Next Article in Journal
Facile Synthesis of Sn/Nitrogen-Doped Reduced Graphene Oxide Nanocomposites with Superb Lithium Storage Properties
Next Article in Special Issue
Preparation of TiO2 and Fe-TiO2 with an Impinging Stream-Rotating Packed Bed by the Precipitation Method for the Photodegradation of Gaseous Toluene
Previous Article in Journal
Electrospun Bimetallic NiCr Nanoparticles@Carbon Nanofibers as an Efficient Catalyst for Hydrogen Generation from Ammonia Borane
Previous Article in Special Issue
Ag3PO4 Deposited on CuBi2O4 to Construct Z-Scheme Photocatalyst with Excellent Visible-Light Catalytic Performance Toward the Degradation of Diclofenac Sodium
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Nanomaterials
Volume 9
Issue 8
10.3390/nano9081083
nanomaterials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Enhancement in Photoelectrochemical Performance of Optimized Amorphous SnS2 Thin Film Fabricated through Atomic Layer Deposition

by
Weiguang Hu
1,
Truong Thi Hien
2,
Dojin Kim
2 and
Hyo Sik Chang
1,*
1
Graduate School of Energy Science and Technology, Chungnam National University, Daejeon 305–764, Korea
2
Department of Materials Science and Engineering, Chungnam National University, Daejeon 305–764, Korea
*
Author to whom correspondence should be addressed.
Nanomaterials 2019, 9(8), 1083; https://doi.org/10.3390/nano9081083
Submission received: 1 July 2019 / Revised: 20 July 2019 / Accepted: 26 July 2019 / Published: 28 July 2019
(This article belongs to the Special Issue Photocatalytic Nanomaterials)
Browse Figures
Versions Notes

Abstract

:
Two-dimensional (2D) nanomaterials have distinct optical and electrical properties owing to their unique structures. In this study, smooth 2D amorphous tin disulfide (SnS2) films were fabricated by atomic layer deposition (ALD), and applied for the first time to photoelectrochemical water splitting. The optimal stable photocurrent density of the 50-nm-thick amorphous SnS2 film fabricated at 140 °C was 51.5 µA/cm2 at an oxygen evolution reaction (0.8 V vs. saturated calomel electrode (SCE)). This value is better than those of most polycrystalline SnS2 films reported in recent years. These results are attributed mainly to adjustable optical band gap in the range of 2.80 to 2.52 eV, precise control of the film thickness at the nanoscale, and the close contact between the prepared SnS2 film and substrate. Subsequently, the photoelectron separation mechanisms of the amorphous, monocrystalline, and polycrystalline SnS2 films are discussed. Considering above advantages, the ALD amorphous SnS2 film can be designed and fabricated according to the application requirements.

