Robust Self-Supported SnO₂-Mn₂O₃@CC Electrode for Efficient Electrochemical Degradation of Cationic Blue X-GRRL Dye

Abstract

Exploration of highly efficient and robust catalyst is pivotal for electrocatalytic degradation of dye wastewater, but it still is a challenge. Here, we develop a three-dimensional self-supported SnO₂-Mn₂O₃ hybrid nanosheets grown on carbon cloth (noted by SnO₂-Mn₂O₃@CC) electrode via a simple hydrothermal method and annealing treatment. Benefitting from the interlaced nanosheets architecture that enlarges the surface area and the synergetic component effect that accelerates the interfacial electronic transfer, SnO₂-Mn₂O₃@CC electrode exhibits a superior electrocatalytic degradation efficiency for cationic blue X-GRRL dye in comparison with the single metal oxide electrode containing SnO₂@CC and Mn₂O₃@CC. The degradation efficiency of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode can reach up to 97.55% within 50 min. Furthermore, self-supported architecture of nanosheets on carbon cloth framework contributes to a robust stability compared with the traditional electrode via the multiple dip/brush coating accompanied by the thermal decomposition method. SnO₂-Mn₂O₃@CC electrode exhibits excellent recyclability, which can still retain a degradation efficiency of 94.12% after six cycles. This work may provide a new pathway for the design and exploration of highly efficient and robust electrooxidation catalysts for dye degradation.

1. Introduction

Water contamination has been a concerning social issue and has garnered extensive attention. Organic wastewater, originating from the massive discharge of chemical production, usually cause serious water pollution due to low biodegradability and complex composition [1,2,3]. Especially, dye contaminations and their intermediates constructed by aromatic group produced after degradation is toxic and carcinogenic, which seriously endangers aquatic life and human health [4,5,6].

Currently, the common methods to treat dye wastewater contains biodegradation, photocatalytic oxidation, adsorption method, flocculant method and membrane separation technology and so on [7,8,9,10,11,12,13,14]. Among them, electrochemical oxidation technology has been considered as an environment-friendly and promising candidate to treat dye wastewater because of its strong oxidation capacity, lack of secondary pollution effects, its reusability and easy operative qualities [15,16]. Electrochemical oxidation method mainly takes hydroxide radical (OH) or active chlorine species to degrade refractory and non-biodegradable organic contaminations. Additionally, the efficiency of electrochemical oxidation technology is greatly determined by anode materials [17].

To date, various anode materials, such as precious metal electrode materials (Pt), boron-doped diamond (BDD) and metal oxide electrode materials (SnO₂, PbO₂, RuO₂, and IrO₂), have been widely studied to oxidize organic dye for further degradation via electrochemical oxidation treatment [18,19]. Among them, SnO₂ exhibits a potential advantage owing to its high oxygen evolution potential (OEP) and corrosion resistance. Generally, a high OEP can accelerate the oxidation process of organic dye pollution through the inhibition of oxygen evolution side-reaction. Nevertheless, SnO₂ electrode has low conductivity and stability, which impedes the large-scale application of degrading dyes wastewater [20]. Therefore, exploiting high-performance anodes with large OEP, fast electronic transfer and high electrochemical oxidation stability is pivotal to efficient dye treatment [17]. Recent researches indicate that introducing foreign elements is a feasible method to enhance catalytic degradation performance of SnO₂-based electrode [21]. Several introduced atoms include Sb, Ru, Ce, Nd and other rare earth elements [22,23,24,25,26,27,28]. For instance, Man et al. designed Sb and Ce co-doped SnO₂ nanoflowers electrode which can boost the decolorization efficiency of organic pollutants due to a reduced charge transfer resistance induced by Ce-doped SnO₂ [29]. Metal oxide are also used to improve the electrooxidation activity. Luu et al. fabricated Ti/SnO₂-Nb₂O₅ bimetallic oxide electrode through the sol–gel method [30]. The experimental illustrates that the right amount of Nb₂O₅ can enhance the electrochemical activity and organic pollutant degradation efficiency of the Ti/SnO₂-Nb₂O₅ electrode. It is worth noting that Mn₂O₃ seems to be a good candidate for electrode material because Mn₂O₃, as a p-type semiconductor material with a bandgap ranging from 1.2 to 1.29 eV, has been demonstrated to possess a faster interfacial electronic transfer between electrode and electrolyte in comparison with other high bandgap metal oxide nanomaterials [31].

