Scavenger-Supported Photocatalytic Evidence of an Extended Type I Electronic Structure of the TiO₂@Fe₂O₃ Interface

Abstract

Heterostructures of TiO₂@Fe₂O₃ with a specific electronic structure and morphology enable us to control the interfacial charge transport necessary for their efficient photocatalytic performance. In spite of the extensive research, there still remains a profound ambiguity as far as the band alignment at the interface of TiO₂@Fe₂O₃ is concerned. In this work, the extended type I heterojunction between anatase TiO₂ nanocrystals and α-Fe₂O₃ hematite nanograins is proposed. Experimental evidence supporting this conclusion is based on direct measurements such as optical spectroscopy, X-ray photoemission spectroscopy, scanning electron microscopy, high-resolution transmission electron microscopy (HRTEM), and the results of indirect studies of photocatalytic decomposition of rhodamine B (RhB) with selected scavengers of various active species of OH^•, h^•, e^–, and ^•O₂^–. The presence of small 6–8 nm Fe₂O₃ crystallites at the surface of TiO₂ has been confirmed in HRTEM images. Irregular 15–50 nm needle-like hematite grains could be observed in scanning electron micrographs. Substitutional incorporation of Fe³⁺ ions into the TiO₂ crystal lattice is predicted by a 0.16% decrease in lattice parameter a and a 0.08% change of c, as well as by a shift of the Raman E_g(1) peak from 143 cm^–1 in pure TiO₂ to 149 cm^–1 in Fe₂O₃-modified TiO₂. Analysis of O 1s XPS spectra corroborates this conclusion, indicating the formation of oxygen vacancies at the surface of titanium(IV) oxide. The presence of the Fe³⁺ impurity level in the forbidden band gap of TiO₂ is revealed by the 2.80 eV optical transition. The size effect is responsible for the absorption feature appearing at 2.48 eV. Increased photocatalytic activity within the visible range suggests that the electron transfer involves high energy levels of Fe₂O₃. Well-programed experiments with scavengers allow us to eliminate the less probable mechanisms of RhB photodecomposition and propose a band diagram of the TiO₂@Fe₂O₃ heterojunction.

1. Introduction

Although anatase TiO₂ and hematite Fe₂O₃ have been studied for many years, completely new effects arise when the combination of both oxides is used in catalysis,¹ photocatalysis,²⁻⁶ Li-ion batteries,^7,8 gas sensors,^9,10 and photoelectrochemical water splitting to generate green hydrogen.¹¹⁻¹³ When treated separately, each of the metal oxides mentioned above offers many attractive features but suffers from fundamental drawbacks as well.

Titanium dioxide is one of the semiconductors that are the most frequently encountered in photocatalysis,¹⁴ solar cells,¹⁵ self-cleaning coatings,¹⁶ and gas sensors¹⁷ due to its non-toxicity, chemical stability, abundance, and low cost. Nevertheless, its basic disadvantage is a wide band gap E_g of above 3.0 eV, resulting in high transparency to the visible range of the light spectrum. Numerous attempts have been made to engineer the TiO₂ band gap with the aim of reducing the separation between the edges of the valence and conduction bands or creating additional states in the forbidden band gap. However, the problem of better adaptation of the optical absorption of TiO₂ to the spectrum of the Sun has never found a satisfactory solution. All efforts, including doping, largely failed due to the development of undesirable recombination centers, inherent to this method of band gap modification.

In contrast to TiO₂, hematite Fe₂O₃ is a good representative of narrow-band-gap semiconductors (2.2 eV). Its absorption spectrum allows for efficient light harvesting within the visible range. Similarly to TiO₂, it is inexpensive and environmentally friendly.^18,19 However, fast recombination of charge carriers resulting from extremely short lifetimes of electron–hole pairs (<10 ps) and small diffusion lengths of holes (2–4 nm) inevitably contributes to the degradation of photocatalytic performance and the low efficiency of energy conversion processes. The low mobility of minority charge carriers and their limited diffusion length are considered responsible for the high surface and bulk recombination rates of charge carriers.²⁰ Therefore, the biggest challenge is to restrict the recombination of the photoexcited electron and holes in order to extend their lifetime to drive much slower photocatalytic processes at the surfaces and interfaces. One of the most efficient solutions to this problem is the creation of solid-state junctions.²¹

Metal oxide heterojunctions can be categorized into type I, II, and III depending on how the band edges of two semiconductors relate to one another.²² Moreover, different charge carrier transfer routes have been proposed, among which Z and S schemes are the most popular.^22,23

To take advantage of the best features of both oxides, TiO₂@Fe₂O₃ heterostructures have been studied as an alternative to improve the photocatalytic performance due to charge transfer phenomena across the interfaces.^8,24−26 Control over interfacial electronic transport is widely accepted as necessary to provide efficient operation of devices based on materials that contain numerous heterojunctions. However, to ensure the best photocatalytic decomposition of organic compounds, the type and electronic structure of the heterojunctions must be controlled as well as their morphology.

In fact, in the case of TiO₂@Fe₂O₃, there remains a profound ambiguity as far as the electronic structure and its type is concerned.²⁷⁻²⁹ One can find different models of the configuration of electronic bands that consequently predict various mechanisms of electron and hole separation.²¹ Research results in favor of the type I^27,30−33 and type II^{19,28,34−36} or that of the extended type I have been published.^4,29,37,38

Formation of a type I heterojunction, where the conduction band (CB) edge of TiO₂ is above the CB of Fe₂O₃ and the valence band (VB) edge of TiO₂ is below that of Fe₂O₃, has been proposed.^27,30−32 However, in this case, the photoelectrons and photoholes generated in TiO₂ upon UV radiation would transfer to the conduction and valence bands of Fe₂O₃, respectively, with no improvement toward suppression of the charge recombination. On the other hand, there are studies^{19,28,34−36} that conclude that a type II heterojunction is created, where electrons formed under visible light in Fe₂O₃ can be transferred to the CB of TiO₂.³⁹ However, there are also reports^4,29,37,38 in which it is accepted that although the TiO₂@Fe₂O₃ composite forms type I heterojunctions, it behaves favorably with respect to electron transfer. It is claimed that in CB_Fe2O3, higher levels exist to which the electrons can be transported. Higher levels in iron III oxide are located above CB_TiO2, so excited e^– can be injected to titanium dioxide. It should be mentioned that the type of band alignment in TiO₂@Fe₂O₃ has not been elucidated based on the direct experiments concerning the heterostructures. UV–vis spectroscopy, VB X-ray photoemission spectroscopy (XPS), and work function measurements as well as photocatalysis have been carried out individually on TiO₂ and Fe₂O₃. Therefore, the knowledge of the relative positions of the valence and conduction bands of these two materials is not explicitly supported by the experimental results.^30,35,38