Graphical Abstract

1. Introduction

One of the effective approaches to overcome the issues related with the increasing energy crisis and environmental pollution is water splitting using the “endless” sunlight to produce and utilize clean energy hydrogen (H2) [1,2]. Therefore, it is essential to propose novel cheap and environmentally friendly materials that can efficiently utilize the sunlight. Recently, an increasing number of two-dimensional (2D) materials have been studied, which are suitable for water splitting applications. Their 2D structures and large specific surface areas are beneficial for the carrier transport and interface electrochemical reaction [3,4]. For example, hydrogen gas has been successfully prepared using 2D materials, such as CdS [5], MoS2 [6,7], and SnS2 [8,9]. Among them, SnS2 is an n-type semiconducting material with a layered cadmium iodide-(CdI2)-type structure. It can absorb visible light owing to its suitable optical band gap and has a high carrier mobility, which is beneficial for a rapid transmission of photon-generated carriers. In addition, considering its low price, nontoxicity, and good stabilities in neutral and even acid solutions, SnS2 is an ideal material for photoelectrochemical (PEC) water splitting [8,9]. However, there are few literatures on PEC water splitting with SnS2 as the catalyst. To prepare cost-effective, highly active, and simply manufactured SnS2 films is still a challenge.
The properties of SnS2 significantly vary with the morphology and preparation method. The reported SnS2 morphologies mainly consist of quantum dots [10], nanoparticles [11,12], nanowires [13], flower-like structures [12,14,15,16], and nanosheets (NSs) [8,9,11,12,14]. In addition, SnS2 can be combined with other elements and the morphologies can change to nanoplates [17] and nanospheres [18]. Various methods have been used to prepare SnS2 crystal structures, including the solvothermal method [8,14,16], hydrothermal method [9,10,12,19], Sn metal sulfuration [13], chemical vapor transport [20,21], chemical vapor deposition [22,23], and atomic layer deposition (ALD) [24,25]. Among them, ALD is a popular film fabrication method, particularly suitable for the fabrication of 2D materials. Firstly, based on sequential self-limiting reactions, ALD provides an excellent conformality and uniformity over large areas. Then, ALD provides an atomic-scale thickness control and tunable film composition, which can control the performance of the film. Moreover, as ALD processes are maintained at modest temperatures (<350 °C), it is easy to obtain an amorphous film [26,27]. In contrast to crystalline films, amorphous films have no cleavage surface. They have better toughnesses and can tightly bind to the substrate in large areas, so some performances may be better than those of crystals [28,29]. Amorphous MoSx has been used to prepare high-quality photoelectrode for PEC sensing [29] and highly active hydrogen evolution catalysts [30]. However, no PEC applications of amorphous SnS2 have been reported.
In this study, ALD was used to prepare smooth 2D amorphous SnS2 thin films at low temperatures. Through field-emission scanning electron microscopy (FESEM) and atomic force microscopy (AFM) observations, we confirmed that the amorphous SnS2 films were smooth and were in close contact with the substrate. X-ray diffraction (XRD), Raman spectroscopy, X-ray photoelectron spectroscopy (XPS), and high-resolution transmission electron microscopy (HRTEM) analyses showed that amorphous SnS2 films were obtained when the preparation temperature was below 140 °C. By optimizing its optical band gap and thickness, the optimal stable photocurrent density (0.8 V vs. saturated calomel electrode (SCE)) of the 50-nm-thick amorphous SnS2 film prepared at 140 °C was 51.5 µA/cm2, which is better than those of most polycrystalline SnS2 films. The equivalent circuit was obtained using electrochemical impedance spectroscopy (EIS). Last, schematic diagrams of photoelectron separation and PEC water splitting are presented. These results indicate that the ALD amorphous SnS2 films are promising for PEC water splitting and other applications involving photoelectric transformation.

2. Materials and Methods

2.1. Tin Disulfide Film Synthesis and Characterization

Tin sulfide (SnxSy) films were deposited by ALD (LucidaTM D, NCD, Daejeon, Korea) on a glass substrate and silicon wafer using a tetrakis (dimethylamino) tin (IV) (TDMASn: 99.99%, Trust Chem, Seoul, Korea) precursor and hydrogen sulfide (H2S mixture with nitrogen gas (N2), H2S: 10.04%) as tin (Sn) and sulfide (S) sources, respectively. N2 was employed to carry the precursors and remove excess precursors or reaction products. The flow rate of the N2 gas was set to 50 sccm by a mass flow controller to maintain the reaction pressure of 0.38 Torr. The N2 purge time between Sn and S pulses was 12.0 s. The H2S flow rate was set to 30 sccm. Under a sufficient S supply, various Sn pulse times (0.2, 0.5, 1.0, 1.5, 2.0, 3.0, and 5.0 s) were tested until the reaction reached self-saturation. The optimal S pulse time was obtained with the same approach. The optimized ALD growth cycle was defined by the following sequence; Sn pulse (2.0 s), N2 purge (12.0 s), H2S pulse (1.0 s), then N2 purge (12.0 s), at 140 °C. Subsequently, approximately 50 nm thick SnxSy films were fabricated at deposition temperatures in the range of 60 to 180 °C. Their thicknesses and surface morphologies were observed using ultrahigh-resolution SEM (S-4800, Hitachi, Ltd., Tokyo, Japan). The surface roughness was measured by AFM (Park XE7, Park Systems, Suwon, Korea). The crystal structures and phases of the films were measured by high-resolution XRD (D8DISCOVER, Bruker AXS Inc., Madison, Wisconsin, USA) using Cu Kα radiation (1.5406 Å), high-performance Raman spectrometry (LabRAM HR-800, HORIBA Jobin Yvon, Montpellier, France) using a 633-nm laser line, and XPS (MultiLab 2000, Thermo Scientific, Seoul, Korea). The crystal structure and chemical composition was confirmed by HRTEM (JEM-2100F, JEOL USA, Inc., Peabody, MA, USA).

