Characterization of Different Types of Screen-Printed Carbon Electrodes Modified Electrochemically by Ceria Coatings

1. Introduction

The creation of screen-printed carbon electrodes (SPCE) led to the essential improvement and expansion of their capabilities as highly sensitive electrochemical sensors (based on measuring various electrical signals - current, potential or resistance) three-electrode cells used for electro-analytical purposes. This achievement led to the fact that SPCEs form the basis of a significant part of modern stationary and portable analytical sensor systems operating on the principle of three-electrode cells. Among the most widely used substrate materials in the production of SPCEs are: graphite (C110), carbon nanotubes (CNT), carbon nanofibers (CNF), mesoporous carbon (MC) and graphene. The advantages of these carrier materials are related to their: highly developed effective working surface, a wide range of potentials in which parallel parasitic electrochemical reactions (typical for aqueous solutions) are not observed; high electrical conductivity, due to their electronic structure; relatively low price.

Single used electrochemical sensors (designed on the basis of SPCE), applied in the determination of traces of pollutants and/or toxic substances in environmental and biological samples, are also attractive from the point of view of the SPCE design. They can be modified in terms of the requirements for a specific analytes. Moreover, the chemical composition and surface structure of the SPCE can be easily changed, thanks to which more efficient solutions can be implemented in terms of the objects under study. In this regard, in recent years, interest in the development and application of more sensitive, specific, fast and precise analysis methods using screen-printed electrodes has been growing strongly [1,2]. They allow implementation of a large number of experiments using small amounts of consumables (samples and reagents) that do not require pre-treatment. Due to the high reproducibility that characterizes the sensors developed on their basis, they are suitable for a wide range of applications in areas such as: medicine, pharmacy, food industry, agriculture, environment and others. Significant advantages of electrochemical sensors based on SPCE are their simple and convenient application for in situ screening devices as well as their relatively low cost. In addition, the compactness of this type of electrochemical analyzers allows their easy portability.

It is known that a number of metal oxides, characterized by a specific structure and relatively low cost, can be applied in various types of sensor analytical systems [3]. At this it is shown that they increase the precision and effectivity of electrochemical analytical methods [4]. At this, it is shown that they increase the precision and effectiveness of electrochemical analytical methods [5]; biosensors [6], oxygen membrane systems and biotechnology [7,8]. The catalytic possibilities, biocompatibility, highly developed specific surface area and high ionic conductivity determine CeO₂ as suitable for the production of electrochemical sensor systems [5,9,10,11,12,13,14,15,16]. The results presented in the above-cited publications and the comments made in them in an indisputable way illustrate and convincingly confirm the qualities and catalytic capabilities of CeO₂.

In light of the above, the main goal of the present work have been to conduct studies aimed at modifying the surface of different screen printed carbon electrodes (C110, CNT, SWCNT, CNF and MC) with cerium oxide coatings of different composition and structure. For this purpose, an effective electrochemical technology were applied, allowing the deposition of defined mixed (Cе₂О₃+CeO₂) systems. In this study, the influence of: the type of carbon substrate; the concentration of Ce³⁺ ions in the working electrolytes; the cathodic current density and the hydrodynamic regime on the changes in the morphology, structure, chemical composition and chemical state of the elements of the thus formed and analyzed systems were studied. In a series of subsequent studies of the thus modified SPCEs, their catalytic, respectively sensor, capabilities will be illustrated.