Most of the studies²⁻⁶ on the photocatalytic behavior of heterostructures aim to improve the photodegradation rate. For example, Xia et al.² studied core–shell α-Fe₂O₃@TiO₂ nanocomposites prepared by the heteroepitaxial growth route and showed their improved photocatalytic activity toward the decomposition of rhodamine B (RhB) in the visible light region. Yao et al.³ have designed and fabricated Fe₂O₃–TiO₂ core–shell nanorod arrays using the glancing angle deposition technique (GLAD). These arrays have been shown to be more efficient for the degradation of methylene blue and the conversion of CO₂ under visible light illumination. Li et al.⁴ synthesized dendritic α-Fe₂O₃/TiO₂ nanocomposites for visible light degradation of eosin red, Congo red, methylene blue, and methyl orange. Huang et al.²⁹ demonstrated enhanced photocatalytic denitrification of pyridine over TiO₂/α-Fe₂O₃ nanocomposites under visible light irradiation. Mendiola-Alvarez et al.⁵ proposed a new P-doped Fe₂O₃–TiO₂ mixed oxide prepared by a microwave-assisted sol gel method for the photocatalytic degradation of sulfamethazine (SMTZ) with better efficiency within the visible range of the electromagnetic spectrum than that of unmodified Fe₂O₃–TiO₂ and TiO₂. Wannapop et al.⁶ studied the photocatalytic degradation of RhB on 1D TiO₂ nanorods synthesized by the hydrothermal method and decorated with Fe₂O₃. The level of degradation after 5 h increased from 30% for TiO₂ to 63% for the Fe₂O₃/TiO₂ heterostructure due to favorable charge transfer at the interface.

However, improvement in the photocatalytic activity is only the secondary aim of our current research. Determination of the type of the electronic structure of TiO₂@Fe₂O₃ should be considered as the primary motivation for this work. The novelty is based on the particular approach to this task, which consists in the application of photocatalysis with specific scavengers of OH^•, h^•, e^–, and ^•O₂^– as an experimental tool to draw conclusions regarding the CB and VB edge configuration.

In our previous paper,³³ we have proposed the formation of an intermediate layer of TiO₂:Fe as a consequence of Fe₂O₃ deposition on the surface of the TiO₂ nanocrystal. The incorporation of Fe³⁺ ions into the TiO₂ lattice is associated with the appearance of an additional acceptor level within the TiO₂ band gap.

In this work, the interface of a specific morphology has been engineered, and the correlation between morphological properties and electronic structure has been demonstrated for the first time. Direct measurements, such as optical spectroscopy, XPS, scanning electron microscopy (SEM), and high-resolution transmission electron microscopy (HRTEM), allowed us to draw conclusions regarding the electronic structure of the interface and its morphology. In addition, indirect studies based on the decomposition of the classical RhB model dye by TiO₂@Fe₂O₃ nanocrystals with and without selected scavengers of various active species have been carried out. A logical scheme has been proposed to eliminate the least probable decomposition routes. Knowledge of the possible mechanism of decomposition of a specific dye is believed to assist in drawing conclusions regarding the charge transfer mechanism at the TiO₂@Fe₂O₃ interface.

2. Experimental Section

2.1. Synthesis of TiO₂ Nanocrystals

A detailed description of the growth process of anatase nanocrystals has been presented in our previous article.³³ Briefly, the hydrothermal method was used to synthesize TiO₂ nanocrystals as a mixture of cubes and rods. Titanium tetraisopropoxide played the role of a titanium dioxide precursor, and diethanolamine acted as a shape-controlling agent. The prepared solution was heated to 215 °C for 24 h in a stainless-steel autoclave. The resulting precipitate was washed with 0.1 M HCl, distilled water, and ethanol and then dried and calcined at 500 °C for 3 h.

2.2. Formation of TiO₂@Fe₂O₃ Heterojunctions

The preparation conditions for particular TiO₂@Fe₂O₃ heterojunctions are given in Table 1. Typically, as described for the TiO₂@2%Fe₂O₃ sample, 75 ml of ammonium carbonate was poured into the beaker containing 0.75 g of TiO₂ anatase nanocrystals. During continuous stirring, 25.95 mL of iron(III) nitrate was added dropwise. Then, the temperature of the solution was increased to 70 °C to decompose ammonium carbonate into NH₃, CO₂, and H₂O. After 4 h, the beaker was covered with a watch glass and placed in the dryer for 18 h at 70 °C to complete the decomposition process. The ammonia formed during heating caused the pH of the mixture to increase, and an alkaline environment was obtained, resulting in the precipitation of iron(III) hydroxide Fe(OH)₃. The nanopowder was then collected by centrifugation and washed five times with a 0.5 %vol ammonia solution. The freshly prepared nanopowder was dispersed in isopropyl alcohol and dried at 70 °C for complete alcohol evaporation. To transform Fe(OH)₃ deposited on the TiO₂ surface into Fe₂O₃, it was necessary to carry out the calcination process at 500 °C for 2 h.

Table 1. Detailed Conditions of Material Preparation.

		Fe/(Fe + Ti) at. ratio [%]
sample	Fe(NO3)3a/TiO2 ratio ±0.2 [mL/g]	assumed	from EDX analysis
TiO2
TiO2@0.2%Fe2O3	3.46	0.239	0.61(2)
TiO2@1%Fe2O3	15.57	1.066	1.23(2)
TiO2@2%Fe2O3	34.60	2.339	3.28(2) (4.09(3))b
TiO2@10%Fe2O3	155.70	9.727	10.81(4)
TiO2@20%Fe2O3	346.00	19.320	25.49(4) (24.40(3))b

^aFe(NO₃)₃ concentration: 8.665(4)·10^–3 M, (NH₄)₂CO₃—saturated solution—100 mL per 1.000(1) g of TiO₂.

^bThe atomic Fe/(Fe + Ti) ratio [%] based on the XPS analysis.

