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Structural and Functional Behaviour of Ce-Doped Wide-Bandgap Semiconductors for Photo-Catalytic Applications

CatMat Lab, Department of Molecular Sciences and Nanosystems, Ca’ Foscari University of Venice and Consortium INSTM RU Ve, via Torino 155, 30172 Venice, Italy
Department of Chemistry and NIS Interdept, University of Turin, and Consortium INSTM RU TO via Pietro Giuria 7, 10125 Turin, Italy
Department of Physics and Geologia, University of Perugia, via Pascolo 1, 06123 Perugia, Italy
Department of Physics and Earth Sciences, University of Ferrara, via G. Saragat 1, 44122 Ferrara, Italy
Author to whom correspondence should be addressed.
Catalysts 2021, 11(10), 1209;
Submission received: 28 July 2021 / Revised: 23 September 2021 / Accepted: 1 October 2021 / Published: 9 October 2021
(This article belongs to the Special Issue Women in Catalysts)


Increasing the photocatalytic efficiency of earth-abundant wide-bandgap semiconductors is of high interest for the development of cheap but effective light-driven chemical conversion processes. In this study, the coupling of ZnO and TiO2 with low contents of the rare-earth Ce species aimed to assess the photo-catalytic performance of the two semiconductors (SC). Structural and optical characterizations were performed to estimate the effect of the different interactions between Zn2+, Ti4+ and Ce4+ ions, and how the photo-responsive behaviour of Ce-Ti and Ce-Zn composites was affected. Therefore, photo-catalytic tests were performed for all Ce-modified SC to assess both their photo-oxidative and photo-reductive properties. Amongst all the tested materials, only Zn-based samples resulted in being suitable for the photo-oxidation of the methylene blue (MB) organic pollutant in a synthetic-dependent fashion.