2. Materials and Methods

The studies were carried out on five types of SPCEs purchased from Metrohm (Metrohm-DropSens Oviedo, Spain): graphite (С110), mesoporous carbon (MC), single-walled carbon nanotubes (SWCNT), multi-walled carbon nanotubes (CNT) and carbon nanofibres (CNF). The preliminary preparation of the SPCEs was carried out by a 20-minute treatment in isopropyl alcohol (Sigma-Aldrich, 99.5%), followed by washing in distilled water and finishing in abs. ethyl alcohol (99.9% ACS, ISO, Reag. Ph Eur). On the surface (0.126 cm²) of the so-called working electrode of SPCEs (representing in essence a three-electrode electrochemical cell [17] local electrochemical deposition of mixed Cе₂О₃+CeO₂ (island-like or dense) coatings was performed. For this purpose, a technology was applied (based on developed compositions and modes for electrochemical deposition), allowing the formation of cerium oxide coatings from non-aqueous solutions (based on absolute C₂H₅OH) [18,19,20,21,22,23,24,25,26,27,28]. In the present work, the influence of two non-aqueous electrolytes, differing in their concentration - 0.1 M CeCl₃x7H₂O and 0.3 M CeCl₃x7H₂O, was studied. Absolute C₂H₅OH was used as the solvent. Galvanostatic deposition of cerium oxide coatings on the studied working electrodes of SPCEs was performed in a three-electrode electrochemical cell using Gamry Interface 1000 potentiostat/galvanostat (United States of America) with a Silver/Silver chloride reference electrode Ag/AgCl (E _Ag/AgCl = +0.197 V vs. SHE) at two cathodic current densities (0.5 and 1 mA.cm^-2) and deposition times of 20, 40 and 80 min. As an Anod (centered around of the working electrode) was applied a bent Pt ring sheet (15х1х0.1 cm). The temperature of the working electrolytes was kept thermostatically at 15^oC. It was realized agitation of the applied electrolytes in the working cylindrical glass cell (volume 100 ml) by stirring at 400 rpm.

The surface morphology, structure and chemical composition in the bulk (in wt. %) of the studied systems (Cе₂О₃+CeO₂/С110; Cе₂О₃+CeO₂/МС; Cе₂О₃+CeO₂/SWCNT; Cе₂О₃+CeO₂/СNT; Cе₂О₃+CeO₂/CNF) were investigated by electron microscopy (JEOL JSM 6390, Tokyo, Japan) under the conditions of secondary electron image (SEM), back-scattered electrons (BEI) and characteristic energy dispersive X-rays analysis (EDS).

The formed phases in the same systems were observed by X-ray diffraction. XRD patterns were recorded on the multipurpose system Empyrean, manufactured by Malvern PANalytical (UK). The system was equipped with a copper anode X-ray tube and a PIXcel3D multifunction Hybrid Pixel Detector. The processing of the XRD patterns and the phase analysis were performed based on the Match! Program [29] and the free crystallographic database COD [30].

The XPS studies were performed in a VG Escalab II system, using AlKα radiation with an energy of 1486.6 eV. The chamber pressure was 1.10^-9 Torr. C1s line of adventitious carbon at 284.6 eV and Ce3d line of Ce⁴⁺ at 916.6 eV were used as internal standard to calibrate the binding energies of the spectra. The photoelectron spectra were corrected by subtracting a Shirley-type background and were quantified using the peak area and Scofield’s photo-ionization cross-section. The chemical composition (in at. %) and the oxidation state of the elements of cerium-based mixed (Cе₂О₃ + CeO₂) coatings deposited on C110, MC, SWCNT, CNT and CNF substrates were evaluated in 0.1 M CeCl₃x7H₂O and 0.3 M CeCl₃x7H₂O solution, according to the chosen regimes of electrodeposition. The accuracy of the BE measured was ± 0.2 eV.

3. Results

3.1. SEM and EDS investigations

Part of the obtained results characterizing the surface morphology, structure and chemical composition (SEM and EDS) of the mixed Ce₂O₃ + CeO₂ coated C110 samples are presented in Figure 1. The micrograph of C110, electrochemically treated for 20 min in 0.1 М CeCl₃x7H₂O (Figure 1a, 1000x), illustrates a highly developed, morphologically rough three-dimensional structure. It is dominated by the characteristic leaf-like elements of the C110 surface with sizes in the order of ~ 5 – 15 µm. At a magnification of 5000x (Fig.1b) of the same sample, sparsely spaced light sphere-like areas are observed, illustrating formed microagglomerates (with sizes ~ 30 – 200 nm, see the included inset obtained at magnification 20 000x) of mixed Cе₂О₃+CeO₂ (according to EDS analyses). Moreover, the number of agglomerates with smaller sizes is dominant. The samples obtained at the higher (0.3 M CeCl₃x7H₂O) concentration of Ce³⁺ in the working electrolyte are characterized in a similar way (Fig.1c,d). In Fig.1d (see the included inset) it is seen that at the higher concentration of Ce³⁺ ions in the working electrolyte, the number of formed cerium oxide agglomerates increases significantly. Under these preparation conditions, agglomerates with a size of ~120 nm are dominant. At the same time, the comparison of the registered values of the total Ce concentration, at the two concentrations of the working electrolyte, does not differ significantly. They vary in the intervals from ~ 1.7 wt. % for Fig. 1a to ~ 1.9 wt. % for Fig. 1c (see the included under the pictures data of EDS analysis illustrated chemical composition of the studied samples).