2.3. Characterization

X-ray diffraction (XRD) was used to study the crystal structure of the obtained materials. Measurements were carried out within the 2θ range from 20 to 80° using an X’PertPro PANalytical diffractometer (Philips) equipped with a copper anode as a radiation source (K_α1 = 0.15406 nm). The HighScore Plus software and the PDF-2 database were applied for qualitative analysis. Quantitative analysis was performed using the Rietveld method. Supplementary conclusions concerning the phase structure were drawn on the basis of Raman spectroscopy. The Jobin-Yvon LabRam HR800 spectrometer, featuring a green laser (532 nm) and a diffraction grating of 1800 g/mm, was applied. The spectra were collected in a range of 1/λ from 80 to 800 cm^–1. A scanning electron microscope (Nova NanoSEM 200) equipped with an energy-dispersive X-ray (EDX) detector was used to calculate the Fe/(Fe + Ti) concentration. Furthermore, transmission electron microscopy (TEM) and HRTEM images were obtained using JEOL JEM-1011 and FEI Tecnai microscopes at accelerating voltages of 100 kV and 200 kV, respectively. Bright-field and high-angle annular dark-field scanning transmission electron microscopy (HAADF STEM) images were obtained in conjunction with EDX spectrum mapping to gain information on the microstructure of the TiO₂ and TiO₂@Fe₂O₃ materials. Digital Micrograph software was employed for analyzing the HRTEM images using fast Fourier transform (FFT) and inverse fast Fourier transform (IFFT) techniques, which allowed us to calculate the interplanar spacing of the observed phases.

The optical properties were determined from the total reflectance spectra R_tot(λ) recorded within the wavelength range of 220–2200 nm using the JASCO V-670 UV–VIS–NIR spectrophotometer equipped with an integrating sphere of 150 nm diameter. The energies of the optical transitions were established as corresponding to the maxima of a wavelength derivative dR_tot/dλ of the total reflectance coefficient with an uncertainty of 0.02 eV.

The chemical composition and electronic state of the ions at the surface were determined by XPS using a VSW spectrometer (Vacuum Systems Workshop Ltd.) with Al Kα radiation. The atomic ratio C_x of an element x on the surface was calculated as where A_x represents the peak area of element x and S_x is the normalized sensitivity for photoelectrons (S_Ti = 4.95 and S_Fe = 10.86).

2.4. Photocatalytic Activity

The photocatalytic activity toward the decomposition of RhB was studied under visible light (12 Philips TL 8W/54–7656 bulb lamps) for all materials obtained. Under typical conditions, 0.075 g of the photocatalyst was dispersed in 50 mL of RhB solution (5 × 10^–5 M). In some experiments, 1 mL of H₂O₂ (30%) was added to the solution and subjected to 30 min of stirring in the dark to achieve an equilibrium of adsorption–desorption, and 2 ml of the solution was collected and filtered. After a given time interval, other portions of the previously illuminated solution were removed and filtered. The UV–vis–NIR spectrophotometer, JASCO V-670, was used to measure the absorbance of the samples over the range 400–800 nm. Finally, the C/C_o ratio was calculated, where C is the concentration of RhB after a certain time of photocatalysis and C_o is the initial concentration of RhB determined for a wavelength equal to 554 nm.

To investigate the active species generated in the photocatalytic system (PS) consisting of a photocatalyst, RhB, and H₂O₂, scavenger experiments were performed. Ethylenediaminetetraacetic acid (EDTA-2Na, 10 mM), benzoquinone (p-BQ, 1 mM), AgNO₃ (100 mM), and tert-butyl alcohol (t-BuOH) (1:20 vol.) were used as scavengers introduced into the PS in the amount of 1 ml to capture holes (h^•), superoxide radicals (^•O₂^–), electrons (e^–), and hydroxyl radicals (OH^•), respectively.

Tests of cyclic photocatalysis were carried out using TiO₂@0.2%Fe₂O₃ and TiO₂@2%Fe₂O₃ heterostructures. After dark adsorption, a 90 min photocatalytic decomposition process of RhB was carried out and repeated four times. After each decomposition process, the photocatalyst was separated from the solution of RhB by centrifugation and washed with ethanol three times. After that, the powder was dried for 4 h at 70 °C and used again.

3. Results

3.1. Crystal Structure and Morphology

The presence of iron in the heterostructures was confirmed by EDX analysis (Figure S1a), and the iron contents are shown in Table 1. The crystal structure has been identified on the basis of XRD data and the use of the PDF-2 database. Analysis has shown that TiO₂ nanocrystals are single-phase and crystallize in a structure of anatase (JCPDS-ICDD #03-065-5714) (Figure 1) or contain traces of rutile (Figure S1b). In the case of Fe₂O₃, all peaks have been assigned to hematite α-Fe₂O₃ (JCPDS-ICDD #01-073-2234). For TiO₂@Fe₂O₃, the presence of secondary phase α-Fe₂O₃ has been confirmed only at the highest concentration of Fe³⁺ ions during preparation. At lower concentrations of Fe³⁺ ions, XRD has not revealed any evidence for the crystallization of iron oxides. Representative XRD patterns are included in Figure 1.

Figure 1.

XRD patterns of TiO₂ nanocrystals and TiO₂ nanocrystals covered with Fe₂O₃. The top bars represent the positions of the anatase peaks, while the bottom bars correspond to α-Fe₂O₃.

Depending on the electronegativity and ionic radius, metal ions can build into oxides either interstitionally or substitutionally. The ionic radius of the Fe³⁺ ion is equal to 0.064 nm and is slightly smaller than that of Ti⁴⁺ ion—0.068 nm, while the Pauling electronegativities of Fe³⁺ (1.83) and Ti⁴⁺ (1.54) are similar. It is, thus, likely that Fe³⁺ ions substitutionally occupy cationic Ti⁴⁺ sites in the TiO₂ lattice.⁴⁰ A distortion of the lattice would manifest itself by a decrease in the lattice parameters. As a result, the positions of all TiO₂:Fe diffraction peaks should shift to higher diffraction angles. This effect can be observed in the XRD pattern of TiO₂@20%Fe₂O₃ compared to that of TiO₂. On the basis of Rietveld analysis, the parameters of the unit cell have been calculated and found to be equal to a = b = 0.3791(1) nm, c = 0.9515(1) nm for TiO₂ and a = b = 0.3785(1) nm, c = 0.9507(1) nm for TiO₂@20%Fe₂O₃. The relative decrease in lattice parameter a is equal to 0.16% while that of parameter c is about 0.08%. This change indicates the incorporation of Fe³⁺ ions into the cationic sublattice of anatase.³³

The Raman spectra of the TiO₂, TiO₂@Fe₂O₃, and Fe₂O₃ nanocrystals are shown in Figure 2. A typical spectrum composed of five bands is observed for anatase TiO₂, while that of α-Fe₂O₃ contains six well-developed bands.⁴¹⁻⁴³ The positions of all Raman peaks are given in Table 2.