1. Introduction

Since it was first introduced, the light-mediated catalytic conversion of many organic and inorganic molecules—also referred as photocatalysis—has become increasingly attractive, especially in the context of energy transition [1]. Therein, photocatalysis was widely employed for both photo-oxidation, such as photo-degradation of water pollutants, and photo-reductive reactions, such as the CO2 reduction or H2 production from water splitting [2], which were extensively studied mainly in wide-bandgap semiconductors [1,3]. In this context, photocatalysis refers to the ability of a semiconductor (SC) to employ the energy of incident photons to form new chemical bonds in a chemical redox reaction via electrons or holes transfer. In fact, when the energy of photons is equal or greater than the semiconductor’s bandgap, an electron-hole pair is generated, which can either recombine or transfer to an acceptor molecule, thereby initiating the oxidizing or reducing process [3].
An effective light-to-chemical conversion generally relies on both charge transfer and charge mobility, which in turn, may be affected by several factors, such as electron mobility, recombination rate and defects density in the material [3,4]. In addition, when dealing with heterogeneous catalysis, either in gaseous or liquid media, other parameters become relevant for the catalytic performance, including the mass, the surface area and presence of active sites of the catalyst, the wavelength employed, the initial concentration of the contaminant, the temperature and the pressure of oxygen, if present [5].
The application of SCs, such as TiO2, ZnO, CeO2, or CdS, as well as many others, for the treatment of air pollutants has been proposed and studied for both outdoor and indoor applications for the photocatalytic oxidation of VOCs, NOx, SOx, CO, and other organic molecules, as well as in the photoreduction of CO2 and H2O [1,5,6].
The employment of TiO2 and ZnO-based catalysts was widely addressed for their non-toxicity, availability and low cost, with a focus on TiO2, regarding its photochemical stability and high photoactivity [1,6]. TiO2 is an n-type and indirect band-gap semiconductor with unique scattering properties [7]. It is present in four different crystallographic phases, namely rutile (tetragonal), anatase (tetragonal), brookite (orthorhombic) and TiO2-B (monoclinic) [3]. Rutile and anatase phases consist of octahedrons, in which each Ti atom is surrounded by six oxygen atoms, whose structure is differently organised according to the phase. The two polymorphs were mostly investigated for their photocatalytic activity, owing to the inter-band transition occurring with energies belonging to the near UV region [8]. Thermal stability, recombination rate, and charge mobility are also different in the two polymorphs, with anatase showing a lower thermal stability, but also a lower recombination rate [8].
ZnO is a direct bandgap, II-VI semiconductor with each atom spatially organized to form a tetrahedron, binding by turn four other atoms, and wurtzite being the phase most commonly stable at atmospheric pressure conditions [9]. Together with a slightly broader bandgap, the higher electron mobility and exciton binding energy of ZnO results in a lower recombination rate and suggests a greater photocatalytic potential when compared to TiO2 [9]. Nanostructured ZnO has been mainly employed for photo-driven oxidative reactions, such as pollutants or dye degradation in water [10,11], but also as a anti-microbial and anti-cancer agent, owing to reported cytotoxic properties [12]. Nevertheless, the role of ZnO as a promising photocatalyst is currently mainly limited by photo-corrosion upon UV-light exposure and absorption in only the UV region of the sun light spectrum [10].
The introduction of lanthanides Ln3+—also known as rare-earths—such as La3+, Eu3+, Pr3+, Nd3+ and Sm3+ in TiO2 semiconductor was reported to increase the adsorption of organic molecules, and proposed to improve both the photocurrent response, the UV incident photon to current conversion and the photocatalytic removal of organic air pollutants [13,14]. All these features were mainly attributed to increased specific surface, formation of mixed oxides and SC heterojunctions, and the presence and amount of Ti3+ recombination centres [14]. In this regard, the introduction of CeO2 in either TiO2 or ZnO-based materials, to form CeO2/TiO2 or CeO2/ZnO-mixed oxides composites, was also shown to reduce the bandgap, thereby also promoting a visible light-driven degradation of organic compounds, the latter also depending on Ce/Ti and Ce/Zn molar ratios [13,15]. Cerium is the most abundant rare-earth element [16], mainly present as CeO2 with a cubic fluorite and Ce2O3 with a hexagonal structure [17], and characterized by non-toxicity, high UV-extinction coefficient and oxygen storage ability, according to its chemical potential, previously related to the co-existence of both Ce3+ and Ce4+ oxidation states in the same material [18], with Ce3+ species being mainly localized at the surface [19].
The band gap of bulk CeO2 was reported to be ~ 3.2 eV, for which the O-2p to Ce-4f transition accounts, and to increase by decreasing the particle size, due to both a quantum confinement and a cluster effect [20]. However, the band gap was elsewhere reported as ~ 2.8 eV and potentially related to the stoichiometric ratio between CeO2 and Ce2O3 oxides [19].
CeO2 is broadly employed as a polishing agent and a glass constituent [16], while nanostructured CeO2 has been mainly proposed as a UV-filter, as a reactive oxygen species (ROS) inactivator, or for drug delivery purposes in biological systems, although its photocatalytic activity has also been proven [21].
For instance, CeO2-ZnO composites showed increased photocatalytic activity compared to bare ZnO, CeO2 and TiO2 in the photo-degradation of water pollutants under visible [13,22] or UV light [23]. Notably, the CeO2/ZnO oxides ratio was related to the presence of defects and heterojunctions, which were suggested to decrease the electron-hole pairs recombination rate, improve the stability [13], and modify the adsorbing properties of the material [24,25]. Metal-doped CeO2 showed high photocatalytic and supercapacitor properties when used as a photoelectrode [26]. Similarly, CeO2/ZnO systems were also employed as photoanodes and proposed for the electro-detection of organic molecules [13]. Nevertheless, still little is known about the employment of such composites in the photo-degradation of water pollutants, as well as CO2 photoreduction, although porous CeO2/ZnO binary oxides were reported for the photo-oxidation of CO [27]. Conversely, CeO2-TiO2 systems were successfully employed to photo-convert gaseous CO2 into CH3OH [17], as well as for the photo-degradation of organic pollutants using UV and visible light [15,28]. Moreover, CeO2-TiO2 mixed systems loaded with Pt or Au were reported for H2 production in the photo-driven H2O splitting upon visible and UV light exposure, respectively [29,30]. The presence of CeO2 was also found to improve the light-harvesting efficiency in TiO2-based dye-sensitized solar cells [31]. The aim of this study was to synthesize CeO2-TiO2 and CeO2-ZnO-mixed oxides by means of a co-precipitation method using two different precipitating agents, to investigate both the structural and optical effect due to the introduction of cerium species over the photo-catalytic performance of earth-abundant metal oxides. In particular, the purpose was to relate the effect of structural and optical properties of the composite materials to the photocatalytic activity. The materials were therefore tested for the H2O-mediated photoreduction of CO2 and for the photo-oxidation of a dye model pollutant methylene blue (MB) under UV light irradiation.

2. Results and Discussion

2.1. Photocatalytic Activity

The photo-driven reduction ability of CZ20, CCZ20 and CT20 was compared to a lab-prepared nanosized ZnO and a commercial TiO2 (P25, Evonik), and it is reported in Figure S1 of SI. Samples were tested in gas phase in a CO2-rich environment both to favour the production of CH4 over the side formation of H2 and to maximized CO2 availability [32]. Results showed no CO2 photo-driven conversion for any of the Ce-containing composites, while both bare ZnO and TiO2 were able to produce CH4 in the tested conditions (Figure S1 of SI). The photo-oxidative properties of the samples were tested on MB degradation tests. Samples were tested in aqueous medium without the addition of salts to avoid side effects and to provide model conditions, in order to highlight the performance of the catalysts and facilitate their comparison. When exposed to light, the mixed oxides samples CZ20 and CCZ20 showed an effective catalytic activity over 1 h. However, the latter was still lower than bare ZnO, as shown by the evolution of the relative concentration C/C0 in Figure 1. CCZ20 showed higher catalytic performance than CZ20, while CT20 showed no photo-oxidative activity in the tested conditions.