In addition, regulating architecture to enhance the active area of electrode has also been proven as an efficient way, which can expose more active sites and favor catalytic oxidation performance [32,33,34,35]. Huang et al. developed a novel microsphere-structured Ti/SnO₂-Sb electrode with small grain size and nanosheets architecture, which possessed a significantly enhanced electrochemical active surface area and degradation efficiency [34]. Hu et al. reported a Pb-modified SnO₂ microsphere electrode that also presented an increased surface area to promote electrooxidation ability [36]. In addition to the high electrochemical degradation properties, the tight adherence between active oxide layer and substrate is another critical factor. Because traditional electrodes are usually synthesized with multiple dip/brush coating accompanied by the thermal decomposition method, vast cracks are likely to appear, thus the instable active layer on electrode substrate can cause a sharply decline of electrode activity or even deactivation [37]. In view of this, it is particularly important to synthesize a catalytic material with high catalytic performance and great stability.

In this work, three-dimensional SnO₂-Mn₂O₃ hybrid nanosheets grown on carbon cloth (noted by SnO₂-Mn₂O₃@CC) is synthesized using a simple hydrothermal and annealing treatment. The interconnected carbon fiber skeleton provides an efficient electronic transfer pathway, and the self-supported nanosheets arrays aligned on carbon cloth also strengthen the binding adherence between the active layer and the electrode scaffold substrate. Interestinglt, Mn precursor source can regulate the formation of nanosheets, which contributes to an increased surface area. Meanwhile, the synergistic effect of SnO₂ and Mn₂O₃ can significantly reduce the interfacial electronic resistance of the electrode. As a result, SnO₂-Mn₂O₃@CC electrode presents a higher OEP and faster interfacial electronic transfer. At 15 mA cm⁻², the degradation rate of cationic blue X-GRRL dye based on SnO₂-Mn₂O₃@CC electrode can reach up to 97.55% within 50 min. Moreover, SnO₂-Mn₂O₃@CC electrode exhibits a good recyclability, which can still maintain stability with a degradation rate of 94.12% after six cycles.

2. Results and Discussion

2.1. Characterization

The synthesis process of SnO₂-Mn₂O₃@CC nanosheets grown on carbon cloth (CC) is shown in Figure 1a, wherein self-supported SnO₂-Mn₂O₃@CC was synthesized using a simple hydrothermal reaction, followed by an annealing treatment at 400 °C. The crystal structure of these electrode materials was characterized using X-ray diffraction (XRD). In Figure 1b, the diffraction peaks at 26.2° and 44.2° are corresponded to the (002) and (101) crystal planes of C substrate (JCPDS No. 75-1621), respectively. The diffraction peaks located at 32.9°, 38.2°, 45.2°, 49.3° and 55.2° can be, respectively indexed to the (222), (400), (332), (431) and (440) crystal planes of Mn₂O₃ (JCPDS No. 41-1442). The residual diffraction peaks at 26.6°, 33.9°, 37.9° and 51.8° match well with the (110), (101), (200) and (211) crystal planes of SnO₂ (JCPDS No. 72-1147), respectively. The above results confirm that the prepared sample is composed of SnO₂, Mn₂O₃ and carbon substrate. Additionally, XRD pattern of the precursor in Figure S1 only detects the existence of SnO₂ and MnF₂, which further confirm the absence of Sn-MnO_x compound in the one-step preparation of SnO₂-Mn₂O₃/CC electrode materials using the hydrothermal method. For comparison, the similar hydrothermal reaction and annealing process are repeated based on the single Sn or Mn source as precursor; the corresponding samples are, respectively denoted by SnO₂@CC and Mn₂O₃@CC. XRD patterns in Figure S2 verify the successful preparation of SnO₂@CC (Figure S2a) and Mn₂O₃@CC (Figure S2b) samples.