Figure 2.

Raman spectra of TiO₂, TiO₂@Fe₂O₃, and Fe₂O₃ nanomaterials.

Table 2. Raman Shift and Intensity of the Selected Bands for TiO₂, Fe₂O₃, and TiO₂@20%Fe₂O₃ Nanomaterials.

	Eg(1) of TiO2		A1g(1) of Fe2O3		Eg(2) of Fe2O3
sample	Raman shift [cm–1]	intensity [a.u.]	Raman shift [cm–1]	intensity [a.u.]	Raman shift [cm–1]	intensity [a.u.]
TiO2	143(1)	29041(5)
TiO2@20%Fe2O3	149(1)	6026(1)	214(1)	211(1)	284(1)	134(1)
Fe2O3			218(1)	177(1)	284(1)	131(1)

When considering TiO₂@Fe₂O₃, in addition to the bands that can be attributed to anatase, two surplus bands can be seen. The Raman shift corresponding to 213–223 cm^–1 is attributed to α-Fe₂O₃ A_1g(1).^42,43 Another band appearing at 284 cm^–1 can be attributed α-Fe₂O₃ E_g(2).⁴¹⁻⁴³ Substitutional incorporation of Fe⁺³ ions for Ti⁺⁴ cations, as determined by XRD data, is further supported by the change of the E_g(1) band from 143 cm^–1 (TiO₂ nanocrystals) to 149 cm^–1 (TiO₂@20%Fe₂O₃) with simultaneous reduction of band intensity by 79%, as shown in Table 2. It has been suggested⁴⁴ that the shift in the anatase E_g(1) Raman band is the result of lattice defects. TiO₂ doping with iron(III) ions was postulated in our previous paper³³ based on the spectrophotometric data.

TEM images provided information on the shape and size of the particles (Figure S2). Titanium dioxide nanocrystals form elongated rods ca. 230 nm long (Figure S2a). The analysis of TiO₂@Fe₂O₃ indicates that Fe₂O₃ forms a discontinuous layer of nanograins with a size of 15–50 nm at the surface of the TiO₂ nanocrystals (Figure S2b,c). In the case of TiO₂@2%Fe₂O₃, Fe₂O₃ crystals take a needle-like shape and grow only on certain walls of TiO₂ (Figure S2b).

EDX mapping and analysis of HRTEM images are shown in Figure 3. All IFFT calculations were performed after noise reduction using spots marked with a yellow circle in the FFT patterns. Then, masking was applied, and the resulting IFFT images presented the arrangement of crystallographic planes (black lines), which allowed the measurement of interplanar spacing.

Figure 3.

(a,b) EDX mapping images; (c,d) HRTEM images with FFT and IFFT analyses indicate the existence of the (101) plane of anatase TiO₂; (e,f) FFT of the purple/blue rectangle of the zoomed-in area shows an amorphous coating (TiO₂) or hematite nanoparticles of size 6–8 nm in the (104) plane of α-Fe₂O₃ (TiO₂@2%Fe₂O₃).

EDX spectrum mapping of the regions shown in HAADF STEM images (Figure 3a,b) was used to create maps of Ti, O, and Fe elements. These results reveal that in the case of TiO₂@2%Fe₂O₃, iron is distributed homogeneously (Figure 3b), and for the TiO₂@20%Fe₂O₃ sample, Fe₂O₃ grains of size tens of nanometers are also observed (Figure S3a).

Well-crystallized structures can be observed for all synthesized powders that are represented by the distinct spots on the FFT patterns. The green rectangles in Figures 3c,d, and S3b indicate the investigated area, the ROI (region of interest) of the FFT analysis. In each case, the spots obtained from the ROI correspond to an interplanar spacing of about 0.354 nm, which is well-correlated with the {101} plane of anatase TiO₂, the presence of which is also confirmed by XRD studies. However, the amorphous layer that was a part of the rod was observed at the surface of the TiO₂ nanocrystals (Figure 3e). Furthermore, in the HRTEM images of the TiO₂@2%Fe₂O₃ and TiO₂@20%Fe₂O₃ composites (Figures 3f and S3c), nanograins of size 6–8 nm deposited on the surface of the TiO₂ nanocrystals were found. To investigate their crystal structure, we performed the FFT analysis from the area in the blue rectangle, and then, the reverse FFT analysis was executed. The measured interplanar spacing was equal to 0.273 nm, which is close to the 0.270 nm lattice spacing of the {104} crystal planes of hematite.

3.2. Electronic Structure

The electronic structure of the components of the composite materials, such as TiO₂@Fe₂O₃, studied by XPS and optical spectrophotometry, plays a special role in the prediction of the character and type of the interface. Additional information about the interfacial charge transfer processes can be obtained from the carefully designed photocatalytic experiment. In this work, we have carried out a series of tests aimed at the photocatalytic degradation of the standard dye, that is, RhB, with and without certain scavengers. From the rates of decomposition of dye, conclusions about the probabilities of charge transfer processes can be drawn, which helps figure out the electronic structure of the interface.

Surface chemistry of the selected elements: Ti, O, and Fe, as well as surface defects, were studied by means of XPS. Figure 4 shows the high-resolution spectra of O1s, Ti2p, and Fe2p from the TiO₂ and TiO₂@2%Fe₂O₃ nanocrystals. XPS data concerning TiO₂@20%Fe₂O₃ nanocrystals with the highest amount of Fe₂O₃ are presented in Figure S4. The values of all binding energies determined by the fitting of the different XPS lines are given in Tables 3 and S1.

Figure 4.

Deconvolution of the O1s, Ti2p, and Fe2p XPS spectra of TiO₂ and TiO₂@2%Fe₂O₃ nanocrystals.