2.2. Effect of Ce-Doping on the Structure

The effect of cerium on the structure and morphology of TiO2 and ZnO semiconductors was investigated by PXRD, Raman spectroscopy, imaging and physisorption techniques, to correlate these properties to the photocatalytic performance of the materials.
XRD analysis of CCZ20 and CZ20 samples revealed the characteristic pattern of wurtzite, with a hexagonal unit cell [10], confirmed by the peaks located at 32.1 (010), 34.5 (002), 36.5 (011), 67.1 (020), 68.5 (112), 69.9 (021) (Figure 2), as well as the presence of cerianite as cubic fluorite, identified by the star in Figure 2, and confirmed by the broadening of the ZnO peaks at 2θ = 47.79° and at 2θ = 57.16°, as already reported [27]. The Rietveld analysis for CZ20 and CCZ20 revealed a difference in the crystallite size of zincite, found to be ~ 80 nm and ~ 20 nm respectively, and attributed to the employment of different precipitating agents. Therefore, the presence of smaller CeO2 cubic fluorite crystallites ( ~ 3 nm) dispersed in the ZnO structure (Figure 2) was hypothesized rather than the substitution of Ce4+ ions to the Zn2+ ones [33].
The CeO2 and TiO2 crystal patterns were not clearly detected after XRD analysis of CT20, which revealed an amorphous pattern characterized by a broad peak at 30° (Figure 3). Such an amorphous structure could partially explain the decrease of the catalytic activity of the material. The formation of cerium titanate CexTi(1-x)O2 in the TiO2 phase [28] was previously reported, as a result of the presence of a hetero-structure as a new phase, but no evidence of this phase is found in our sample.
Raman spectroscopy is an efficient tool for the structural characterization of SC. In the Raman spectra of CZ20 and CCZ20, it was possible to recognize signals of both components (Figure 4). The low-intensity band at 100 cm−1 is attributed to ZnO, whose characteristic pattern consisted of the two signals located at 100 cm−1 and 438 cm−1 [34], while the strong band at 460 cm−1 is attributed to ceria. The asymmetric broadening of this last band indicates the presence of small CeO2 nanoparticles dispersed in the ZnO structure [35], as hypnotised by XRD analysis. It can be notice that CZ20 has an intense fluorescence above 1000 cm−1, probably correlated with a higher concentration of defects, which are in turn responsible of the luminescence phenomenon, on smaller particles [36]. The sample CT20 also presents a very fluorescent Raman spectrum, and only a sharp signal at 140 cm−1 can be recognized. This strong signal is characteristic of anatase phase, typical of TiO2 (P25) (whose spectrum is shown in Figure 4), but due to the amorphous nature of our sample, could be better ascribed to Ti–O stretching mode. In this case, the luminescence of CT20 could be also correlated to the amorphous nature of the obtained small nanoparticles.
The N2 physisorption analysis showed an increase in surface area upon introduction of cerium. The BET-specific surface area of CCZ20 was both higher than bare ZnO and CZ20, as reported in Table 1. This difference was again attributed to the use of different precipitating agents. The sample CT20 showed a considerably higher specific surface area compared to the commercial standard (P25) one, as shown in Table 1. The isotherm of CCZ20 was found to be typical of macro-mesoporous materials and comparable to bare ZnO (Figure 5), while the type IV isotherms exhibited by CT20 indicated a clearly mesoporous profile with an average pore diameter of ~ 8 nm (Figure S3 in SI). Conversely, the small hysteresis in the CZ20 isotherm suggested a very low porosity of the composite material (Figure 5).
SEM analysis of ZnO showed nanostructured aggregates with variable sizes, ranging from 30 to 50 nm (Figure S2 of Supporting Information, SI).
The cerium-containing composites obtained via co-precipitation method are depicted in Figure 6a–f. CZ20 and CCZ20 showed a remarkable difference in size, morphology and roughness at low magnification (Figure 6a,c). The reported difference in crystallites dimension likely reflected the bigger size of CZ20 elongated structures, compared to the smaller spheroidal nano-sized particles of CCZ20, which showed instead an average diameter of 30 nm (Figure 6a–d). Similarly, the size of spheroidal CeO2-TiO2 NP, showing an average diameter of 12 nm, likely supported an amorphous structure as the possible result of the different ionic radius of Ce4+ and Ti4+ (Figure 6e,f) [37]. The decreased particle dimensions, were correlated to the increased surface area, as reported by N2 physisorption.
The morphological properties of the cerium-containing samples were mainly ascribed to the employed synthetic technique and to the different Zn or Ti interactions with Ce4+ ions, resulting in two different crystal structures. In fact, the different precipitation conditions may have affected the structural features of the samples, also resulting in the different catalytic activity of CCZ20 and CZ20, as well as of CT20. In particular, it is proposed that the presence of carbonate species favoured a slower precipitation of Ce4+ and Zn2+ ions, with the consequent stabilization of Ce-Zn composites with homogeneous size and structure, also reflected in the different zincite crystallite sizes of CZ20 and CCZ20. On the other hand, the introduction of Ce4+ ions in the TiO2 structure resulted in lattice distortion and consequent smaller nanoparticle size, contributing to the amorphous phase and owed to the relevant difference in the ionic radius of Ti4+ (0.61 Å), compared to both Ce4+ and Zn2+ ones, which exhibit larger radii as 0.87 Å and 0.74 Å, respectively [37].