With increasing electrodeposition time, a gradual increase in the Ce concentration is recorded (up to ~ 3%, at 40 min of deposition, according to the data recorded in the work protocol). This increase becomes strongly pronounced at a deposition time of 80 min. Figure 2 presents the results obtained with the same compositions and electrodeposition time. They illustrate significant changes in the surface structure and composition of the studied systems. Compared to the deposition time of 20 min (Fig. 1), at which the concentration of deposited Ce is relatively low (~ 1.7 – 1.9 wt.%), after 80 min of electrodeposition duration it increases significantly (from ~ 8 to ~ 21 wt.%) – Figure 2. Moreover, it makes an impression that at the higher concentration of Ce³⁺ in the working electrolyte (0.3 M CeCl₃x7H₂O) the concentration of cerium in the deposited layers is lower (~ 8 % - Fig. 2 c, d), compared to the layers obtained in 0.1 M CeCl₃x7H₂O (~ 21 wt. % - Fig. 2 a, b). At the same time, with an increase in the concentration of cerium ions in the working electrolyte (from 0.1 to 0.3 M CeCl₃x7H₂O ), the sizes of the spheroidal cerium oxide agglomerates forming it decrease significantly, varying in the range of 10 – 100 nm – Fig. 2d. At an electrolyte concentration of 0.1 M CeCl₃x7H₂O these sizes reach ~ 1 µm – Fig. 2b. Obviously, the significantly larger spherical agglomerates presented in Fig. 2b, although fewer in number, include a significantly larger amount of cerium, compared to the micro-agglomerates registered in Fig. 2d. While at an electrolyte concentration of 0.3 M CeCl₃x7H₂O, this amount, or concentration, is about three times lower. At the same time, however, the specific surface area of many times the number of ceria nano-agglomerates (Fig.2d) exceeds their specific and effective (from a catalytic point of view) surface area by orders of magnitude. These results indicate that by varying the concentration of Ce³⁺ ions in the working electrolyte and the electrodeposition time of the ceria coating, the structure and specific catalytically active surface area of the modified SPCE C110 based on C110 substrate can be influenced in a certain way.

Based on the results presented above, when modifying the surface of SPCEs with a cerium oxide coating, in which the substrate material is: CNT, SWCNT, CNF or MC, the following electrodeposition modes were preferred and applied: current density i = 0.5 mA.cm^-2 and 1 mA.cm^-2; time of deposition τ = 40 and 80 min and agitation of the electrolytes at 400 rpm of the stirrer. The concentration of cerium ions in the working electrolyte was 0.1 M CeCl₃x7H₂O. The obtained results in a summarized form are presented in Figure 3, Figure 4, Figure 5 and Figure 6. These figures compare the SEM photographic images and EDS data (noted below the figures) of the cerium oxide-modified surfaces of C110, CNT, SWCNT, CNF and MC electrode substrates with the sequential increase in the change in cathodic current density and deposition time.

Based on the analysis of the results obtained, it was found that when applying:

• current density 0.5 mA.cm^-2 and electrodeposition time 40 min (Figure 3), the morphology and surface structure of the SPCEs treated in this way practically reproduce those of the untreated substrates. Interesting, in terms of the concentration of cerium oxide deposited on them, were established for: С110 (Се – 3.52%), CNT (Се – 3.17%) and SWCNT (Се – 6.07%). Although with a relatively lower concentration of cerium oxide registered on the CNF electrode (Се – 1.09%), it attracts attention with its highly developed surface morphology and structure. With a lower concentration of cerium (1.57%), in this mode, the MC system is also characterized;

