photodegradation kinetic curves of Rhodamine B (RhB) dye using MON-loaded fibers, under visible light excitation, are demonstrated in Figure 7d. In the graph, the y-axis represents the change in the relative concentration (C/C0) of the dye, where C<sup>0</sup> is the initial concentration and C is the remaining concentration of the contaminant in the reactor (as a function of time). All samples were preserved in a dark environment in contact with the dye in solution for 1 h before exciting the oxides with continuous radiation.

The use of the fibrous membrane (without additives) in solution returned negligible variation in the initial concentration of RhB (1 µM) throughout the analyzed time interval. This proves that the polymer matrix acts as an inert support to prevent the particle aggregation, and provides a greater oxides surface area to interact with the contaminant.

The pristine TiO<sup>2</sup> nanopowder was used in the experimentation and has not demonstrated considerable photocatalytic action in visible light, since the energy of the incident light photons was not sufficient to overcome the anatase bandgap energy (3.2 eV) and promote electron/hole mobility, which is necessary for the dye degradation process to occur.

before exciting the oxides with continuous radiation.

maining concentration of the contaminant in the reactor (as a function of time). All samples were preserved in a dark environment in contact with the dye in solution for 1 h

**Figure 9.** Change in absorbance spectra of *RhB* dye, using (**a**) TW -, (**b**) TWV3 - and (**c**) TWV5-loaded fibers nanocomposites. (**d**) Dye photodegradation dynamics using MON-loaded fibers, under visible light excitation. The TiOଶ and TWV5 powders (with higher and lower bandgap, respectively) were also tested for comparison purposes. (**e**) Derivative of the relative **Figure 7.** Change in absorbance spectra of RhB dye, using (**a**) TW-, (**b**) TWV3- and (**c**) TWV5-loaded fibers nanocomposites. (**d**) Dye photodegradation dynamics using MON-loaded fibers, under visible light excitation. The TiO<sup>2</sup> and TWV5 powders (with higher and lower bandgap, respectively) were also tested for comparison purposes. (**e**) Derivative of the relative concentration of RhB with time. (**f**) Application of the pseudo-first-order kinetic model to the experimental data.

Differently, the MON supported in the fibers showed photocatalytic activity under the action of visible light (using a lower energy hv). The dye degradation percentage achieved after 120 min of visible light irradiation were 73%, 75%, and 92%, using TW- to TWV5-containing fibers, respectively.

The derivative of the relative concentration of RhB with time d(C/C0) dt (Figure 7e) showed that the greatest excursion in the rate of dye degradation, in the time interval of greatest decay of C, occurs with the use of fibers loaded with TWV5 nanostructures (followed by TWV3- and TW-loaded fibers samples, respectively), in a relationship directly proportional to the pollutant photodegradation kinetics.

For the studied metal oxide nanostructures, the RhB photodegradation kinetics was given in terms of the reaction rate coefficient (k), obtained from the application of the pseudo first order (PFO) model [48] to the experimental data. According to the model, k is equivalent to the value of the slope of the linear fit in the graph ln (C0/C) versus t (Figure 7f). In fact, the dye degradation process is well-fitted by PFO kinetics, since the correlation constants for the three MON were close to 1 (best fit results).

The values obtained for the reaction rate coefficient were 1.92 <sup>×</sup> <sup>10</sup>−<sup>2</sup> , 1.98 <sup>×</sup> <sup>10</sup>−<sup>2</sup> , and 2.83 <sup>×</sup> <sup>10</sup>−<sup>2</sup> min−<sup>1</sup> , using the samples TW-, TWV3-, and TWV5-loaded fibers. In other words, it was proven that the highest reaction rate was obtained with the sample with the highest concentration of vanadium.

Especially, the increase in the doping level provided a decrease in the TiO<sup>2</sup> bandgap (as discussed previously). This allowed the occurrence of free electrons in the conduction band and holes in the valence band, essential to the dye degradation reactions in solution.