SEM images in Figure 1c,d and Figure S3 show that both Mn₂O₃@CC and SnO₂@CC are composed of small and compact particles, while the surface of SnO₂@CC sample presents a more tight-packed particles and seems to have a dense cover layer, which is verified by a broken surface with an intentional scratch (Figure S4). It is well known that a compact surface can block the contact between electrode and electrolyte, unavailing electrocatalytic activity. In contrast, the synthesized SnO₂-Mn₂O₃@CC sample (Figure 1e) exhibits an obviously different morphology, which is composed of nanosheets with a thickness of 5 nm. As depicted in Figure 1e, the interlaced nanosheets are vertically aligned on the carbon fiber with irregular orientation. Compared with the tight-packed particles, the nanosheets-like morphology of SnO₂-Mn₂O₃@CC sample offers an enhanced surface area, availing the connectivity of catalytic active sites on electrode and electrolyte. It is worth noting that the self-supported nanosheets on CC substrate show a robust stability in comparison with the common electrode via the multiple dip/brush coating accompanied by the thermal decomposition method. A hydrothermal and annealing treatment can promote the adhesion between active materials and the substrate scaffold, and avoid the active materials peeling from the substrate, thus contributing to good stability. In addition, the self-supported nanosheets structure can ensure a rapid electron transfer between the electrode and the active layer, which shortens the charge transfer pathway compared with the aggregated particles.

Transmission electron microscopy (TEM) and high-resolution transmission electron microscopy (HRTEM) were use to investigate the morphology and structure of SnO₂-Mn₂O₃ nanosheets, which was prepared using the scratching from the carbon cloth framework. As shown in Figure 1f, SnO₂-Mn₂O₃ presents a nanosheet morphology, consistent with SEM results. HRTEM image displays that the SnO₂-Mn₂O₃ nanosheets are composed of crystalline nanoparticles (Figure 1g). The lattice fringes with a distance of 0.334 and 0.271 nm are corresponded with (110) plane of SnO₂ and (222) plane of Mn₂O₃, respectively, which corroborates the fact that the nanosheet is composed of SnO₂ and Mn₂O₃. The scanning TEM (STEM) image and energy dispersive X-ray spectroscopy (EDS) elemental map** images (Figure S5) confirms the existence and homogeneous distribution of Sn, Mn and O elements on SnO₂-Mn₂O₃ hybrid nanosheets. Additionally, the content of Mn₂O₃ is 57.8 wt% in the mixed oxide nanosheets (Figure S6 and Table S1). Based on the above result, we can deduce that the additive of Mn precursor source can not only regulate the morphology to form three-dimensional intersected nanosheets, but also promote the hybrid Mn₂O₃ and SnO₂ composition.

X-ray photoelectron spectroscopy (XPS) measurement was performed to analyze the chemical composition and the valence state of the SnO₂-Mn₂O₃@CC sample. In Figure 2a, the characteristic peaks of Sn, C, Mn and O can clearly be observed in the XPS survey, confirming the existence of Sn, C, Mn and O in SnO₂-Mn₂O₃@CC. In Sn 3d XPS spectrum (Figure 2b), the peaks located at 487.2 and 495.6 eV are ascribed to Sn 3d_5/2 and Sn 3d_3/2, respectively. Additionally, binding energy difference between Sn 3d_3/2 and Sn 3d_5/2 is about 8.4 eV, indicating that Sn⁴⁺ exists in SnO₂-Mn₂O₃@CC [29]. The Mn 2p XPS spectrum can be deconvoluted into three characteristic peaks (Figure 2c). The peaks at 641.5 and 653.1 eV, respectively correspond to Mn 2p_3/2 and Mn 2p_1/2, suggesting the existence of Mn³⁺ in Mn₂O₃, and the peak at 645.5 eV is the satellite peak (marked by Sat.). The O 1s spectrum (Figure 2d) can be fitted into two characteristic peaks. The O 1s peak at 530.75 eV is associated with the lattice oxygen (O_L) existing in the metal oxide crystal. Peaks located at 532.26 eV is attributed to the adsorbed oxygen (O_ad). In general, O_ad can promote the generation of ·OH during the electrooxidation process, owing to the easy exchange between O_ad and oxygen adsorbed molecules on the catalytic layer [38]. The aforementioned results indicate that SnO₂ and Mn₂O₃ successfully coexisted in the prepared SnO₂-Mn₂O₃@CC sample.