• current density 0.5 mA.cm^-2 and electrodeposition time 80 min (Figure 4), the change in the morphology, structure and chemical composition of the surface of the such treated SPCE is drastic. The concentration of cerium in the deposited layer is: on C110 - 11.9%; on MC - 23.04%; on CNF - 56.11%; on CNT - 47.85% and on SWCNT - 48.06%. Accordingly, the modifying surface layer of cerium oxide on C110 is made up of uniformly dispersed spheroidal agglomerates with a diameter of ~ 0.05 – 0.2 µm. The surface cerium oxide layer formed on MC is made up of many times larger (diameter ~ 1 – 3 µm), densely arranged spheroidal agglomerates, containing cracks with a width of ~ 0.01 – 0.05 µm. The morphology and structure of the modified CNF are similar to MC, with fewer but wider cracks, reaching over 1 µm. The electrodeposited cerium oxide layer on the CNT is a dense and smooth coating containing regularly formed cracks with a width of ~ 0.1 – 0.5 µm. Similar conclusions are drawn for the modified SWCNT;

• registered differences may be related to the thicker cerium oxide coating deposited at the higher (1 mA.cm^-2) current density, evidence for which is the established higher cerium concentration in the studied SPCEs systems: at C110 (Ce – 3.49%), at MC (Ce – 8.63%), at CNF (Ce – 27.06%), at CNT (Ce – 17.8%) and at SWCNT (Ce – 31.23%);
• current density 1 mA.cm^-2 and electrodeposition time 80 min (Figure 6), the change in the morphology, structure and chemical composition of the SPCEs treated in this way is even more pronounced. The concentration of registered cerium is respectively: at С110 (Се – 65.47%), at МС (60.58%), at CNF (57.66%), at CNT (Се – 68.13%) and at SWCNT (Се – 69.55%). Accordingly, the modifying surface layer of cerium oxide on С110 is made up of a smooth, dense coating containing regularly formed cracks with a width of ~ 0.2 – 1.5 µm. Similar – dense and cracked – are the coatings also deposited on MC, CNT and SWCNT electrodes. Significantly different in its morphology and structure is the cerium oxide coating deposited on a CNF substrate. It is made up of spheres with a highly developed surface, the diameter of which varies in the range of ~ 1 – 7 µm.

3.2. XPS investigations

addition to the data presented and commented on above, it was necessary to conduct XPS studies. Through them (along with the established morphology, structure and chemical composition in the volume of the modified SPCEs) the chemical composition of the surface of the samples was characterized as well as the chemical state of the registered elements, in particular – of Ce³⁺ and Ce⁴⁺ (in at.%). In addition, a quantitative assessment was made of the presence and possible changes in the ratio of the concentrations of Ce³⁺ and Ce⁴⁺ in the oxide layers deposited on SPCEs. These data also provide opportunities for effective quantitative assessment when planning the study of ongoing (oxidation/reduction) catalytic processes, respectively electroanalytical studies. The data from the XPS analyses of the studied systems are presented in Table 1 and Table 2.

As expected, with increasing deposition current density, the cerium concentration of the surface cerium oxide layer increases from 5 – 10 at.% to about 10 – 15 at.%. Accordingly, this increase is at the expense of the decrease in the carbon concentration. This effect can be associated with an increase in the thickness of the deposited cerium oxide layers, in which the X-ray beam irradiating the layer during analysis cannot reach the carbon substrate. Of course, with increasing deposition time, in the layers deposited at 0.5 mA.cm^-2, the concentrations of cerium and, respectively, the oxygen associated with it increase. However, this tendency is escaped for CNT and SWCNT samples. For the SWCNT sample, this decrease is particularly dramatic. In a sample on which the deposition lasted for 40 min, the Ce concentration was close to 15 at.%, while in the one deposited for 80 min, its concentration decreased to 5 at.% (Table 2). It is important to note that the Ce⁴⁺ concentration calculated from the Ce3d spectrum is high and reaches about 40 – 80 % of the total amount of deposited Ce.

From the chemical shift of the XPS spectra, the valence state of the elements build the deposited oxide layer can be estimated. This information can be taken into account when optimizing the conditions for obtaining mixed Cе₂O₃+CeO₂ coatings. Figure 7a shows the separated XPS core photoelectron spectra of C1s. The figures present the spectra of samples obtained at 1 mA.cm^-2 and a deposition time of 80 min. The spectra of this group of samples are shown because the intensity of the spectra of Се3d, О1s and С1s is highest and most pronounced in them.