The TWV5 powder was also tested and returned a percentage of degradation similar to the noted for TW and TWV3 nanostructures dispersed in the fibers. This demonstrates that the performance difference between the TWV5 powder and fiber-supported TWV5 forms is associated to the greater surface area of these MON induced by the high level of nanoparticles dispersion in the electrospun fibers. More specifically, at the atomic level, vanadium ion substituents induce stress on the TiO<sup>2</sup> (host metal oxide) crystal structure. This configuration results in the formation of a large amount of defects in its crystal lattice, providing superior chemical reactivity for photocatalysis processes.

Based on the values of optical bandgap energies and photodegradation results, we present a possible photocatalytic mechanism for the RhB degradation in water, using the TWV5-loaded fibers nanocomposites (illustrated in Figure 8). The authors suggest that the larger surface area of the V-doped TiO2/WO<sup>3</sup> (1/1 in mol) nanostructures (that is obtained with their dispersion in the fibers) induces more reactive sites for the photocatalytic reactions that occur on the surface of these semiconductors, promotes a lower probability of e−/h+ recombination, and enhances the charge transport [49]. In the illustrative scheme (Figure 8), the (V vs. NHE)-axis means the band potential versus normal hydrogen electrode scale [49]. The positions of the potentials of the TiO<sup>2</sup> and WO<sup>3</sup> band edges at pH 7.0 were given according to the literature [50]. Note that there is a difference in the edge positions of both oxides. This creates a potential gradient at the nanocomposite interface, which would facilitate the charge separation and inhibit the e−/h+ recombination [12,49,51].

The RhB photodegradation using TiO2/WO3-based nanocomposites typically involves the action of the hydroxyl (•OH) and superoxide (•O − 2 ) radicals [11,12,49,52]. The continuous incidence of visible light in the reactor environment generates available electrons and holes (hν → e <sup>−</sup> + h<sup>+</sup> ) in both WO<sup>3</sup> and V-doped TiO<sup>2</sup> oxides for the photocatalysis reactions.

Part of the photogenerated electrons also tend to be transferred from WO<sup>3</sup> to V-doped TiO2, due to the potential difference [53,54] (which is influenced by V donor levels below the TiO<sup>2</sup> CB, as previously discussed). Similarly, as the potential of the V-doped TiO<sup>2</sup> VB edge is more positive than that of WO3, it is suggested that the holes generated in the BV of the first oxide can also move into the BV of this last one. In summary, a hole can migrate to the semiconductor nanocomposite interface either directly or after their transfer from one oxide to another. These charge transfers in opposite directions can decrease recombination rates, in addition to promoting sufficient electron/hole separation for the photocatalysis

process to occur more efficiently [49,53]. Thus, the electrons and holes that reach the semiconductor-solution interface can react with the redox species O<sup>2</sup> and H2O and form the superoxide (•O − 2 , O<sup>2</sup> + e<sup>−</sup> → •O − 2 ) and hydroxyl (•OH, H2O + h<sup>+</sup> → •OH) radicals. The analysis of these processes indicates that these radicals and the photogenerated holes are the main agents of oxidation of the organic pollutant RhB into carbon dioxide and water. Thus, the best catalytic activity, obtained with TWV5-loaded fibers, stems from the combination of improved photoresponse and charge separation efficiency, and the presence of a higher active sites density of the hybrid nanostructures [55]. site interface, which would facilitate the charge separation and inhibit the e-/h+ recombination [12,49,51]. The RhB photodegradation using TiO2/WO3−based nanocomposites typically involves the action of the hydroxyl (•OH) and superoxide (•Oଶ ି) radicals [11,12,49,52]. The continuous incidence of visible light in the reactor environment generates available electrons and holes (hν → e− + h+) in both WO3 and V-doped TiO2 oxides for the photocatalysis reactions.

*Inorganics* **2022**, *10*, x FOR PEER REVIEW 14 of 18

**Figure 10.** Possible photocatalytic mechanism for the RhB degradation in water, using the TWV5-loaded fibers nanocomposites. **Figure 8.** Possible photocatalytic mechanism for the RhB degradation in water, using the TWV5 loaded fibers nanocomposites.