2.3. Effect of Ce-Doping on the Functional and Optical Behaviour

To investigate the influence of structural differences highlighted on the sample reducibility, TPR analyses were resorted on.
The H2-TPR results of CCZ20 and CZ20 showed a pronounced peak between 400 °C and 500 °C (Figure 7), which differed from the latter as a possible result of different CeO2 crystallite size and distribution. The increased presence and stability of surface Ce4+ species were related to the peak between 500 °C and 600 °C in CZ20, as bare CeO2 reduction profile is typically characterized by two broad peaks between 400 °C and 600 °C and above 800 °C, attributed to surface and bulk Ce4+ to Ce3+ reduction, respectively [38]. Three main bands were detected in the CT20 reduction profile and attributed to a Ce-like and a Ti-like peak at 500 °C and 650 °C respectively, upon comparison with both bare CeO2 and TiO2 [39,40], and an intermediate component around 600 °C, attributed to the synergic interaction of Ce3+ and Ce4+ ions, with TiO2 in the amorphous phase.
The attenuated total reflectance (ATR) spectroscopy was performed to evaluate the possible presence of species adsorbed at the surface and spectra of bare and doped materials, as shown in Figure 8. In the spectra of all samples, there is a broad band in the 3500–3000 cm−1 spectral range, attributed to the surface adsorbed water and to—OH functional groups, both interacting by hydrogen bonds. The presence of the corresponding δ (HOH) bending mode at 1630 cm−1 indicates that undissociated water molecules are present into and on the surface of the materials. These signals are more intense for TiO2-based samples. The bands observed in the 1600–1200 cm−1 spectral region can be associated to adsorbed carbonates species [41,42], and are more intense for bare ZnO-based materials. For CT20 sample, the presence of two bands at 1570 cm−1 and 1350 cm−1, absent in the spectrum of bare TiO2, suggests an increased affinity for carbonates adsorption by the doped material, that could be related to increased basicity of the sample due to the presence of cerium. A similar behaviour was observed for CCZ20, whose spectrum shows two bands at 1570 and 1350 cm−1, more intense than those of bare ZnO. CZ20 showed a different behaviour: bands related to absorbed water are very low, and a very different pattern is observed in spectral range 1600–1200 cm−1. The intense signals at ≈2900 cm−1 are attributable to stretching modes of aliphatic groups (CHx), whose corresponding bending modes are detectable around 1500 cm−1, while below 1200 cm−1, there are signals ascribable to C–C stretching mode. As no templates were used in the synthetic procedure, it is possible that carbonaceous residuals were captured from the surrounding environment, including atmospheric CO2. The presence of surface-bound compounds could have reduced the hydrophilicity for CZ20 sample, thereby also affecting the photocatalytic activity. In fact, these features can limit the interaction with the medium and prevent the formation of reactive oxygen species, both in aqueous and gaseous media. Moreover, too strongly adsorbed C-based compounds could prevent the binding and release of the intermediate reagents, thereby affecting product formation, especially in the CO2 photo-reduction.
Therefore, to further elucidate the presence of surface-adsorbed compounds, temperature-programmed analysis was performed.
The result of the He-TPD analysis of samples is reported in Figure 9. The peak detected at 290 °C for ZnO was attributed to surface-adsorbed carbonates, as suggested by ATR analysis, released with the temperature increase [43]. The TPD of CT20 showed a similar peak at 310 °C, and two other detectable bands at 350 °C and 600 °C attributed to the release of adsorbed carbonates and to the temperature-dependent reduction of superficial Ce4+ state into Ce3+, with consequent O2 release. The band found at around 600 °C in CZ20 was related to the decomposition of organic residual, in accordance with FTIR results. Conversely, CCZ20 only showed a broad band above 700 °C, suggesting the possible presence of multiple adsorption sites with different binding affinity, as already suggested by ATR data.
Figure 10 shows the He-TPD of CT20 before and after exposure to CO2 gaseous pulses. The use of CO2 pulses aimed to identify and better discriminate amongst the potential CO2-binding sites in the materials, as observed in standard He-TPD (Figure 9).
The comparison of He-TPD (Figure 10a) and CO2-TPD (Figure 10b) showed an increase in the relative intensity of the peaks at 120 °C and 350 °C, which were therefore attributed to CO2 release. Notably, the detection of a band between 700 and 800 °C after exposure to CO2 suggested the presence of surface regions able to strongly bind the molecule. As a consequence, the band centred at 650 °C was ascribed to the reduction of Ce4+ to Ce3+ species, leading to O2 release, as already reported [38]. These results supported the overall increased affinity for CO2, owing to the increased basicity of the material, as expected by introducing CeO2 and, as suggested, by ATR spectroscopy.
The optical behaviour of the synthesized materials was further elucidated by diffused reflectance spectroscopy (DRS) and photo-luminescence (PL) analysis.
Results obtained by DRS were converted and plotted, as shown in Figure 11, using the Kubelka–Munk function F(R).
The DRS analysis of both CZ20 and CCZ20 showed a red shift of the absorption, indicated by the small tail in the visible region and attributed to the presence of CeO2, as already reported [34]. Conversely, DRS analysis of CT20 displayed a broader visible absorption band than bare TiO2 (P25, Evonik), which was related to the achievement of TiO2 band gap engineering, and was likely related to the formation of a CexTi1-xO2 mixed phase.
In the study, the optical properties were related to the bandgap evaluation, as reported in Table 2 and discussed in the Supporting Information File. In this case, m = 1 2 was used for ZnO [44], while the presence of indirect transitions was accounted for CeO2-TiO2 mixed oxide, as the optical behaviour may be different according to the crystal phase [45], and as no defined TiO2 phase was detected. Band gap evaluation supported the red shift detected by DRS analysis, reflected in the decrease of E g value for CT20, compared to bare TiO2. Conversely, CeO2 doping did not considerably affect the optical properties of ZnO, as also suggested by the Tauc plots (see Supporting Information). The Urbach plot (Figure S5 of the SI) was used to calculate the Urbach energy E U which has been previously used to estimate the density of electronic intra gap states in the materials [46]. Therefore, the increased value of E U for CZ20 and CCZ20 was related to increased number of intra gap states, when compared to pristine ZnO. The introduction of CeO2 considerably affected the E U value, thereby leading to a different distribution of states in the adsorption range, also according to the synthetic method employed. A similar modification of the Urbach energy was observed for CeO2-doped TiO2, although the Urbach rule is not always obeyed by amorphous materials [46].
PL analysis showed a remarkable difference in the photoluminescence profile of CZ20, when compared to CCZ20 and bare ZnO, both in visible and UV emission. As already reported for ZnO [47,48], the broad band centred at 610 nm detected for CZ20 was attributed to a defect-related emission, with the high intensity likely reflecting the different size of ZnO-based nanostructures compared to the other samples (Figure 12). Besides the introduction of visible-emitting defects, it is also possible that the presence of surface-bound C-based compounds had a preferential passivating effect over the non-radiative emission upon recombination events. The low intensity band at around 430 nm for CT20 was attributed to the presence of CeO2, as similarly reported for bare CeO2 NPs [49], and this band was found to be red-shifted up to 460 nm for both CZ20 and CCZ20 (Figure 12). The presence of surface-related defects, as suggested by the broad visible band of CZ20, was related to the lower oxidative ability of the sample, when compared to CCZ20. In fact, the presence of intra states defects can result in recombination events, affecting the charge transfer and therefore the surface-related photocatalytic activity, as already reported [50,51].