It is important to analyze both the spectra of Ce3d and O1s, as well as C1s, in order to establish the influence of the substrate on the growth of the CeO₂ layers.

The peaks in the spectra of С1s are broad. For this reason, they are deconvoluted. The most likely is the peak fitting, in which they are divided into three groups. The peaks positioned at 284.6 eV are characteristic of the presence of adventitious carbon [31,32,33] and are most likely not due to the carbon from the substrate. This peak may also overlap with the peak characteristic of the presence of C = C – bond in graphite [34].

The second group of peaks, with a binding energy of about 286.2 eV, is due to the presence of C – O bonds [35,36]. The third group of peaks is positioned at about 288.7 eV and is due to the presence of carboxyl groups [37,38,39]. The figure shows that the intensity, respectively the amount of COOH groups, decreases in the order C110 > MC > CNF > CNT > SWCNT (See Figure 7a). In the C1s spectrum, a group of peaks at low binding energies is also visible – from 282.4 to 283.6 eV. These low energies are characteristic of the presence of metal-carbide phases, but in this case they are due to uneven charging of the carbon substrates [40]. We exclude the presence of a metal-carbide phase due to the impossibility of obtaining such a phase with the method we used for preparation. Carbon interacts with other elements only at high temperatures, and the cerium layers are deposited when the electrolyte is cooled to 15°C. At the same time, XRD studies do not show the presence of CeC₂. Some authors [41] have shown that graphene can suppress the so-called differential charging effects. They are usually due to samples with insulating domains or island structures that have varying thicknesses on a conducting surface. The spectral features of these areas will be shifted to lower binding energies. These effects, in our opinion, are due to the carbon peaks positioned at 283.6 eV and the lower binding energies at 282.4 eV. At the same time, in MC, CNT and SWCNT samples, intense peaks appear at about 294.0 eV. They are, in our opinion, again due to this differential charging.

Figure 8 shows the spectra of Ce3d. They consist of spin-orbit splitted doublets. Each doublet showing an extra structure – satellites due to final state effects [18,42]. In the figure, the doublets (v, u and vo, uo) and their satellites (v', u', v'', u'', u''') are denoted by the generally accepted notation of Burroughs et al. [43]. The peaks and satellites characteristic of Ce⁴⁺ are marked in red, and the peaks characteristic of Ce³⁺ are marked in blue. Pardo et al. [44] use the magnitude of u''' – the peak at 916.6 eV, characteristic of Ce⁴⁺, to calculate its concentration. It can be seen from the figure (see also Table 2) that the cerium layers deposited on carbon substrates consist of a mixture of Ce³⁺ and Ce⁴⁺. The table gives the ratio between these two oxidized forms of Ce.

Figure 7b shows curve fitted photoelectron spectra of O1s. They consist mainly of three peaks located at around 529.4, 531.5 and 532.5 eV. The peak at 529.4 eV is associated with the presence of the Ce – O bond [45,46,47]. A slight shift of 0.2 eV of the peak of the C110 sample towards lower binding energies – 529.2 eV is observed. For the CNF sample this shift is again by 0.2 eV, but towards more positive binding energies – 529.7 eV.

The band positioned at 531.5 eV and usually designated O_HBE is due to the presence of the double structure in the spectrum of O1s associated with Ce3d [18]. It has been assigned to Ce₂O₃ oxide on the surface or to hydroxyl groups on the surface or to oxygen chemisorbed on the surface in other forms such as CO, CO₂. However, other XPS studies suggested that the presence of the O peak maybe attributed to oxide ions in the HBE defective CeO_х (x < 2) layer.

The peak at 532.5 eV is typical of the presence of adsorbed OH groups and water [48,49,50].

According to the obtained XPS data, presented in Table 2, the change in the total concentration of cerium (Ce³⁺+Ce⁴⁺) registered on the surface of the studied systems shows that:

• at the lower cathode current density (0.5 mA.cm^-2), the maximum recorded value for Ce, reaching 11.2 at.%, was recorded on SPCE MC. It is important to note that this sample also recorded the highest value for the Ce⁴⁺ concentration – 63 at.% (Table 1);
• relatively high values of Ce, respectively for the concentration of Ce⁴⁺, were also found in SPCEs CNF, CNT, SWCNT and C110;
• at the higher cathode current density (1 mA.cm^-2), the maximum recorded value of the Ce concentration, reaching 14.7 at.% and 11.3 at.%, are registered on SPCEs SWCNT and CNT. And in these samples the highest value for the C^e4+ concentration was established – 64 at.% (Table 2);
• also noteworthy, with regard to the relatively high value of Ce, respectively the concentration of Ce⁴⁺, are the results characterizing SPCEs C110 and MC, at a cathode current density of 1 mA.cm^-2.