Table 3. Results of XPS Analysis of TiO₂ and TiO₂@2%Fe₂O₃ Nanocrystals—Assignment of Ti2p, O1s, and Fe2p peaks to Certain Types of Bonding.

	binding energy (eV)
symbol	TiO2	TiO2@2%Fe2O3	type of bonding	refs
Ti2p
TiI	458.2(3)	458.4(3)	Ti 2p3/2, O–Ti–O	[45]
TiII	463.8(3)	464.0(3)	Ti 2p1/2, O–Ti–O	[45]
TiI′	472.1(3)	472.2(3)	satellite of Ti2p3/2, O–Ti–O	[45]
TiII′	477.3(3)	477.6(3)	satellite of Ti2p1/2, O–Ti–O	[45]
O1s
OI	529.3(4)	529.3(4)	Ti–O–Ti	[46]
OII	530.6(4)	530.6(4)	oxygen vacancies or defects	[46]
OIII	532.7(4)	532.7(4)	chemisorbed species, e.g., OH–, H2O, O2–	[46]
Fe2p
FeI		710.6(7)	Fe 2p3/2, Fe3+ in Fe2O3	[47, 49]
FeII		715.2(8)	satellite of Fe 2p3/2, Fe3+ in Fe2O3	[47, 49]
FeIII		723.5(7)	Fe 2p1/2, Fe3+ in Fe2O3	[47, 49]
FeIV		728.4(7)	satellite of Fe 2p1/2, Fe3+ in Fe2O3	[47, 49]

The shape of the Ti2p XPS peak is complex in all samples. In the case of TiO₂, four components with the following binding energies 458.2 eV (Ti_I), 463.8 eV (Ti_II), 472.1 eV (Ti_I’), and 477.3 eV (Ti_II’) were fitted. The Ti2p_3/2–Ti2p_1/2 (Ti_I–Ti_II) doublet arises from spin orbit splitting and can be ascribed to Ti⁴⁺ ions in TiO₂ (titanium–oxygen–titanium bonding). The higher energies of 472.1 eV (Ti_I’) and 477.3 eV (Ti_II’) correspond to the satellite peaks of Ti2p_3/2 and Ti2p_1/2, respectively.⁴⁵ Upon covering TiO₂ nanocrystals with Fe₂O₃, the Ti2p XPS peaks shift slightly toward higher binding energies, and their exact positions depend on the amount of deposited Fe₂O₃, that is, the shift of 0.1–0.3 eV is observed at the lower amount of Fe₂O₃ (TiO₂@2%Fe₂O₃) while that of 0.6–1.0 eV at the higher amount of Fe₂O₃ (TiO₂@20%Fe₂O₃). The shift of these peaks indicates changes in the chemical environment of Ti⁴⁺ ions.

Analysis of the O1s peak reveals three components at 529.3 eV (O_I), 530.6 eV (O_II), and 532.7 eV (O_III). The lowest-energy O_I component is related to lattice oxygen O^2– in a fully coordinated position in the TiO₂ lattice (titanium–oxygen–titanium bonding). The highest-energy O_III component is associated with species, such as hydroxyl groups OH^–, water molecules H₂O, or dissociated oxygen O^2–, chemisorbed at the surface. The medium-energy O_II component, in agreement with reports in the literature,⁴⁶ can be attributed to the oxygen vacancy V_O in the titanium dioxide lattice. It should be noted that a small amount of Fe₂O₃ on the surface of TiO₂ does not cause any changes to the positions of the O1s peaks, while its high amount causes a shift of about 0.1–0.2 eV toward higher binding energies (Figure S4).

The Fe2p XPS peak has been fitted with four lines. In the case of TiO₂@2%Fe₂O₃, they are located at 710.6 eV (Fe_I), 715.2 eV (Fe_II), 723.5 eV (Fe_III), and 728.4 eV (Fe_IV). Two main Fe_I and Fe_III peaks correspond to Fe2p_3/2 and Fe2p_1/2 states, respectively, which shows that iron is present in the form of Fe³⁺ ions. The component denoted Fe_II has been assigned to the satellite of Fe2p_3/2 and to the satellite of Fe2p_1/2.⁴⁷⁻⁴⁹ At the highest amount of Fe₂O₃, not only an increased intensity of these peaks is observed but a shift of about 0.4–0.8 eV toward higher binding energies can also be seen (Figure S4). Quantitative analysis of XPS data indicates that the atomic fraction of iron reaches 4.1% in the case of lower (TiO₂@2%Fe₂O₃) and 24.4% for the highest amount of Fe₂O₃ (TiO₂@20%Fe₂O₃) at the surface of TiO₂ nanocrystals (Table 1).

Although the presence of iron oxide does not cause a drastic shift in the XPS peaks of O1s, it manifests itself quite differently. The deposition of Fe₂O₃ at the surface of TiO₂ nanocrystals leads to changes in the area under the O1s lines. In particular, the O_II component at the medium binding energy is affected. An increase in the amount of Fe₂O₃ deposited is accompanied by an increase in the fraction attributed to oxygen vacancies. For TiO₂ nanocrystals, the O_II fraction is equal to 34.4% and gradually increases to 38.2% for a low amount of Fe₂O₃ and up to 63.3% for a high amount of Fe₂O₃ on the surface of TiO₂. The increase in V_O contribution combined with the fact that the presence of a large amount of Fe₂O₃ results in a slight shift of the peaks can be treated as a proof of substitutional doping of Fe³⁺ into the titanium sublattice. The formation of oxygen vacancies at the surface of titanium dioxide can bring two additional electrons associated with one V_O. As a result, two Ti³⁺ ions can appear.⁴⁶

The comparison of the optical reflectance spectra of TiO₂ before and after being covered with Fe₂O₃ is presented in Figures 5a (0.2 and 2%) and S5 (1, 10, and 20%). Figures 5b and S5b demonstrate the first derivative spectra dR_tot/dλ of TiO₂, TiO₂@Fe₂O₃, and Fe₂O₃. All possible optical transitions are listed in Table S2 and shown schematically in Figure 5c.

Figure 5.

(a) Spectral dependence of the total optical reflectance R_tot, (b) first derivative spectra dR_tot/dλ of TiO₂@Fe₂O₃; hν—photon energy, and (c) diagrams of optical transitions in TiO₂ and α-Fe₂O₃.

In the case of pure TiO₂, the peak in dR_tot/dλ can be seen at 3.32 eV, corresponding to anatase (1a). The same peak appears in dR_tot/dλ of TiO₂@2%Fe₂O₃ at slightly different positions 3.43 eV (1a) due to the presence of iron oxide. Furthermore, four additional transitions have been identified for TiO₂@Fe₂O₃. Three of them have been assigned:

• (2) at 2.9 eV—level of Fe³⁺ impurity in the forbidden band of TiO₂,^50,51

• (4) at 2.2 eV—direct optical transition from the VB to CB in α-Fe₂O₃,

• (5) at 1.8 eV—indirect optical transition from the VB to CB in α-Fe₂O₃.⁵²

In addition, a fourth transition (3) at 2.5 eV has been observed in this work when the Fe/(Fe + Ti) atomic ratio exceeded 1%. The origin of this transition remained unclear for a long time until it was realized that it could be attributed to the size effect in Fe₂O₃.⁵³ For nanoparticles with a size decreasing from 120 nm to 7 nm, an increase in the band gap energy from 2.18 to 2.95 eV was demonstrated. This effect has been attributed to the size effect, which was accompanied by a modification of the hematite structure. Fondell et al.⁵² analyzed optical absorption as a function of film thickness for hematite. Two direct transitions were found at 2.15 and 2.45 eV, and they were blue-shifted by 0.3 and 0.45 eV, respectively, when the film thickness was decreased from 20 to 4 nm.