Part of the photogenerated electrons also tend to be transferred from WO3 to V-doped TiO2, due to the potential difference [53,54] (which is influenced by V donor levels below the TiO2 CB, as previously discussed). Similarly, as the potential of the V-doped TiO2 VB edge is more positive than that of WO3, it is suggested that the holes generated in the BV of the first oxide can also move into the BV of this last one. In sum-Based on these aspects, the TWV5-loaded fibers were reused in two new photodegradation cycles (Figure 9). The second cycle (Figure 9b) returned a percentage of RB dye degradation of 90% after 120 min of radiation incidence. In the third cycle (Figure 9c), the percentage of 85% was obtained, and with a slight decrease in the reaction rate, with degradation saturation after 140 min of exposure of the material to white light.

mary, a hole can migrate to the semiconductor nanocomposite interface either directly or after their transfer from one oxide to another. These charge transfers in opposite directions can decrease recombination rates, in addition to promoting sufficient electron/hole separation for the photocatalysis process to occur more efficiently [49,53]. Thus, the electrons and holes that reach the semiconductor-solution interface can react with the redox species O2 and H2O and form the superoxide (•Oଶ ି, O2 + e<sup>−</sup> → •Oଶ ି) and hydroxyl (•OH, H2O + h+ → •OH) radicals. The analysis of these processes indicates that these radicals The XRD spectrum of TWV5-loaded fibers (Figure 9d), after the third cycle of photodegradation, showed that all the characteristic peaks of TiO<sup>2</sup> and WO<sup>3</sup> (previously described in Figure 1) were preserved after the electrospinning processes and the photocatalysis cycles, with no phase change in the constituent oxides. It is important to highlight that the recyclability of the material is feasible due to the hydrophobic nature of the polymeric membrane and the maintenance of the MON photoactivity, without significant loss of the photocatalyst for reuse.

and the photogenerated holes are the main agents of oxidation of the organic pollutant RhB into carbon dioxide and water. Thus, the best catalytic activity, obtained with TWV5 −loaded fibers, stems from the combination of improved photoresponse and charge separation efficiency, and the presence of a higher active sites density of the hy-The photocatalysis process was discontinued with three cycles, since the polymer membrane showed imminence of mechanical wear (behavior expected by the acrylic nature of the polymer) caused by the handling and rearrangement of the material in the reactor during the preparation for its reuse.

brid nanostructures [55]. Based on these aspects, the TWV5 −loaded fibers were reused in two new photodegradation cycles (Figure 11). The second cycle (Figure 11b) returned a percentage of RB dye degradation of 90% after 120 min of radiation incidence. In the third cycle (Figure In summary, the increasing level of vanadium doping in the crystalline structure of TiO2, the smaller bandgap value given to the TWV5 nanostructures, associated with their greater surface area when dispersed in electrospun fibers, prove the best results of dye degradation obtained with visible light.

11c), the percentage of 85% was obtained, and with a slight decrease in the reaction rate, with degradation saturation after 140 min of exposure of the material to white light.

nificant loss of the photocatalyst for reuse.

reactor during the preparation for its reuse.

**Figure 11.** (**a**–**c**) Dye photodegradation cycles using TWV5-loaded fibers, under visible light excitation; (**d**) XRD spectrum of TWV5−loaded fibers, after the third cycle of photodegradation. **Figure 9.** (**a**–**c**) Dye photodegradation cycles using TWV5-loaded fibers, under visible light excitation; (**d**) XRD spectrum of TWV5-loaded fibers, after the third cycle of photodegradation.

The XRD spectrum of TWV5-loaded fibers (Figure 11d), after the third cycle of photodegradation, showed that all the characteristic peaks of TiO2 and WO3 (previously described in Figure 3) were preserved after the electrospinning processes and the photocatalysis cycles, with no phase change in the constituent oxides. It is important to highlight that the recyclability of the material is feasible due to the hydrophobic nature of the polymeric membrane and the maintenance of the MON photoactivity, without sig-

The photocatalysis process was discontinued with three cycles, since the polymer membrane showed imminence of mechanical wear (behavior expected by the acrylic nature of the polymer) caused by the handling and rearrangement of the material in the