2.4. Relevant Parameters Influencing the Photo-Catalytic Performance

Crystallinity, intra-gap states distribution and reactant affinity were found to be relevant factors, all able to affect the overall light-responsiveness and redox properties of CeO2 composite materials.
The formation of an amorphous phase upon doping with CeO2 repressed the photo-catalytic activity. In fact, the lack of photo-catalytic activity of TiO2-CeO2 oxides composite (CT20) was mainly attributed to the presence of an amorphous phase, suggesting the role of crystal structure in surface-related charge transfer processes as well. Moreover, the suppression of the photo-reducing activity was observed, with increased binding affinity towards C-based reagents by the composite materials. The decreased photo-oxidative activity was both related to a partial modification of the band gap—whose shift in the visible likely decreased the energy available to the charge transfer to donor molecules—and to the presence of surface related defects. These results suggested the relevance of the optical properties of Ce-based materials in driving successful photon-activated reactions. In addition, surface hindering by C-based residuals could have prevented the formation of reactive oxygen species. Notably, the precipitation with different methods also led to different results. The co-precipitation with carbonates (CCZ20) resulted in a higher photo-catalytic activity—also owed to increased specific surface area and related to a decreased visible luminescence—when compared to the precipitation that occurred in the presence of sodium hydroxide (CZ20). The difference in the relative density of intra gap states observed was related to a difference in the photo-catalytic performance, possibly owed to the occurrence of recombination events.