In the present work, structural studies do not show any evidence of phases other than α-Fe₂O₃ of iron oxide. TEM and HRTEM images for TiO₂@2%Fe₂O₃ and TiO₂@20%Fe₂O₃ composites (Figures 3, S2, and S4) confirm that iron oxide nanoparticles deposited at the surface of TiO₂ nanocrystals crystallize as α-Fe₂O₃. The combination of SEM and HRTEM studies indicates that the applied synthesis method produces relatively large 15–50 nm as well as very small 6–8 nm α-Fe₂O₃ nanoparticles on the surface of TiO₂. Therefore, we propose that the additional 2.48 eV optical transition is associated with the presence of small Fe₂O₃ nanoparticles.

3.3. Photocatalytic Degradation of RhB

RhB, as a model cationic aminoxanthene dye, is widely applied in the textile and color glass industry.⁹⁵⁴ Its structural formula is shown in Scheme 1.

Scheme 1. Structural Formula of RhB in (a) Open and (b) Closed Forms.

Efficient degradation of RhB is of upmost importance due to its high toxicity. There are many degradation schemes of RhB, one of them being laser cavitation.⁹⁵⁵ The N-de-ethylation and chromophore cleavage are two degradation pathways of RhB.

In this paper, we have undertaken photocatalytic methods of dye decomposition. Under the illumination of RhB, electron transitions occur due to the presence of orbitals: HOMO (the highest occupied molecular orbital) and LUMO (the lowest unoccupied molecular orbital). For RhB, the HOMO level is at −4.97 eV and the LUMO level is at −2.73 eV relative to vacuum, giving an energy gap of 2.23 eV.⁹⁵⁶

Photodegradation of RhB can proceed via three oxidation routes^54,55

1

2

3

To decide which of these three routes will play the most important role, one must consider the availability of active radicals: ^•O₂^– and ^•OH, as well as holes and electrons in the PS. Active species are formed in the interactions of electrons e^– and holes h^• with dissolved oxygen, water, and hydrogen peroxide, according to the following reactions:^56,57

4

5

6

In PSs containing metal oxide semiconductors, electrons and holes are provided by irradiation with photons of energy hν exceeding their band gap energy (hν ≥ E_g). Oxidation and reduction abilities of the photogenerated charge carriers depend not only on the band gap of a photocatalyst but also on the proper alignment of its conduction CB and VB edges with respect to the oxidation and reduction levels of active species, as shown in Figure 6. Therefore, from the photocatalytic performance of single semiconductors or their heterojunctions, one can draw conclusions concerning their electronic structure.

Figure 6.

Energy band diagram of pure TiO₂ and Fe₂O₃.

Stoichiometric TiO₂ is a wide-band semiconductor (E_g = 3.0–3.2 eV) with CB and VB edges properly aligned with respect to the levels of oxidation and reduction of active radicals. Electrons photoexcited to the CB and holes left in the VB as a result of UV light absorption in TiO₂ can participate in reactions (eq 4) and (eq 5). The reaction (eq 6) is also possible in the presence of H₂O₂. However, visible radiation will produce an effect only in the case of defects responsible for the introduction of additional levels in the forbidden band gap of TiO₂.

On the other hand, the lower band gap of Fe₂O₃ allows visible light to generate electrons and holes. However, since CB_Fe2O3 is located near the reduction potential of O₂/^•O₂^– (see Figure 6), electrons created under visible light in the CB of Fe₂O₃ can only reduce oxygen to superoxide radicals to a small extent.

Furthermore, the process described by eq 5 cannot occur in this oxide because its VB is above the water oxidation potential H₂O/^•OH, while reduction of hydrogen peroxide (eq 6) is possible due to the CB edges being above the H₂O₂/^•OH potential. For this reason, preliminary photocatalytic studies under visible light carried out without the addition of H₂O₂ showed that dye decomposition was negligible (Figure S6a,b).

The influence of H₂O₂ addition on RhB decomposition without a photocatalyst was also investigated in the system RhB + H₂O₂ + vis (Figure S6b). The results showed no negative impact of the additive, that is, no photolysis of H₂O₂ was observed. Therefore, the rest of the photocatalytic tests were performed with its addition.

The energy band diagram presented in Figure 6 corresponds to single pure photocatalysts of TiO₂ and Fe₂O₃ treated separately. To construct the corresponding electronic model of the interface between TiO₂ and Fe₂O₃, additional well-programed experiments with scavengers of the discussed radicals were performed, as illustrated in Figure 7. A drastic decrease in the photocatalytic activity after the addition of a specific scavenger indicates that the captured radicals are the main active species in the PS. In this paper, tert-butyl alcohol (t-BuOH), disodiumethylene diaminetetraacetate (EDTA-2Na), p-benzoquinone (p-BQ), and AgNO₃ were used as ^•OH, h^•, ^•O₂^–, and e^– scavengers, respectively.

Figure 7.

Schematic diagram showing the effect of the addition of particular scavengers on the mechanism of RhB decomposition.

The influence of scavengers on RhB decomposition is quite different for pure TiO₂ and Fe₂O₃. Figure 8 shows normalized dye degradation after 60 min from the addition of a specific scavenger in relation to degradation without its addition

7

Figure 8.

Effect of radical scavengers on RhB photocatalytic degradation on Fe₂O₃₂ (a) and TiO₂ (b) photocatalysts under visible light.

The abbreviation PC in Figures 8 and 9 denotes a normalized dye degradation without the addition of scavengers; therefore, it is always equal 100%. The photocatalytic activity of hematite nanoparticles does not change after the addition of a hole scavenger (EDTA-2Na) (Figure 8a), which is consistent with the statement discussed previously (Figure 6) that VB_Fe2O3 is above the oxidation potential of water (reaction I does not occur, see Figure 7). The abbreviation PC in Figures 8 and 9 denotes a normalized dye degradation without the addition of scavengers; therefore, it is always equal 100%. The photocatalytic activity of hematite nanoparticles does not change after the addition of a hole scavenger (EDTA-2Na) (Figure 8a), which is consistent with the statement discussed previously (Figure 6) that VB_Fe2O3 is above the oxidation potential of water (reaction I does not occur, see Figure 7). Furthermore, superoxide radicals have been shown to play a minor role in RhB decomposition as CB_Fe2O3 is located only slightly higher than the O₂/^•O₂^– potential, which does not allow electrons to completely reduce the dissolved oxygen in the dye solution (reaction II, see Figure 7). On the other hand, a high decrease in photoactivity is observed when e^– and OH^• are captured from the system. This shows that OH^• radicals, which are formed in reaction III, play a key role in the decomposition of RhB dye (see Figure 7). After the electrons are scavenged, the reduction of H₂O₂ to OH^• is stopped, and therefore, the photocatalytic process is slower.