2.2. Electrochemical Characterization

Linear voltammetry scanning (LSV) curves of different electrodes were tested in 0.5 M NaCl solution to evaluate the OEP of these electrodes, which can be obtained by the intersection value of the horizontal line and the tangent of LSV curve. OEP is an important factor to determine the electrochemical oxidation capacity of electrodes, because a large OEP value can restrain the oxygen evolution side reaction, thus providing more ·OH and larger current efficiency for electrooxidation reaction; meanwhile, it also restrains the oxidation of substrate produced by oxygen. Consequently, a larger OEP value usually suggests a superior electrooxidation catalytic activity of the electrode. As shown in Figure 3a, the OEP value of SnO₂-Mn₂O₃@CC electrode is 1.73 V vs. the saturated calomel electrode (SCE), exceeding SnO₂@CC (1.68 V vs. SCE) and Mn₂O₃@CC (1.70 V vs. SCE). These results suggest the SnO₂-Mn₂O₃@CC electrode induced by Mn precursor can hinder the oxygen evolution side reaction on anode and contribute to a higher current efficiency in comparison with the single metal oxide electrode.

Interfacial impedance of different electrodes was evaluated using the electrochemical impedance spectroscopy (EIS). Nyquist plots and fitting results of different electrodes are displayed in Figure 3b and

Table 1. The impedance fitting results for different electrodes.

	Rs (Ω cm2)	Rf (Ω cm2)	Rct (Ω cm2)	Qf (mF cm2)	Qdl (mF cm2)
SnO2-Mn2O3@CC	5.887	1.629	8.509	1.32	2.27
SnO2@CC	6.577	4.051	70.65	0.21	0.52
Mn2O3@CC	7.329	1.604	34.53	0.91	0.79

. In the equivalent circuit (the inset in Figure 3b), R_s, R_f and R_ct, respectively represent the solution resistance, oxide film resistance and charge transfer resistance on the interface of electrolyte and electrocatalyst; and Q_f and Q_dl depict the film capacitance and the double layer capacitance, respectively. R_ct of SnO₂-Mn₂O₃@CC electrode is 8.51 Ω cm², which is far less than SnO₂@CC (70.65 Ω cm²) and Mn₂O₃@CC (34.53 Ω cm²). Moreover, the SnO₂-Mn₂O₃ hybrid nanosheets (Table S2) also present the optimal intrinsic electrical conductivity. The aforementioned result verifies that the SnO₂-Mn₂O₃ hybrid nanosheets induced by the Mn precursor additive can improve the charge transfer kinetics, which favors the electrochemical/electrooxidation catalytic activity of electrodes.

A large electrochemical active surface area (ECSA) is also an important factor in evaluating the catalytic activity area for a good electrode, which can afford more exposed catalytic active sites to promote electrocatalytic oxidation. According to ECSA = C_dl/C_s, ECSA is proportional to the double-layer capacitance (C_dl), thus C_dl can be used to assess the ECSA and can be calculated using cyclic voltammetry (CV). In Figure S7, CV curves of different electrodes are tested in the non-Faraday region from 0.5 to 0.7 V vs. SCE in 0.5 M NaCl solution at a scanning rate ranging from 20 to 100 mV s⁻¹. As shown in Figure 3c, SnO₂-Mn₂O₃@CC exhibits the largest C_dl value (6.19 mF cm⁻²), exceeding SnO₂@CC (3.23 mF cm⁻²) and Mn₂O₃@CC (1.37 mF cm⁻²). The result suggests that hybrid SnO₂-Mn₂O₃@CC can afford the largest catalytic surface area, matched well with SEM results.