3. Materials and Methods

3.1. Synthesis of the Materials

Synthesis of Nanoparticle (NPs) of ZnO and TiO2-Based Materials

All the ZnO- and TiO2-based materials were synthesized via wet chemistry precipitation method.
A 0.5 M aqueous solution of the metal precursors Zn(NO3)·6H2O and of cerium ammonium nitrate [CAN, Ce(NO3)6(NH4)2], was prepared using a Zn:Ce molar ratio of 4:1. By means of a peristaltic pump, the solution was progressively added to 200 mL of distilled water with simultaneous introduction of either a 1 M Na2CO3 or a 9 M NaOH solution, to keep the pH at 9. The white-yellowish solution was then aged under continuous stirring for 20 h at 60 °C. The obtained compound was filtered and washed with distilled water and dried for 18 h at 110 °C. Therefore, the samples were air-annealed at 400 °C for 4 h and labelled CCZ20 and CZ20 if precipitated with Na2CO3 or NaOH, respectively. Similarly, for the CeO2-TiO2 composites labelled CT20, a 0.4 M aqueous solution of TiO(SO4) × (H2O) and Ce(NO3)6(NH4)2 precursors was prepared using a Ti:Ce molar ratio of 4:1 using a 9 M NaOH as precipitating agent.

3.2. Photo-Catalytic Experiments

3.2.1. CO2 Photo-Conversion

The photo-conversion of CO2 occurred in a flat-bottom borosilicate glass photoreactor (volume 2.8 cm3 and exposed surface 7.5 cm2). The catalyst dispersed in ethanol (Merck Life Science S.r.l, Milan, Italy) was spread on the bottom reactor while heating at 150 °C to obtain a homogenous film, alternating spreading and heating cycles until complete depletion of the dispersion. The reactor was then installed into a lab-made gas line [32] equipped with heated piping and a bubbler, in which a 13.3 CO2/H2O reaction mixture was generated by bubbling a CO2 flow (99.9%) into the bubbler filled with milliQ H2O, kept at 40 °C and monitored until a constant composition was reached. The gas output was analysed through a gas chromatograph (GC, HP 6890) equipped with a thermo-conductivity detector (TCD) and a Porapak Q packed column (Figure 13). The reactions were run by locking the stabilized CO2/H2O gaseous mixture within the reaction and by irradiating it for 6 h. The UVA light was generated through a UV lamp (Helios Italquartz, Milan, Italy). The light intensities were kept at 60 W/m2. These values were controlled through a Delta Ohm HD 2302.0 photo-radiometer equipped with an LP 471 probe for UV (315-400 nm) light.

3.2.2. Photocatalytic Test for Methylene Blue Degradation

The amount of 10 mg of (0.05 M) either CZ20, CCZ20, or CT20 catalyst was dissolved in a 1·10−5 M methylene blue (MB) solution, with a pH of 7.6 under stirring conditions and exposed to a total of 60 min of dark before 1 h of light exposure with a UV Hg lamp at 365 nm wavelength. At different times, 2 mL aliquots were withdrawn, and the absorption was measured by a UV-Vis spectrophotometer (Cary5000, Agilent technologies, Milan, Italy).

3.3. Characterizations

3.3.1. Optical Characterization

Vibrational spectra were recorded on pure samples. ATR spectra were obtained with a Vertex 70 spectrophotometer (Bruker, Billerica, MA, USA) equipped with the Harrick MVP2 ATR cell, with resolution 4 cm−1. FT-Raman spectra were obtained with the same instrument equipped with the RAMII accessory, by exciting with a 1064 nm laser, with a resolution of 4 cm−1. Diffused reflectance spectra were measured with a Cary 5000 UV-Vis spectrophotometer (Agilent Technology). The Tauc plot was obtained and employed to evaluate the bandgap value of synthesized materials. Therefore, the evaluation of the bandgap value was obtained by plotting [ F ( R ) h v ] 1 m versus h v as according to Equation (1) and as previously suggested [52]
[ F ( R ) h v ] 1 m =   K ( h v E g )
In which F ( R ) is the Kubelka–Munk function, K is a constant characteristic of the material, h v is the energy of incident photons and E g is the bandgap. The value of m depends on the type of transition and represents m = 1 2 for direct and m = 2 for indirect allowed transitions.
The Urbach energy ( E U ) was obtained by the Urbach relation (Equation (2)), where f(R∞) is used instead of the optical absorption coefficient (α), h is the Plank constant (6.626∙10−34 J∙s), ν the photon frequency in s−1, α0 and E 0 are temperature-dependent constants.
f ( R ) = α 0 exp ( h v E 0 E U )
The EU is assessed from the near absorption-edge slope of ln(α) vs. [46].
Photoluminescence measurements were recorded at room temperature on powder samples using a Fluorolog F2Horiba/Jobin-Yvon spectrofluorometer (Horiba, Kyoto, Japan), with excitation at 320 nm or at 380 nm.

