1. Introduction
Presently, the utilization of hydrocarbon-based fuels in various sectors generating unlimited pollutants causes damage to the earth’s environment. An alternative eco-friendly energy source is needed urgently to prevent or reduce the pollutant emissions. In this process, the most popular photoelectrochemical activity (PA) is a highly considerable alternative technique to produce environmental fuel like hydrogen. In the PA technique, semiconductors are used as catalyst materials for fuel generators under the irradiation of solar light. Numerous semiconducting nanostructures were tested for PA such as IrO
x, TM
3C
12O
12, Ni
3Se
4, TiO
2, etc. [
1,
2,
3,
4]. However, the mono-nanostructures could have the ability to generate induced currents due to less optical utilization, a high recombination rate, and poor kinetics. To overcome the limitation of the catalyst materials, several techniques were adopted to improve the catalyst activity of the catalysts, for example, doping, development of heterostructures, and alteration of morphology.
Nowadays, the spinel structures of AB
2X
4, where A and B can be divalent and trivalent, are used as a photocatalyst due to their excellent physical and chemical properties. In the spinal structures, the ZnFe
2O
4 nanostructures are well-established for catalytic applications [
5] owing to the band gap, electrochemical stability, and availability. However, the main catalytic activity is limited because of its spectral response range, poor conductivity, fast recombination rate, and poor electronic and separation behavior. Therefore, the researchers focused on increasing the charge transfer and separation rate by constructing heterostructures, loading co-catalysts, and doping. The development of heterostructures could exhibit several advantages and could enhance the charge movement at the solid–liquid junction, the photon harvesting range, the excitation of electron and hole, and the surface reactions.
The Fe
2O
3 nanostructures were utilized in the study to develop a heterostructure photocatalyst due to its high estimated efficiency, stability, availability, and narrow optical band gaps. Additionally, the Fe
2O
3 nanostructures, with the combination of other semiconducting nanostructures, can significantly enhance catalytic properties under illumination [
6]. Further, the band edge locations of ZnFe
2O
4 are preferably offset from that of Fe
2O
3, and it is assumed that the ZnFe
2O
4-Fe
2O
3 heterostructures can efficiently enrich the charge separation produced in both ZnFe
2O
4 and Fe
2O
3 regions by permitting movement of charges. Because the ZnFe
2O
4 valence band edge is positioned towards a more negative voltage compared to Fe
2O
3, the ZnFe
2O
4-Fe
2O
3 anode that may be best employed is the band edge offset to generate charge in the Fe
2O
3 and transfer to the ZnFe
2O
4, which then moved to the catalyst/electrolyte interface. This should be extremely beneficial for photon-harvesting the extra charge produced in Fe
2O
3. The charges produced in the ZnFe
2O
4 can transfer to the Fe
2O
3 and then move to the electrode contact.
In the study, the preparation, analysis, and photoelectrochemical properties of ZnFe2O4-Fe2O3 heterostructure were systematically investigated, achieving an enhanced light absorption and highest photocurrent generation in ZnFe2O4-Fe2O3 heterostructure.
3. Results and Discussion
The crystalline structure of synthesized ZnFe
2O
4 (Z), Fe
2O
3 (F), and ZnFe
2O
4-Fe
2O
3 (ZF) nanostructures are shown in
Figure 2.
Figure 2 shows an XRD analysis of Z nanostructures, observing a cubic crystalline structure as per JCPDF card No.:89-4926 with the space group of Fd-3m. The reflected peak positions were noticed at 18.1°, 29.9°, 35.3°, 37.0°, 42.8°, 53.2°, 56.7°, 62.2°, and 73.5° with a (h l k) planes of (111), (220), (311), (222), (400), (422), (511), (440), and (533), demonstrating an efficient synthesis of Z nanostructures without any other impurities [
7]. The phase analysis of F nanostructures, shown in
Figure 2, specifies a rhombohedral crystalline structure as per JCPDF card No.:79-0007 with the space group of R-3c. The characteristic peaks of F were noticed at 24.2°, 33.2°, 35.7°, 40.9°, 49.6°, 54.1°, 57.7°, 62.5°, 64.1°, 72.0°, and 75.5° with a (h l k) planes of (012), (104), (110), (113), (024), (116), (122), (214), (300), (1010), and (220) representing an efficacious preparation of F nanostructures without any other impurities [
8]. Further, the ZF heterostructure shows a combination of XRD peaks in pristine Z and F samples, demonstrating the same crystalline structure with strong interaction among the structures, as shown in
Figure 2. No impurities were noticed during the formation of heterostructures, which signifies the quality of the synthesized samples. This strong interaction that occurred in the heterostructure may improve the charge carrier mechanisms, which are more beneficial for achieving enhanced current densities.