Voltammetric charge (q*) is also a critical parameter to assess the active surface area of electrodes, which is relevant to the specific electroactivity of the sites and can be obtained via CV curves [39]. It is worth noting that the total voltammetric charge (q*_T) contains the outer voltammetric charge (q*_O) and the inner voltammetric charge (q*_I), which can be calculated from the relationship of q* and scan rate (v). The detailed equations are as follows:

$$q^{*}{=q}_{\mathrm{O}}^{*}{+\mathrm{k}}_1{v}^{-1/2}$$

(1)

$${{(q}^{*})}^{-1}{=(q}_{\mathrm{T}}^{*}{)}^{-1}{+\mathrm{k}}_2{v}^{1/2}$$

(2)

$$q_{\mathrm{T}}^{*}{=q}_{\mathrm{O}}^{*}{+q}_{\mathrm{I}}^{*}$$

(3)

At a very low scan rate, the total active surface containing the inner and outer of electrode can participate in the reaction, thus the total voltammeric charge q*_O can be calculated by Equation (1). The intercept of the straight line in Figure 3d is the reciprocal of q*_T, whereas at a high scan rate, especially when v approaches to ∞, electrolyte ions only contact with the outer surface of electrode, and has no time to permeate into the inside of the electrode, thus only q*_O contributes to the charge. According to Equation (2), q*_O is equal to the intercept of q* vs. v^−1/2 (Figure 3e). As listed in

Table 2. Electrochemical analysis results under different scan rates of the prepared anodes.

	q*T (mC cm−2)	q*O (mC cm−2)	q*I (mC cm−2)
SnO2-Mn2O3@CC	3.991	1.879	2.112
SnO2@CC	1.7999	1.0491	0.7508
Mn2O3@CC	0.6456	0.49192	0.1537

, SnO₂-Mn₂O₃@CC electrode presents the largest total voltammetric charge, which is, 2.2 and 6.2 times of SnO₂@CC and Mn₂O₃@CC, respectively. Similarly, both q*_O and q*_I value of SnO₂-Mn₂O₃@CC are still greatly larger than SnO₂@CC and Mn₂O₃@CC electrodes. These above results further confirm that the active surface area of hybrid SnO₂-Mn₂O₃@CC is larger than the single metal oxide electrode, which can ascribe to the three-dimensional nanosheets architecture produced by the addition of Mn precursor.

Service life of electrode is another pivotal factor to estimate the catalytic activity, which determines its further practical application. An accelerated life test of different electrode was carried out at 100 mA cm⁻². As manifested in Figure 3f, SnO₂-Mn₂O₃@CC electrode exhibits the longest service life, exceeding that of SnO₂@CC and Mn₂O₃@CC, which indicates that the hybrid SnO₂-Mn₂O₃@CC electrode induced by the addition of Mn precursor source can improve electrode service life and stability. Interestingly, the service life of these electrodes is superior than the traditional dip/brush-coating electrodes [40], which may be ascribed to the tight adhesion between catalytic active layer and substrate generated using the hydrothermal and annealing process. Therefore, the self-supported structure on substrate seems as a good candidate for a robust electrooxidation catalyst.