Figure 9.

Effect of radical scavengers on RhB photocatalytic degradation on TiO₂@Fe₂O₃ photocatalysts under visible light: example kinetics of the dye decomposition on TiO₂@2%Fe₂O₃ (a) and normalized degradation of the dye on TiO₂@1%Fe₂O₃ (b), TiO₂@2%Fe₂O₃ (c), and TiO₂@10%Fe₂O₃ (d).

Different situations occur when we consider TiO₂ nanocrystals (Figure 8b). In this case, a decrease in the photocatalytic activity is observed after the addition of the e^–, h^•, and OH^• scavengers. This means that the main active species, as in the case of Fe₂O₃, are hydroxyl radicals, but originating from two different reactions. First, there is the reduction of hydrogen peroxide by electrons (reaction III, see Figure 7), and second, water is oxidized by holes (reaction I, see Figure 7). Moreover, the addition of the ^•O₂^– scavenger has little effect on photocatalysis as CB_TiO2 is located closely to the O₂/^•O₂ potential (Figure 6).

Additional changes occur in the case of a heterojunction composed of anatase nanocrystals covered with iron oxide nanoparticles (Figure 9). The p-BQ (^•O₂^–) scavenger slightly reduces the photoactivity of the tested materials. This means that in this case as well, superoxide radicals play a minor role in RhB photodegradation (Figure 9b–d). On the other hand, after scavenging the OH^• radicals and electrons from the system, a significant decrease in RhB decomposition was observed (inhibition of reaction III, see Figure 7) because the hydroxyl radicals from H₂O₂ reduction are the main active species in the decomposition of RhB. However, the most interesting effect was observed after the addition of a hole scavenger. It is assumed that the elimination of h^• from the system reduces the recombination rate, and thus, more electrons were able to reduce H₂O₂. Furthermore, it should be noted that the increase in photocatalytic activity after the addition of EDTA-2Na (h^•) is proportional to the amount of Fe₂O₃ in the heterojunction (1%—212, 2%—230, and 10%—325). The small amount of hematite (TiO₂@1%Fe₂O₃) is responsible for the low area of the TiO₂@Fe₂O₃ interface where recombination can occur. When this surface increases, the number of probable recombination sites also increases; therefore, effective scavenging of holes resulted in a high increase in photoactivity in the case of TiO₂@10%Fe₂O₃ (Figures 9d and S7).

As the stability of the photocatalysts is a very important issue for practical applications, the recyclability photocatalytic tests were performed. Two selected heterostructures were subjected to the RhB photodegradation in a sequence of four successive reactions (Figure S8). After the first cycle, the efficiency of photocatalysts decreases slightly; however, in the third and fourth cycles, it remains constant. This allows us to conclude that the obtained TiO₂@Fe₂O₃ heterostructures show stability in the cyclic photocatalytic process.

4. Discussion

Analysis of the spectral dependence of the absorption coefficient presented in Figures 5 and S5 shows that the presence of iron oxide Fe₂O₃ strongly modifies its shape and moves the fundamental absorption edge from UV toward the visible range. The characteristic energies of the optical transitions in TiO₂, Fe₂O₃, and TiO₂@Fe₂O₃ determined as the maxima in the first derivative of dR_tot/dλ are given in Table S2. The trivalent iron metal dopants Fe³⁺ can act as acceptors. The incorporation of Fe³⁺ into TiO₂ with an ionic radius (0.064 nm) smaller than that of Ti⁴⁺ (0.068 nm) can be expressed by the following reaction

8

Not only optical results but also the analysis of the XPS studies support the possibility of substitution of some amount of Fe³⁺ into the titanium sublattice as Fe_Ti^′. The energy difference ΔE between the band gap of TiO₂ nanocrystals (E_TiO2) and the acceptor doping level E_dop (Figure 10a) was calculated from the experimental data (Table S2) and is presented as a function of Fe/(Fe + Ti) in Figure 10b. The position of the iron Fe³⁺ level within the TiO₂ band gap varies with the increasing Fe₂O₃ concentration. As can be seen, the Fe acceptor level is located in the range of 0.3–0.5 eV above the top of VB_TiO2 depending on the concentration of the dopants. It is also affected by the microstructural properties of titanium dioxide, that is, the form of material (nanopowders and nanocrystals) and the type of synthesis of TiO₂@Fe₂O₃ heterojunctions.^33,53 This effect has also been demonstrated for TiO₂ modified with chromium Cr³⁺.⁵⁸

Figure 10.

(a) Energy difference ΔE between the TiO₂ nanocrystal band gap E_TiO2 and the acceptor doping level E_dop as a function of the Fe/(Fe + Ti) ratio obtained from EDX, our previous work,³³ and single-crystal data from ref (59), (b) acceptor level within the TiO₂ band structure caused by Fe³⁺ doping, (c) dependence of the band gap energy E_g on the particle size of the hematite (ref (53)), and (d) TiO₂@2%Fe₂O₃ nanostructure with different grain sizes of Fe₂O₃.

The simultaneous occurrence of direct and indirect optical transitions has been demonstrated for α-Fe₂O₃,⁵² as discussed in Section 3.2 of this work and illustrated in Figure 10c. The well-pronounced size effect has been reported by Chernyshova et al.⁵³ for direct optical transitions. The results of our studies regarding the absorption feature at 2.48 eV (3) indicate quite good correspondence with these observations (Figure 10c). This confirms that the size effect can be attributed to the presence of small 6–8 nm α-Fe₂O₃ nanograins, the evidence of which has been demonstrated by HRTEM.