SEM analysis of synthesized ZnFe
2O
4 (Z), Fe
2O
3 (F), and ZnFe
2O
4-Fe
2O
3 (ZF) nanostructures were shown in
Figure 3.
Figure 3a shows an irregular sizes of nanoparticles nanostructure of Z samples, with the particle sizes ranging from ~14 nm to 35 nm, respectively.
The morphology of synthesized F samples shown in
Figure 3b shows an irregular shape of nanoparticles nanostructure. ZF heterostructure shows similar morphology to pristine samples with strong interaction among the Z and F nanostructures, as shown in
Figure 3c. In addition, to investigate the more detailed morphology of synthesized ZF heterostructure, the HR-TEM analysis was performed (
Figure 4a–c).
Figure 4a,b shows a clear strong interaction among the pristine Z and F samples with a lattice fringe width of 0.489 nm and 0.252 nm. The selected area electron diffraction pattern of the ZF sample, shown in
Figure 4c, observed a ring pattern with the combination of Z and F nanostructures. These high-resolution morphology analyses agree well with the SEM and XRD analyses.
The optical bandgap of the synthesized ZnFe
2O
4 (Z), Fe
2O
3 (F), and ZnFe
2O
4-Fe
2O
3 (ZF) nanostructures were shown in
Figure 5a. The estimated optical bandgap of 2.05, 1.97, and 2.01 eV was achieved for Z, F, and ZF nanostructures. These obtained bandgap values are well-matched with the reported literature [
9,
10]. The ZF structures changing the bandgap may be due to alteration of sizes and oxygen vacancies. Additionally, the ZF bandgap changes are due to the alteration of heterostructure band edges due to the static electric field-induced potential energy and strain-induced deformation potential.
The XPS analysis of ZF nanostructures was shown in
Figure 5b–e. The XPS survey spectra consists only of the synthesized heterostructure elemental peaks, which indicates the purity of the nanostructures, as represented in
Figure 5b. Further, to investigate the electronic states of the heterostructure, the core-level peaks were recorded, as shown in
Figure 5c–e. For ZF nanostructures, the deconvoluted peaks of Zn2p showed spin-orbit split peaks with a distance of ~23.1 eV and binding energies of ~1020.3 and ~1043.4 eV, ascribed to the Zn2p
1/2 and Zn2p
3/2 states of Zn
2+ in the ZF nanostructures (
Figure 5c). The deconvoluted Fe2p peaks of ZF nanostructures were shown in
Figure 5d, with binding energies positioned at 709.9, 712.3, 718.1, 723.3, 726.1, and 731.9 eV, allotted to Fe2p
3/2, Fe2p
1/2, and satellite peaks of Fe
3+. Further, the O1s peaks of ZF nanostructures are shown in
Figure 5e and the energy peaks are located at 528.9 and 530.6 eV, which are attributed to the bonded lattice oxygen and adsorbed oxygen.