#### In summary, the increasing level of vanadium doping in the crystalline structure of **3. Materials and Methods**

#### *3.1. Materials*

TiO2, the smaller bandgap value given to the TWV5 nanostructures, associated with their greater surface area when dispersed in electrospun fibers, prove the best results of dye degradation obtained with visible light. **4. Conclusions**  The main aim of the current research was to investigate the preparation of vanadium-doped TiO2/WO3 nanostructures supported on electrospun membranes, their mi-The chemicals titanium dioxide (anatase TiO2, 99.7% purity, <25 nm particle size, Sigma Aldrich, Burlington, VT, USA), tungsten trioxide (WO3, 99.9% purity, <100 nm particle size, Sigma Aldrich), vanadium pentoxide (V2O5, 99.9% purity, 80 nm particle size, Nanoshell, Layton, UT, USA), acrylic copolymer Eudragit® L100 (Evonik Industries, Essen, NW, Germany), ethanol PA (99.8%, Neon Comercial, Suzano, Brazil), and rhodamine B (Vetec, São Paulo, SP, Brazil) were used as received. All these reagents are analytically pure.

#### *3.2. Sample Preparation*

The material samples for the photocatalysis tests were prepared in two steps: (i) sintering of metal oxide nanocomposites (MON) and (ii) dispersion of MON in electrospun polymeric membrane. The tested MON configurations were defined as: TiO2/WO<sup>3</sup> (1/1 in mol, TW base sample); and TWV3 and TWV5 samples (TW mixture with 3 and 5 wt% of V2O5, respectively).

For the sintering process, each metal oxide mixture was sintered in a muffle oven at 500 ◦C for 2 h [22]. For the electrospinning process, 0.25 g of each sintered MON was mechanically dispersed in 4 mL of alcoholic solution (with a polymer concentration of 0.27 g/mL) and inserted into the reservoir of a conventional syringe (volume of 10 mL and 0.7 mm of diameter of the metal needle). Thus, simultaneously, a pressure of 100 µLmin−<sup>1</sup> on the syringe plunger and an electric potential difference (ddp) of 15 kV (applied to the tip of the metal capillary) promote the composite material to be electrospun towards a grounded plane metal collector (area of 0.1 <sup>×</sup> 0.1 m<sup>2</sup> , separated by 10 cm from the needle tip), with respective evaporation of the solvent. An illustration of the electrospinning process is shown in Figure 10a. The MON-contained fibrous membrane is then collected for the photocatalysis tests. *Inorganics* **2022**, *10*, x FOR PEER REVIEW 4 of 18 the needle tip), with respective evaporation of the solvent. An illustration of the electrospinning process is shown in Figure 1a. The MON-contained fibrous membrane is then collected for the photocatalysis tests.

**Figure 1.** Illustrative scheme of the (**a**) MON dispersed in electrospun fibers and their use in (**b**) photodegradation of the dye in aqueous solution. **Figure 10.** Illustrative scheme of the (**a**) MON dispersed in electrospun fibers and their use in (**b**) photodegradation of the dye in aqueous solution.

#### *2.3. Microstructural Characterization 3.3. Microstructural Characterization*

Japan).

*2.4. Photocatalysis Tests* 

The sample microstructure was investigated by: scanning electron microscopy (SEM) and energy-dispersive X-ray spectroscopy (EDS) with 10 to 20 kV accelerating voltage (Vega 3XM Tescan equipment, Tescan, Brno, Czech Republic); X-ray diffraction (XRD) in the 20– 60° range, scan rate of 0.02 °s−1 and Cu Kα radiation (Miniflex Rigaku equipment, Rigaku Corporation, Tokyo, Japan); Raman spectroscopy, excitation with = 532 nm laser, 20 − 25 mW (HORIBA Scientific, Osaka, Japan); differential scanning calorimetry (DSC), 30–300 °C range, nitrogen flow of 50 mLmin−1, heating temperature rate of 10 °Cmin−1 (Schimadzu DSC-60 equipment, Shimadzu Corporation, Kyoto, Japan); and UV–vis with diffuse reflectance spectroscopy (DRS), 200– 1400 nm wave-The sample microstructure was investigated by: scanning electron microscopy (SEM) and energy-dispersive X-ray spectroscopy (EDS) with 10 to 20 kV accelerating voltage (Vega 3XM Tescan equipment, Tescan, Brno, Czech Republic); X-ray diffraction (XRD) in the 20–60◦ range, scan rate of 0.02 ◦ s <sup>−</sup><sup>1</sup> and Cu Kα radiation (Miniflex Rigaku equipment, Rigaku Corporation, Tokyo, Japan); Raman spectroscopy, excitation with *λ* = 532 nm laser, 20–25 mW (HORIBA Scientific, Osaka, Japan); differential scanning calorimetry (DSC), 30–300 ◦C range, nitrogen flow of 50 mL min−<sup>1</sup> , heating temperature rate of 10 ◦C min−<sup>1</sup> (Schimadzu DSC-60 equipment, Shimadzu Corporation, Kyoto, Japan); and UV–vis with diffuse reflectance spectroscopy (DRS), 200–1400 nm wavelength range (Schimadzu UV-2600i spectrophotometer, Shimadzu Corporation, Kyoto, Japan).