The dye degradation (solid curves) presented in Figure 10d corresponds to the PS consisting of photocatalyst + RhB + H₂O₂. TiO₂@2%Fe₂O₃ with different iron(III) oxide grain sizes were used as photocatalysts. It was observed that the RhB concentration for the photocatalyst with Fe₂O₃ grains of a large size decreased to 85% after 60 min, but the highest changes equal to 70% were observed for the TiO₂@2%Fe₂O₃ heterojunction composed of both the large and small Fe₂O₃ grains after the same time. The explanation of this phenomenon is related to the different band structure at the interface caused by the different microstructure (see the explanation of Figure 11). Furthermore, when the hole scavenger was added (dashed lines, see Figure 10d), the decomposition accelerated due to the reduction of recombination at the TiO₂@Fe₂O₃ interface (from 70 to 30% in the case of TiO₂@2%Fe₂O₃).

Figure 11.

Proposed band diagram of the TiO₂@Fe₂O₃ heterojunction and electron as well as hole transfer routes between electronic states.

Based on the experimental results, including optical, structural, and electronic properties, as well as HRTEM imaging, it was possible to propose the energy diagrams of the TiO₂@Fe₂O₃ heterostructure presented in Figure 11 and the mechanism of RhB decomposition.

Covering of titanium dioxide with iron oxide is claimed to result in the formation of an additional acceptor level within the TiO₂ band gap. Upon visible light irradiation, generation of electron–hole pairs can occur in TiO₂ only when the acceptor level is activated (2.80 eV). Electrons excited from the Fe³⁺ level are transferred to the TiO₂ CB following the reaction: Fe³⁺ → Fe⁴⁺ + e’. Centers Fe⁴⁺ can be treated as Fe³⁺ ions with photoholes h^• located on them. The holes can move in the TiO₂ lattice by the hopping mechanism according to the reaction Fe⁴⁺ → Fe³⁺ + h^•. The position of the Fe acceptor level is below the water oxidation potential H₂O/^•OH, while water oxidizes to hydroxyl radicals (eq 5) and then ^•OH_(H2O) participates in RhB degradation (eq 2). However, it is a subsidiary reaction in this system.

In the previous work, hematite grains tens of nanometers in size, characterized by a direct band gap of 2.2 eV, formed at the TiO₂ surface, and the type I heterojunction was created (Figure 11a). Furthermore, in this work, the obtained TiO₂@Fe₂O₃ heterojunction possesses the same large Fe₂O₃ grains, but here, this interface has been carefully examined. In the type I heterojunction, the photoelectrons involved in the RhB decomposition originated from two sources. The first is the acceptor level formed in TiO₂, from which the excited e^– are transferred to the CB of TiO₂ and then to Fe₂O₃. The second are photoelectrons that form in the iron oxide (2.2 eV). Both participate in the reduction of hydrogen peroxide to OH^•, and a small part of them reduced O₂ to ^•O₂^–. As mentioned in Section 3.3, hydroxyl radicals are the main active species in RhB degradation.

The extended type I heterojunction is created because of an additional optical transition at a photon energy of 2.5 eV that originated from Fe₂O₃ nanoparticles with a size of several nanometers. Photoelectrons from high energy levels in iron(III) oxide are transferred to lower energy states in the CB of titanium dioxide through the interface. Then, together with the electrons from TiO₂, they reduce H₂O₂ to OH^•, which is the main route of the decomposition of RhB.

5. Conclusions

The TiO₂@Fe₂O₃ heterostructures composed of shape-controlled titanium dioxide nanocrystals covered with α-Fe₂O₃ nanoparticles have been successfully synthesized. The results of various characterization methods have shown that in addition to the presence of iron oxide nanoparticles on the surface of TiO₂, the TiO₂ lattice is substitutionally doped with Fe³⁺ ions, which is accompanied by the formation of oxygen vacancies. First, XPS studies of the O1peak have confirmed the existence of the component attributed to the oxygen vacancies V_O in the TiO₂ lattice. Furthermore, the formation of a thin, doped TiO₂:Fe layer has been found, manifested by the appearance of an additional acceptor level within the TiO₂ band gap. In terms of the microstructure, SEM analysis revealed α-Fe₂O₃ nanoparticles of different shapes agglomerated in irregular grains up to 100 nm in size. However, deposition on the surface of TiO₂ nanocrystals causes the crystallization of evenly distributed Fe₂O₃ nanoparticles with sizes several tens of nanometers (up to 50 nm from SEM) and a few nanometers (6–8 nm from HRTEM). The presence of Fe₂O₃ nanoparticles in TiO₂@Fe₂O₃ heterostructures has also been evident in UV–vis studies, which have also shown an additional optical transition attributed to the size effect of α-Fe₂O₃. The photocatalytic performance of the TiO₂ nanocrystals and heterostructures of TiO₂@Fe₂O₃ toward RhB decomposition and the detailed mechanism of this reaction have been investigated using relevant scavengers to determine active species in the system. In-depth analysis has allowed the indication of ^•OH hydroxyl radicals as the main active species responsible for the decomposition of RhB by TiO₂ nanocrystals, Fe₂O₃ nanoparticles, and TiO₂@Fe₂O₃ heterojunctions. On the basis of the experimental results and the relative band positions of the TiO₂@Fe₂O₃ materials, the mechanism of RhB degradation was proposed. Under visible light, in addition to Fe₂O₃, only the Fe³⁺ acceptor level within the TiO₂ band gap is active, and electron–hole pairs are created. Electrons excited from the Fe³⁺ acceptor level are transferred to the TiO₂ CB. Furthermore, the high energy levels located in the Fe₂O₃ CB associated with the optical transition are responsible for the electron transfer from CB_Fe2O3 to CB_TiO2. Therefore, all electrons in the TiO₂ CB participate in the formation of OH radicals in the reaction with H₂O₂, which is considered the most probable route of RhB decomposition. The proposed band diagram of the TiO₂@Fe₂O₃ heterojunction supports the hypothesis of an extended type I band configuration.

Supporting Information Available

The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acsami.2c06404.

• EDX analysis of chemical composition; XRD pattern of the TiO₂ nanocrystal; TEM images of the TiO₂@Fe₂O₃ heterostructure; EDX mapping and HRTEM images with FFT and IFFT analysis of the TiO₂@Fe₂O₃ heterostructure; XPS analysis of the TiO₂@Fe₂O₃ heterostructure; analysis of spectral dependence of total reflectance and optical transition energies of TiO₂ and the TiO₂@Fe₂O₃ heterostructure; analysis of photocatalytic decomposition of RhB dye under visible radiation, photocatalytic activity with and without the addition of H₂O₂ to the PS; dye degradation in the presence of scavenger of holes; and recycled photocatalytic decomposition process of RhB in the presence of TiO₂@Fe₂O₃ and H₂O₂ (PDF)

The authors declare no competing financial interest.