2.3. Electrochemical Degradation of Cationic Blue X-GRRL

Electrooxidation ability of these prepared electrode materials were evaluated based on the degradation of the cationic blue X-GRRL dye. The time-dependent Ultraviolet Spectrophotometer (UV–vis) absorbance spectra of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode are shown in Figure 4a, which is a pivotal factor to estimate the degradation efficiency of cationic blue X-GRRL. The azo conjugated chromogenic system in cationic blue X-GRRL dye molecule corresponds to the absorption peak of 608 nm [41]. In Figure 4a, the intensity of characteristic adsorption peak at 608 nm decrease with time and disappears after 50 min, indicating that cationic blue X-GRRL has been completely decomposed in 50 min. Meanwhile, a visually gradual color fading of cationic blue X-GRRL dye is depicted in the time-dependent photos (Figure 4b). The color is near to colorless at 40 min, suggesting that cationic blue X-GRRL dye has been successfully degraded in the electrochemical oxidation process. Moreover, the time-dependent UV–vis absorbance spectra of cationic blue X-GRRL on SnO₂@CC and Mn₂O₃@CC electrodes are also tested (Figure S8a,b). The comparative intensity of time-dependent characteristic adsorption peaks at 608 nm (Figure S8c) indicate a faster degradation process of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode.

The electrocatalytic oxidation performances of different electrodes for degrading cationic blue X-GRRL with an initial concentration of 20 mg L⁻¹ were investigated. In Figure 5a, after 50 min of electrolysis, the removal efficiency of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC is 97.55%, which is superior than that of Mn₂O₃@CC (92.74%) and SnO₂@CC electrode (88.3%). Meanwhile, the relationship between time and electrochemical degradation of cationic blue X-GRRL on different electrodes follows the pseudo-first-order kinetics model, which can be described as the following equation:

$${-\ln (\mathrm{A}}_{\mathrm{t}}{/\mathrm{A}}_0)=k\mathrm{t}$$

(4)

where, A₀ is the initial absorbance, A_t is the absorbance at given time t and k is the kinetic rate constant. As displayed in Figure 5b, the reaction kinetic rate constant k₁ of SnO₂-Mn₂O₃@CC is larger than Mn₂O₃@CC and SnO₂@CC electrodes, indicating a faster cationic blue X-GRRL degradation rate. The detailed values of k on different electrodes are listed in Table S3. Different kinds of supporting electrolyte have varied influences on the electrocatalytic degradation efficiency. Therefore, different electrolytes containing NaCl, Na₂SO₄ and Na₂CO₃ were used to investigate the effect of electrolyte ions on degrading cationic blue X-GRRL. As displayed in Figure 5c, the degradation efficiency of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode in three electrolytes increase along with time. Additionally, the dye degradation efficiency in 0.5 M NaCl electrolyte can be as high as 97.55% after 50 min, which greatly exceeds that of Na₂SO₄ (17%) and Na₂CO₃ (79.23%). During the electrooxidation process, HO· free radicals are responsible for the dye degradation, which is verified by the time-dependent fluorescence spectrometry (Figure S9), moreover, chlorine species also plays an important role. Since the redox potential of Cl⁻/Cl₂ (U = 1.36 V vs. RHE) is low than that of HO·/H₂O (U = 2.2 V vs. RHE) [42], Cl₂ is more easily generated in comparison with HO· in wastewater, along with a series of the following reactions [43]:

$${\mathrm{Cl}}^{-}\to {\mathrm{Cl}+\mathrm{e}}^{-}$$

(5)

$$2·\mathrm{Cl}\to {\mathrm{Cl}}_2$$

(6)

$${\mathrm{Cl}}_2{+\mathrm{H}}_2\mathrm{O}\to {\mathrm{HClO}+\mathrm{H}}^{+}{+\mathrm{Cl}}^{-}$$

(7)

$$\mathrm{HClO}\to {\mathrm{H}}^{+}{+\mathrm{ClO}}^{-}$$

(8)

$$\mathrm{HClO}+\mathrm{organics}\to {\mathrm{CO}}_2{+\mathrm{H}}_2\mathrm{O}+\mathrm{HCl}$$

(9)

Therefore, SnO₂-Mn₂O₃@CC electrode in 0.5 M NaCl electrolyte can contribute to the excellent electrocatalytic oxidation efficiency. Moreover, the degradation of cationic blue X-GRRL in different electrolytes follows the pseudo-first-order kinetics (Figure 5d). SnO₂-Mn₂O₃@CC electrode displays the fastest reaction degrading rate in 0.5 M NaCl electrolyte, and the corresponding reaction rate constant is listed in Table S4.