The XPS data obtained and discussed above reveal possibilities for choosing optimal combinations for forming catalytically effective (modified with ceria coatings) SPCEs. Moreover, the established significant differences (and the possibilities for combining and varying them with the structure and chemical composition of SPCEs) of the total and individual concentrations of Ce³⁺ and Ce⁴⁺ (in mixed Ce₂O₃+CeO₂ coatings, deposited on SPCEs) provide solutions for their electroanalytical application in studying the behavior of both cathodic and anodic processes/reactions.

3.3. XRD Investigations

The samples were placed in the diffractometer without any preliminary sample preparation. They were carefully centered relative to the position of the X-ray beam. The processing of the diffractograms and phase analysis were carried out based on a program Match! [29] and a free crystallographic database COD [30].

Figure 9 presents the XRD patterns of the studied SPCEs. All Screen-printed electrodes were carefully centered so that the X-ray beam fell into the area of the carbon substrates covered with cerium oxide layers - the so-called working electrode of the SPCE. However, the recorded diffractograms also show the diffraction peaks of the carbon substrate. Phase identification showed the presence of Corundum (Al₂O₃ COD Entry # 96-900-9679), Rutile (TiO₂ COD Entry # 96-900-9084), Silver (Ag COD Entry # 96-110-0137), (due to the silver ring forming the Reference electrode of SPCE) and Graphite (C COD Entry # 96-901-2231). All registered compounds are related to the presence of these elements in the studied electrode substrates. The deposited thin cerium oxide film is represented by a single diffraction peak located at an interplanar spacing of d = 3.11 – 3.12 Å. This value fully corresponds to the strongest peak of Cerianite (CeO₂ COD Entry # 96-900-9009) [51], with Miller indices (111). This is not unusual and has been observed in other methods of growth and formation of CeO₂ [52,53].

Figure 10 shows the polyhedral structural model of CeO₂. The cerium atoms are coordinated in a cubic coordination formed by the oxygen crystals and are located inside the polyhedron. In it, the oxygen atoms are shown in reduced size (marked in red), located at the vertices of an imaginary cube. The growth axis is directed upwards, and a plane with Miller indices (111) is indicated in magenta.

Since the deposited coatings have an orientation of (111), and the properties of the cerium oxide crystallites are anisotropic, the references to the properties studied during the experiments (such as characterization of: corrosion resistance, degradation of dyes, concentration of pharmaceutical forms, etc.) should be related mostly to the crystal plane (111) of obtained and observed in our investigations cerianite (CeO₂).

4. Discussion

In light of the results obtained and commented above (paragraphs 3.1-3.3) regarding the formation of Ce – oxide layers, XPS – spectra of C1s were also obtained and analyzed. It is observed in them that in the samples where a carbon peak due to differential charging was registered at the highest binding energies (294 eV), the carbon peaks at the lowest binding energies (283.6 eV) are absent. This is probably related to the differences in the morphology of the carbon substrate, which inevitably affect the growth of mixed Ce₂O₃+CeO₂ coatings. The question of why in some cases the carbon substrates manage to compensate for this charging, and in other cases not, is debatable. These charging effects are most likely due to the differences in the ability of the layered structures to conduct electrons. Table 2 shows that differential charging does not affect the concentration of Ce⁴⁺. In all samples it remains high. At the same time, the concentration of Ce⁴⁺ is related to the ionic conductivity of the layers due to the known ability of ceria to act as an oxygen pump – to easily accept and release oxygen ions (the so-called Oxygen Storage Capacity – OSC). For these reasons, we can assume that the sensor properties of the semiconductor materials obtained by us will be due to both the presence of electronic conductivity and the presence of ionic conductivity.