3.3.2. Structural Characterization

N2 Physisorption data were recorded using a Micromeritics TriStar II Plus analyser, recording the adsorption—desorption isotherms at −196 °C. All samples were previously pre-treated in vacuum at 200 °C for 2 h. Surface area information was taken in the 0.05–0.35 p/p0 range. Surface area was evaluated using the BET equation [53], while pore volume and pore size distribution on the desorption-branch isotherm using the BJH model [54]. X-ray diffraction (XRD) patterns were collected on a Bruker D8 Advance powder diffractometer with a sealed X-ray tube (copper anode; operating conditions, 40 kV and 40 mA) and a Si(Li) solid state detector (Sol-X) set to discriminate the Cu Kα radiation. Data scans were performed in the 2θ range 5–75° with 0.02° step size and counting times of 3 s/step. Quantitative phase analysis and crystallite size determination were performed using the Rietveld method, as implemented in the TOPAS v.4 program (Bruker AXS, Bruker, Billerica, MA, USA) using the fundamental parameters approach for line-profile fitting. The determination of the crystallite size was accomplished by the Double–Voigt approach and calculated as volume-weighted mean column heights based on integral breadths of peaks. Morphology and composition were examined by Field Emission Gun Electron Scanning Microscopy (FE-SEM) LEO 1525 ZEISS (Zeiss, Oberkochen, Germany), after metallization with chromium. Elemental composition and chemical mapping were determined using a Quantax EDSFT (Bruker, Billerica, MA, USA).

3.3.3. Temperature Programmed Analysis

Temperature programmed reduction (TPR) was performed on lab-made reaction equipment, placing 50 mg of samples into a U-shaped quartz reactor and heating from r.t. to 800 °C at 10 °C/min, in a 5% H2/Ar gas mixture (40 mL/min flow at STP). A MgClO4 trap was used to remove water from the outcoming flow, and the gas was analysed through a Gow-Mac TCD. He-TPD were performed with the same procedure using a pure He as carrier gas (40 mL/min at STP) instead, without the MgClO4 trap. CO2-TPD were performed similarly after pre-treating the sample in He flow (40 mL/min STP) at 110 °C for 1 h, to remove surface-adsorbed species. The sample was exposed to pure CO2 at r.t. in a sequence of pulses up to saturation. Finally, the sample was heated from r.t. to 800 °C at 10 °C/min in He flow, and the outcoming gases analysed without the MgClO4 trap.

4. Conclusions

In this study, we assessed the structural and optical modifications—as well as their effect on the photo-catalytic activity—of CeO2-doped wide band gap semiconductors. We concluded that the introduction of 20% mol Ce effects on the structural and optical behaviour was dependent on the semiconductor employed; either ZnO or TiO2. The lanthanide to metal interaction resulted in a consistent modification of TiO2 crystal structure, showing an amorphous phase, which also resulted in increased surface area and modified bandgap, as suggested by the enhanced visible light absorption. The presence of Ce in ZnO-based materials was mainly detected as cerianite nanocrystallites dispersed in the ZnO wurtzite crystal structure, associated to poor red shift in the light absorption and no bandgap modification. The synthesis of the composites using NaOH as a precipitating agent was also related to the detectable presence of surface-adsorbed carbonates. The employment of different precipitating agents was also reflected on the size and morphology of ZnO-based materials, as well as on the distribution and abundance of Ce4+ states in the material. The affinity for C-based compounds, resulting from the introduction of CeO2, together with the bandgap modification, was considered as the main limiting factor preventing the effective photo-catalytic conversion of CO2 by both CeO2-TiO2 and CeO2-ZnO composites. The decreased photo-degradation of MB was overall attributed to a decreased crystallinity, and to the presence of surface-related recombination events, together with a low photo-activity of CeO2 in the mild irradiating and temperature conditions employed.
In conclusion, CeO2-ZnO-mixed oxides resulted in being more appropriate for photo-oxidizing reactions compared with the photo reduction of CO2 in mild temperature and pressure conditions.

Supplementary Materials

The following are available online at, Figure S1: CO2 photoreduction, Figure S2: ZnO SEM, Figure S3: pore distribution, Figure S4: Tauc plot, Figure S5: Urbach plot.

Author Contributions

Conceptualization, G.F. And D.Z.; methodology, E.G., A.D.M., G.C. (Giuseppina Cerrato), G.C. (Giuseppe Cruciani) and A.G.; Data revision F.M. and M.S. All authors have read and agreed to the published version of the manuscript.


This research received no external funding.

Conflicts of Interest

The authors declare no conflict of interest.