The impedance analysis of the synthesized samples was performed to understand the charge transfer behavior under the dark and light conditions in 0.1 M KOH aqueous electrolyte. The recorded Nyquist plots for ZnFe
2O
4 (Z), Fe
2O
3 (F), and ZnFe
2O
4-Fe
2O
3 (ZF) nanostructures under light ON/OFF states in 0.1 M KOH electrolyte were shown in
Figure 6. In general, the Nyquist plots exhibit three regions: (1) contact resistance region at the lower applied frequency, (2) charge kinetics region at the mid of the applied frequency, and (3) diffusion region at the higher applied frequency (
Figure 6a). Herein, the recorded Nyquist plots for Z, F, and ZF nanostructures exhibited three regions under both the dark and light state at the applied frequency range of 7 MHz to 1 Hz (
Figure 6b). The radius of the semicircle in the charge kinetics region varied for all the photoelectrodes under dark and light states. However, in the light state, the radius of the semicircle is significantly smaller than that of the dark state for all the electrodes in 0.1 M KOH, demonstrating that the fabricated electrodes respond well to the incident light in the three-electrode setup. The smallest radius of the semicircle was noticed for the ZF electrode than that of other Z and F electrodes, indicating that the ZF electrode may exhibit a better charge transfer mechanism and could generate enhanced photocurrents under illumination. To explore this in detail, the recorded Nyquist plots were fitted with the physical equivalent circuit, and the fitted circuit for all the prepared electrodes is shown in the inset of
Figure 6b. The circuit consists of R1, R2, R3, C1, and C3, referring to a resistance due to the interface of 0.1 M KOH electrolyte and the electrode surface, bulk catalyst charge-transport resistance, charge-transfer resistance, bulk catalyst capacitance, and Helmholtz capacitance, as given in
Table 1. The R1 values should be lower for attaining good charge transportation among the surface of the fabricated electrode and the chosen electrolyte to achieve higher photocurrents via photoelectrochemical activity. In the light state, the synthesized electrodes showed lower solution resistance values than that in the dark state. The lowest R1 value of 16.92 Ω was observed under a light state for ZF heterostructures than that of other electrodes in both dark and light states, signifying that the ZF nanostructures have good contact with the electrolyte at the interface of the fabricated electrode surface and the KOH aqueous electrolyte, which may increase the charge carriers’ movement at the solid–liquid interface. Additionally, this allows charge carriers into electrolytes for the further catalytic process without accumulating at the junction. The R2 values of the synthesized electrodes showed a lower resistance in the light state than that in the dark state. The lowest value of 22.98 Ω was achieved for the ZF electrode under a light state compared with Z and F electrodes, indicating that the ZF electrode exhibits minimized grain boundaries and effective charge separation [
11]. The charge transfer resistance of the synthesized electrodes showed a lower light state than that of the dark state, which can be observed in
Table 1. The ZF heterostructures showed the lowest R3 value of 9.41 kΩ under the light state than that of other Z and F electrodes, which signifies that the ZF has a good transfer mechanism and may be beneficial for getting a higher catalytic activity under illumination conditions. The capacitance values of the synthesized Z, F, and ZF electrodes were higher in the light state than that in the dark state. The ZF nanostructures showed a maximum C1 value of 8.06 nF compared to Z and F photoelectrodes, due to the formation of the heterostructure that evaded charge buildup at the solid–liquid interface. The Helmholtz capacitance values of the synthesized photoanodes specified the charge transfer capacity of the electrode surface to the KOH electrolyte solution. The higher C3 value of 6.87 μF for ZF heterostructure under light state compared to Z and F anodes indicates a larger charge carrier buildup at the ZF surface/0.1 M KOH interface than at the Z and F anodes [
12]. Therefore, the above analysis suggests that the ZF heterostructure anode can generate improved photocurrents under illumination in the 0.1 M KOH. Additionally, under dark and light states, the Bode and phase plots were recorded for Z, F, and ZF electrodes in 0.1 M KOH electrolyte, as shown in
Figure 6c,d. The ZF heterostructures showed a shifted impedance toward the low frequencies compared with the Z and F samples, which may be associated with the rapid generation and improved charge carriers’ transportation. This improvement was equitable for decreasing the recombination rate in heterostructures [
13].
Figure 6d shows a Bode phase analysis of Z, F, and ZF anodes under both conditions in 0.1 M KOH. The ZF heterostructure showed a shifted frequency peak towards a smaller value, which advised a superior lifetime of charges than that of Z and F anodes. This designated that the uniform distribution of catalysts enhances the charge separation and improves the charge lifetime [
14].