Current density is another critical factor affecting the electrocatalytic degradation ability of electrodes. Figure 5e shows the degradation efficiency of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode in 0.5 M NaCl electrolyte by applying 5, 10, 15 and 20 mA cm⁻². The degradation efficiency of cationic blue X-GRRL shows a remarkable enhancement with the increased current density ranging from 5 to 15 mA cm⁻², while the degradation efficiency decreased when the current density is 20 mA cm⁻². An excessive current density along with a higher potential can impel the oxygen evolution side reaction, restraining electrochemical oxidation reaction. Moreover, excessive current density is a waste of electric energy and economic cost. Therefore, 15 mA cm⁻² is an optimal condition for degrading cationic blue X-GRRL.

The recyclability of electrode is a pivotal issue in its practical application. SnO₂-Mn₂O₃@CC electrode is used for recyclable degradation of cationic blue X-GRRL for six times. As shown in Figure 5f, the removal efficiency of cationic blue X-GRRL almost remains constant for six cycles. The successive degradation rates at the 50th min are 97.55%, 96.83%, 95.4%, 94.52%, 94.03%, and 94.12%, respectively. The above result confirms that SnO₂-Mn₂O₃@CC electrode as an electrooxidation catalyst for cationic blue X-GRRL dye possesses a good recyclability.

As shown in Figure 6, the electrocatalytic degradation mechanism of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC is proposed based on the aforementioned results in the degradation experiments. Firstly, H₂O and Cl⁻ on the surface of SnO₂-Mn₂O₃@CC electrode lose electrons to form hydroxyl radical (·OH) and active chlorine in the NaCl solution, and the active chlorine further hydrolyzes into ClO⁻. Then, the ·OH radical and ClO⁻ combine with cationic blue X-GRRL dye molecule and degrade the dye molecule to produce CO₂ and H₂O [41]. In the electrocatalytic degradation process of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC, active chlorine may be the main factor for the rapid degradation.

3. Materials and Methods

3.1. Materials

T Stannous chloride dihydrate (SnCl₂⋅2H₂O, 98.0%), manganese acetate tetrahydrate (MnC₄H₆O₄⋅4H₂O, 99.0%), ammonium fluoride (NH₄F, 96.0%), sodium carbona anhydrous (Na₂CO₃, 99.8%), sodium chloride (NaCl, 99.5%), ethanol (C₂H₅OH, 99.7%) and sodium sulfate anhydrous (Na₂SO₄, 99.0%) were purchased from Sinopharm chemical Reagent Co, Ltd. (Shanghai, China). A commercial cationic blue X-GRRL was obtained from Jiangsu **ji Industrial Co., Ltd. (China).

3.2. Preparation of SnO₂-Mn₂O₃@CC

Firstly, the carbon cloth substrate was treated in HNO₃ and rinsed with deionized water and ethanol. Typically, 2 mmol MnC₄H₆O₄·4H₂O, 2 mmol SnCl₂·2H₂O and 5 mmol of NH₄F were dissolved in 20 mL of solvent containing ethanol and deionized water with a volume ratio of 1:1, then a carbon cloth (2 × 3 cm²) and the above solution was transferred to a 50 mL autoclave at 180 °C for 6 h. After washing it several times, the prepared sample was dried at 60 °C; for 8 h. Finally, the SnO₂-Mn₂O₃@CC was synthesized by annealing at 400 °C; for 2 h in air atmosphere.

For SnO₂ @CC and Mn₂O₃@CC, all the above processes were repeated, except for the initial precursor sources. SnO₂ @CC contains 2 mmol SnCl₂·2H₂O and 5 mmol of NH₄F, while Mn₂O₃@CC includes 2 mmol MnC₄H₆O₄·4H₂O and 5 mmol of NH₄F.