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Figure 1. Time evolution of MB relative concentration C/C0 during the photo-catalytic tests of the composite samples under UV light irradiation.
Figure 1. Time evolution of MB relative concentration C/C0 during the photo-catalytic tests of the composite samples under UV light irradiation.
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Figure 2. XRD pattern of bare ZnO and CeO2-ZnO precipitated with carbonates (CCZ20) and NaOH (CZ20).
Figure 2. XRD pattern of bare ZnO and CeO2-ZnO precipitated with carbonates (CCZ20) and NaOH (CZ20).
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Figure 3. XRD Pattern of CT20. Blue and red lines show the cerianite-, cubic fluorite- and anatase-related crystallographic peaks.
Figure 3. XRD Pattern of CT20. Blue and red lines show the cerianite-, cubic fluorite- and anatase-related crystallographic peaks.
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Figure 4. Raman spectra of pristine and doped materials.
Figure 4. Raman spectra of pristine and doped materials.
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Figure 5. Comparison of N2 physisorption isotherms of (black) bare ZnO, (blue) P25, (black dash) CZ20, (black dot) CCZ20, and (blue dash) CT20.
Figure 5. Comparison of N2 physisorption isotherms of (black) bare ZnO, (blue) P25, (black dash) CZ20, (black dot) CCZ20, and (blue dash) CT20.
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Figure 6. SEM analysis of (a,b) CZ20, (c,d) CCZ20 and (e,f) CT20 showing different roughness and size; spheroidal particles of (d) 30 nm and (f) 12 nm average diameter for CCZ20 and CT20 clusters.
Figure 6. SEM analysis of (a,b) CZ20, (c,d) CCZ20 and (e,f) CT20 showing different roughness and size; spheroidal particles of (d) 30 nm and (f) 12 nm average diameter for CCZ20 and CT20 clusters.
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Figure 7. H2-TPR comparison of CCZ20, CCZ20 and CT20.
Figure 7. H2-TPR comparison of CCZ20, CCZ20 and CT20.
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Figure 8. ATR spectra in the spectral range 3800–1000 cm−1.
Figure 8. ATR spectra in the spectral range 3800–1000 cm−1.
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Figure 9. He-TPD of Ce-Zn composite.
Figure 9. He-TPD of Ce-Zn composite.
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Figure 10. He-TPD of CT20 (a) before and (b) after exposure to a CO2-rich environment for 1 h at room temperature.
Figure 10. He-TPD of CT20 (a) before and (b) after exposure to a CO2-rich environment for 1 h at room temperature.
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Figure 11. Kubelka–Munk function obtained by DRS analysis of Ce-doped samples.
Figure 11. Kubelka–Munk function obtained by DRS analysis of Ce-doped samples.
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Figure 12. Photoluminescence of Ce-Ti and Ce-Zn composites was measured with a laser excitation wavelength of 380 nm, while bare ZnO and TiO2 were investigated using a 320 nm laser source.
Figure 12. Photoluminescence of Ce-Ti and Ce-Zn composites was measured with a laser excitation wavelength of 380 nm, while bare ZnO and TiO2 were investigated using a 320 nm laser source.
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Figure 13. Lab-made gas line employed for the photo-catalytic experiment.
Figure 13. Lab-made gas line employed for the photo-catalytic experiment.
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Table 1. BET-specific surface area of bare and CeO2-doped samples.
Table 1. BET-specific surface area of bare and CeO2-doped samples.
SampleSpecific Surface Area (m2/g)
TiO2 (P25)50
Table 2. Calculated band gap values and Urbach energies obtained via Tauc plot and Urbach plot methods, respectively.
Table 2. Calculated band gap values and Urbach energies obtained via Tauc plot and Urbach plot methods, respectively.
Sample m E g   ( eV ) E U   ( eV )
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Forghieri, G.; Zanardo, D.; Ghedini, E.; Menegazzo, F.; Giordana, A.; Cerrato, G.; Di Michele, A.; Cruciani, G.; Signoretto, M. Structural and Functional Behaviour of Ce-Doped Wide-Bandgap Semiconductors for Photo-Catalytic Applications. Catalysts 2021, 11, 1209.

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Forghieri G, Zanardo D, Ghedini E, Menegazzo F, Giordana A, Cerrato G, Di Michele A, Cruciani G, Signoretto M. Structural and Functional Behaviour of Ce-Doped Wide-Bandgap Semiconductors for Photo-Catalytic Applications. Catalysts. 2021; 11(10):1209.

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Forghieri, Giulia, Danny Zanardo, Elena Ghedini, Federica Menegazzo, Alessia Giordana, Giuseppina Cerrato, Alessandro Di Michele, Giuseppe Cruciani, and Michela Signoretto. 2021. "Structural and Functional Behaviour of Ce-Doped Wide-Bandgap Semiconductors for Photo-Catalytic Applications" Catalysts 11, no. 10: 1209.

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