Tafel plots of the fabricated Z, F, and ZF anodes were recorded to realize the hydrogen evolution mechanism in 0.1 M KOH aqueous electrolyte under dark and light conditions. The plotted Tafel data for the synthesized Z, F, and ZF anodes were presented in
Figure 7. All the nanostructures exhibited a shift in voltage towards the anode under a light state compared with the dark state. It signifies that the anodes produced a large number of charges, which significantly helps to improve the catalytic activity. Further, the Tafel plots of the anodes under the light ON/OFF conditions in the electrolyte were fitted to attain the Tafel slopes, limiting current density (J
L) and exchange current density (J
p) (
Table 2). Usually, a smaller Tafel slope indicates that the anodes need less applied voltages to generate induced charges. The Tafel slopes achieved for the electrodes under the light states showed less than that of the dark state for the anodes. However, the lowest Tafel slopes of 58.8 mVdec
−1 were achieved for the ZF anode, which is much smaller than that of Z and F anodes in any conditions, representing that the anode produced huge, induced charges, and hence, that the ZF anode has a fast charge kinetics [
15]. The estimated J
L and J
p values of the anodes under dark and light states in 0.1 M KOH electrolytes are given in
Table 2. The J
L values of the ZF anode showed a lower value compared to the Z and F anodes under the ON/OFF conditions. The lowest J
L and J
p of −0.04 and −1.70 mAcm
−2 were achieved for ZF under the light ON condition, demonstrating that ZF offers more of a transfer rate. Hence, ZF may show improved catalytic activity under illumination.
The sweep voltammetry analysis of Z, F, and ZF electrodes is shown in
Figure 8a. A sharp increment in photocurrent was noticed from ~0.6 V to 1 V in the applied potential for all the electrodes under both the light/dark states. However, the photocurrents generated by the fabricated electrodes showed higher current densities in the light condition than that in the dark state. The pristine Z electrode generated almost null photo-induced currents under illumination. However, the heterostructured sample showed a significantly improved generation of photo-induced current densities compared to pristine Z and F samples. The maximum photo-induced current density of 2.41 mAcm
−2 was observed for the ZF electrode under a light state due to lower solution resistance and charge transfer resistance. The obtained photoanode performance was compared with the reported literatures, given in
Table 3.
CA analysis of the fabricated Z, F, and ZF anodes were examined at various applied potentials of 0.3, 0.5, and 0.5 V in 0.1 M KOH liquid electrolyte, as shown in
Figure 8b–d. The synthesized Z, F, and ZF electrodes showed excellent switching behavior during light ON/OFF states. The applied potential has a significant effect on the generation of photocurrents under light conditions. The photocurrent generation increased with applied voltages up to 0.5 V and then decreased at a higher applied potential of 0.7 V. The maximum photocurrent density was shown at an applied voltage of 0.5 V for all the electrodes. However, the heterostructure of the ZF electrode showed the highest current densities in all the applied voltages compared to that of the Z and F electrodes. This could be due to the construction of heterostructures with a combination of Z and F, decreased resistance values, improved active sites, transfer kinetics, lower recombination rate, and increased capacitance behavior. Therefore, the ZF heterostructure generated the highest photocurrents at an applied voltage of 0.5 V when compared with the others under various conditions. The produced currents of Z, F, and ZF anodes at different applied voltages are as follows: 0.7 V < 0.5 V > 0.3 V.
The photocurrent generation of the heterostructure is schematically represented in
Figure 9. Under ON condition, the photoanode absorbs light energy in terms of photons, generates a cloud of electrons and holes on the photoanode surface, and further separation of charges occurs due to the variation of work functions. The positive charges move to the surface of the electrode and produces oxygen from the liquid electrolyte. At the same time, the generated negative charge carriers move towards the counter electrode and generate a hydrogen. Therefore, the heterostructure increases the light absorption ability due to the synergistic effect of the electrodes [
23,
24], thereby increasing the generation of charge pairs and enhancing the catalytic activity.