It is also debatable to what extent the C1s peaks, due to differential charging at the highest binding energies (294 eV), should be taken into account in the calculation of the total carbon concentration. If we compare the intensity of Ce3d – spectra of SPCEs MC, CNT and SWCNT samples with those of the other samples, we will see that their area value is comparable to that of the other SPCEs in which they are absent (C1s peaks, due to differential charging at the highest binding energies (294 eV)). For example, in SPCEs MC and CNT the areas of the Ce3d spectra are 59846 and 67186, respectively. The difference between them and the area of the Ce3d peak in the SWCNT sample is greater. In this case, it was calculated to be 39609. This value is almost twice lower than in the other two samples. This and comparing the XPS spectra with the SEM results – the analyses showing dense cerium coatings – gave us the basis to recalculate the atomic percentage concentrations of all elements, without taking into account the C1s peaks due to differential charging at high binding energies (294 eV). This gives the results given in brackets in Table 2. They show that when we do not take the peak at 294 eV into account in the carbon concentration calculations, the cerium concentration does not decrease, but as expected, increases after 80 min. electrodeposition. On the other hand, this decrease in concentration can also be due to optical effects from a surface that is not uniformly smooth and reflects electrons in different directions due to this unevenness. It is possible that the lower cerium concentration is also due to a thinner deposited layer, which is a result of the presence of diffusion limitations in the transfer of cerium ions in the electrolyte.

For all samples, the areas of the Ce3d peaks compared to the sums of the areas of the two O1s peaks corresponding to the Ce – O bond are approximately equal to the stoichiometric ratio of Ce to oxygen in CeO₂. For example, for the SWCNT sample, the area of the Ce3d peak is 37309/51.6 (51.6 is The Relative Sensitivity Factor (RSF) for Ce3d) = 723, and the sum of the areas of the two oxygen peaks at 529.4 and 531.5 eV is 5184/2.93 (2.93 is the RSF for O1s) = 1769, which is 2.4 : 1 in favor of oxygen. This ratio suggests the absence of oxygen deficiency, respectively, we exclude the possibility of the presence of oxygen vacancies. This may possibly affect the sensing properties of the obtained electrodes.

The established significant differences and variations in the total and individual concentrations of Ce³⁺ and Ce⁴⁺ in the mixed (Ce₂O₃ + CeO₂) coating, registered on the studied SPCEs, suggest their effective application in the study of both cathodic and anodic catalytic processes. A significant influence in this will obviously be determined by the established morphological and structural changes on the surface of the Screen-Printed Carbon Electrodes modified with mixed Ce₂O₃ + CeO₂ coatings. They could have a significant impact on the specific catalytic active surface of the modified SPCEs.

5. Conclusions

An original electrochemical technology (compositions and modes for electrochemical deposition of cerium oxide layers from non-aqueous solutions) has been successfully applied. It allowing the formation of promising cerium oxide coatings, with respect to their application as sensors. For these purpose five types of carbon screen-printed electrodes of the company Metrohm: carbon (C110), mesoporous carbon (MC), single-walled (SWCNT) and multi-walled carbon nanotubes (CNT) and carbon nanofibers (CNF) were modified with ceria coatings. The qualitative and quantitative changes in the morphology (SEM), structure (XRD), chemical composition (XPS, EDS) and chemical state (XPS) of the elements constituting the electrodeposited cerium oxide coatings as well as the carbon SPCEs have been studied. As a result of these studies, the conditions for modifying SPCEs were optimized in order to achieve the desired effect in terms of the structure and chemical composition of the surface of the thus treated SPCEs. In addition, the presence and possible changes in the ratio of Ce³⁺ and Ce⁴⁺ in the cerium oxide layers deposited on SPCEs were established.

As a result of the conducted investigations, it was found that the highest concentration of the modified Ce-oxide layer containing the largest amount of Ce⁴⁺ was found on substrates made of mesoporous carbon (MC), single-walled (SWCNT) and multi-walled (CNT) carbon nanotubes. These coatings also have the highest degree of surface charging, as determined by XPS analyses, which can serve as an indication of the presence of both electronic and ionic conductivity. This makes these substrates the most suitable for sensor catalytic systems.

The electrochemical characterization of the capabilities and sensitivity of the thus modified SPCEs is pending with the aim of their application in catalytic and electroanalytical aspects.