length range (Schimadzu UV-2600i spectrophotometer, Shimadzu Corporation, Kyoto,

tion (neutral pH) (on a Hach DR 5000 UV-vis spectrophotometer, Hach Company, Ames, IA, USA), under the action of the *MON*-loaded fibers (19 mg) (scheme in Figure 1b). The photocatalysis tests were performed in a closed cubic box (volume of 40 cm3), equipped with lateral heat dissipating fans, reactor (capacity of 150 mL, placed on a magnetic stirrer and connected to a sample collection system), and light source (Figure 2a). The metal oxide nanostructures were activated by continuous white light (60 W power, 650 lm/m2 intensity, spectrum in Figure 2b). The solution in the reactor (surface top) was main-

#### *3.4. Photocatalysis Tests*

The temporal dynamics of the photocatalysis process was investigated from the variations in the UV-vis absorption of Rhodamine B dye (peak centered at 555 nm) solution (neutral pH) (on a Hach DR 5000 UV-vis spectrophotometer, Hach Company, Ames, IA, USA), under the action of the MON-loaded fibers (19 mg) (scheme in Figure 10b). The photocatalysis tests were performed in a closed cubic box (volume of 40 cm<sup>3</sup> ), equipped with lateral heat dissipating fans, reactor (capacity of 150 mL, placed on a magnetic stirrer and connected to a sample collection system), and light source (Figure 11a). The metal oxide nanostructures were activated by continuous white light (60 W power, 650 lm/m<sup>2</sup> intensity, spectrum in Figure 11b). The solution in the reactor (surface top) was maintained at 16.5 cm from the light source end. The reuse of composites in new photocatalysis cycles was possible by washing the material in aqueous solution (ultrapure water, neutral pH) under constant agitation for 3 h followed by drying in an oven at 40 ◦C for 12 h. All measurements were made in triplicate. *Inorganics* **2022**, *10*, x FOR PEER REVIEW 5 of 18 tained at 16.5 cm from the light source end. The reuse of composites in new photocatalysis cycles was possible by washing the material in aqueous solution (ultrapure water, neutral pH) under constant agitation for 3 h followed by drying in an oven at 40 °C for 12 h. All measurements were made in triplicate.

**Figure 2.** (**a**) Experimental apparatus for photocatalysis tests; (**b**) emission spectrum of white light applied during the photocatalysis experiments. **Figure 11.** (**a**) Experimental apparatus for photocatalysis tests; (**b**) emission spectrum of white light applied during the photocatalysis experiments.

#### *2.5. Statistical Analysis 3.5. Statistical Analysis*

The particles size, fibers diameter, and temporal dynamics of the dye photodegradation were given as an average of three independent measurements for each tested MON configuration. The normality and equality of means tests (95% confidence level, comparing the significance level (α) to the p-value returned by statistical tests) were performed as population statistics. The sample sizes (n) were obtained from SEM images using ImageJ software (National Institutes of Health, Bethesda, MD, USA). The particles size, fibers diameter, and temporal dynamics of the dye photodegradation were given as an average of three independent measurements for each tested MON configuration. The normality and equality of means tests (95% confidence level, comparing the significance level (α) to the p-value returned by statistical tests) were performed as population statistics. The sample sizes (n) were obtained from SEM images using ImageJ software (National Institutes of Health, Bethesda, MD, USA).