3.3. Characterization Measurements

The crystalline structures of the electrodes were investigated using the X-ray diffraction (XRD) equipment (Rigaku D-MAX 2500/PC, Tokyo, Japan) with a Cu Ka radiation source (λ = 0.15405 nm). The surface morphology of the electrode materials was analyzed using scanning electron microscopy (SEM, Tescan MIRA4, Jebulno, Czech Republic) and transmission electron microscopy (TEM, Tecnai G2F30, Hillsboro, OR, USA). The chemical composition and oxidation state were detected on X-ray photoelectron spectrometer (XPS, Thermo Scientific, ESCALAB 250XI, Waltham, MA, USA) with a Mg-Kα radiation source. The degradation experiment was carried out on an ultraviolet spectrophotometer (UV–vis, Bei**g Puxi General Instrument Co., Ltd., Bei**g, China).

3.4. Electrochemical Testing

All of the electrochemical tests were carried out on a CHI 760D electrochemical workstation in a three-electrode system at 25 °C;. A total of 0.5 M NaCl solution was served as the electrolyte solution. The synthetic material (1 × 1 cm²) was served as the working electrode, and a platinum sheet and saturated calomel electrode (SCE) were served as the counter electrode and the reference electrode, respectively. Electrochemical impedance spectroscopy (EIS) curves were examined under 0.54 V vs. SCE at a frequency ranging from 10⁻² to 10⁻⁵ Hz in 0.5 M NaCl. The double layer capacitance (C_dl) of the material was implemented using cyclic voltammetry (CV) tested in the non-Faraday region from 0.5 to 0.7 V (vs. SCE). Accelerated service life tests of different electrodes were performed at 100 mA cm⁻² in 0.5 M NaCl. Electrodes were regarded as devitalized when the applied potential exceeded 3 V.

3.5. Electrocatalytic Experiments

The electrooxidation degradation of cationic blue X-GRRL dye was carried out at 15 mA cm⁻² in 100 mL solution containing cationic blue X-GRRL solution (20 mg L⁻¹) and NaCl (0.5 M). During the degradation process, 2 mL of solution was taken out at a special interval and its concentration and absorbance were detected using the Ultraviolet Spectrophotometer (UV–vis). The removal efficiency of dye was described as follows:

$$\mathrm{Removal}\mathrm{efficiency}\left(\%\right)=\frac{{\mathrm{A}}_0{-\mathrm{A}}_{\mathrm{t}}}{{\mathrm{A}}_0}\times 100\%$$

(10)

where, A₀ is the initial absorbance, and A_t is the absorbance at given time t.

Recyclability of SnO₂-Mn₂O₃@CC electrode was performed at 15 mA cm⁻². After every degradation cycle, SnO₂-Mn₂O₃@CC electrode was washed with water for several times and was directly used for next degradation cycle.

4. Conclusions

In summary, self-supported SnO₂-Mn₂O₃ hybrid nanosheets grown on carbon cloth is successfully synthesized using a simple hydrothermal and annealing treatment. The addition of Mn precursor can regulate the formation of nanosheets to the interlaced network architecture, which contributes to an increased surface area and more exposed active sites. Meanwhile, Mn precursor dopant can enrich the component of active layer, thus the synergistic effect of SnO₂ and Mn₂O₃ accelerate a faster interfacial electronic transfer. Self-supported nanosheets on carbon cloth contribute to a robust stability compared with the traditional electrode via the multiple dip/brush coating accompanied by the thermal decomposition method. Consequently, SnO₂-Mn₂O₃@CC electrode possesses a larger electrochemical active area and improved q*_T, q*_O and q*_I value. The degradation efficiency of cationic blue X-GRRL on SnO₂-Mn₂O₃@CC electrode can reach up to 97.55% within 50 min and the electrocatalytic oxidation process follows the first-order kinetic. Moreover, SnO₂-Mn₂O₃@CC electrode exhibits excellent recyclability, which can still retain a degradation efficiency of 94.12% after six cycles. This excellent electrocatalytic oxidation activity indicates that the self-supported SnO₂-Mn₂O₃@CC electrode is a promising electrooxidation catalyst for dye degradation.