#### **3. Results and Discussion 4. Conclusions**

*3.1. Microstructural Analysis*  The XRD data of the TW, TWV3, and TWV5 MON are shown in Figure 3. The X-Pert HighScore software was used to identify the crystal phases of the studied materials. The crystallographic parameters were obtained from the International Center for Diffraction Data (ICDD). The tetragonal crystal phase of the anatase TiOଶ (a=b= 3.7821 Å, c = 9.5022 Å, and α = β = γ = 90° lattice constants [32], 01-071-1166 ICDD The main aim of the current research was to investigate the preparation of vanadiumdoped TiO2/WO<sup>3</sup> nanostructures supported on electrospun membranes, their microstructural characterization, and their potential application as photocatalysts. The planned MON-loaded fibers were successfully produced from the sintering and electrospinning processes. All composites showed photocatalytic activity in visible light, with better performance for the sample with 5 wt% of V2O5.

card) and monoclinic WOଷ (a = 7.306 Å, b = 7.540 Å, c = 7.692 Å, α = γ = 90° and β ് 90° [33], 01-083-0951 ICDD card) were detected by XRD measurements. This demonstrates that the oxide mixture sintering (with the selected parameters) has not resulted in a phase change or crystalline solid solution formation in the resulting *MON*. The saturation in the unit cell volume and crystallite size of TiO2, from the TWV3 to TWV5 sample, and the doping of TiO<sup>2</sup> (observed in the microstructural characterization) confirm that the best results of dye photodegradation, anotated for the TWV5-loaded fibers, are directly influenced by the higher doping level of V5+ ions in this system.

centrated in the region of 2θ = 20–35° [35]) were superimposed by the peaks of TiO2 and

All sintered oxide mixtures show similar values of WOଷ parameters, with a = 7.30 Å, b = 7.53 Å, c = 7.68 Å, α = γ = 90°, and β = 90.59°, with no changes in comparison

In addition, no diffraction peaks of VଶOହ were detected in the XRD spectra of the TWV3 and TWV5 composites, in comparison to the TW sample [34]. The V2O5 na-

WO3 (with higher intensities).

to lattice constants of the starting material.

In addition, the use of polymer matrix as a support for metal oxide nanostructures allowed the production of flexible devices, provided better photocatalytic performance of oxides and ease of removal of oxides from the aqueous environment, without significant loss of photocatalyst for reuse.

Based on the excellent results of photocatalysis using TWV5 nanostructures, the continuity of research involves the execution of other important experiments to quantify parameters of the photodegradation mechanism of RhB (and other dyes) using these metal oxide nanocomposites, such as active species trapping and transient photocurrent test (evaluating the separation efficiency of charge carriers over the photocatalyst surface). Other perspectives involve the use of selective oxides as dopants (for example, Nb2O5, MoO<sup>3</sup> and In2O3); the improvement of the mechanical strength properties of the polymeric membrane that supports the MON nanostructures; development of the mechanical support apparatus for tests with the photocatalyst in an environment with larger proportions; and use of these nanostructured devices in other chemical decontamination processes.

**Author Contributions:** Sample preparation and characterization, M.F.G.P., M.M.N., P.H.N.C., C.Y.B.O., G.F.T. and E.S.A. Writing, editing, and review, M.F.G.P., C.Y.B.O. and E.S.A. All authors have read and agreed to the published version of the manuscript.

**Funding:** This research was funded by Conselho Nacional de Desenvolvimento Científico e Tecnológico (CNPq, Project 202451/2015-1), Fundação de Amparo à Pesquisa do Estado da Bahia (FAPESB, Project 1252/2018) and Fundação de Amparo a Ciência e Tecnologia do Estado de Pernambuco (FACEPE, project IBPG-0849-3.03/2020) brazilian research agencies.

**Institutional Review Board Statement:** Not applicable.

**Informed Consent Statement:** Not applicable.

**Data Availability Statement:** Not applicable.

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

#### **References**