2.2. Optical Properties of the Amorphous SnS2 Films

In order to analyze the effects of the growth temperature on the optical properties of the amorphous SnS2 films, thin films were fabricated at different temperatures (60, 100, and 140 °C) on glass substrates. Their transmittances and absorbances were then measured by UV–Vis spectroscopy (UV-2600, Shimadzu Corporation, Tokyo, Japan) in the wavelength range of 300 to 1400 nm, and their optical band gaps were analyzed.

2.3. Photoelectrochemical Performances of the Amorphous SnS2 Films

Amorphous SnS2 films with different thicknesses (25, 50, 75, and 100 nm) were deposited on fluorine-doped tin dioxide (FTO) transparent conductive glass substrates at different temperatures (60, 100, and 140 °C). Specimens with effective areas of 1 × 1 cm2 were then prepared and used as working electrodes. The PEC measurements were performed in a conventional three-electrode system using an electrochemical workstation (AUT84826, Metrohm AG, Herisau, Switzerland) under an AM 1.5G simulated sunlight illumination (100-W Xe arc lamp, model 11002 SunLiteTM Solar Simulators, Abet Technologies, Inc., Milford, CT, USA). A platinum (Pt) wire and SCE were used as the counter and reference electrodes, respectively. Linear sweep voltammograms under intermittent illumination and dark conditions were measured with a scanning rate of 5 mV/s in the range of −0.7 to 0.9 V (vs. SCE). The EIS measurements were carried out in the frequency range of 1000 to 0.1 kHz at a bias potential of 0.8 V (vs. SCE) under illumination. In addition, the stability of the photocurrent response was evaluated at 0.8 V (vs. SCE) during 360 s. The measurement of incident photon-to-current conversion efficiency (IPCE) (Model 10500 low cost solar simulator, Abet Technologies, Inc., Milford, CT, USA) was performed in a bias potential of 0 V (vs. reversible hydrogen electrode (RHE)). All of the above analyses were carried out at room temperature.

3. Results and Discussion

3.1. Tin Disulfide Film Deposition

3.1.1. Atomic layer deposition Model

The self-saturation state of the ALD process can be achieved by alternately changing the pulse times of the tin and sulfur sources. The optimal SnxSy film deposition sequence of one ALD cycle was determined to be: Sn pulse (2.0 s), N2 purge (12.0 s), H2S pulse (1.0 s), then N2 purge (12.0 s). Under this deposition condition, the growth rates of the SnxSy films at different deposition temperatures are shown in Figure 1. The growth rate decreased with the increase in the deposition temperature in the range of 60 to 180 °C, which is similar to a previous result for tin sulfides fabricated by ALD using the same Sn source [24]. The inset shows the variation in the film thickness with the number of growth cycles at 140 °C. The thickness was proportional to the number of growth cycles, which indicated that the SnxSy films were deposited during the ALD.

3.1.2. Surface Morphology and Roughness

The SnxSy films were strongly adhered to all of the substrate surfaces at deposition temperatures of, or lower than, 140 °C. These films on the glass were pale yellow. The color changed with the increase in the deposition temperature, as shown in Figure S1 (Supporting information). At 180 °C, the adherence of the SnxSy films was low, and the color turned to black gray. All of the SnxSy films seemingly remained smooth, shiny, and pinhole-free.
The microscale surface morphologies of the SnxSy films deposited on the silicon wafer were observed using FESEM. As shown in Figure 2a, the SnxSy film grown at 140 °C was very smooth and uniform (inset). Its surface and cross-section morphologies were similar as the fabrication temperature was lower. However, at 180 °C, an irregular distribution of flake grains was observed on the surface, and the film’s continuous but fluctuant cross-section exhibited a slightly nonuniform thickness, as shown in Figure 2b. Figure 2c shows an AFM image and surface roughness measurement results of the SnxSy film grown at 140 °C on the silicon wafer. The root mean square (RMS) roughness is 0.401 nm, which indicates that the film is very flat.

3.1.3. Crystal Structure and Phase Analysis

The XRD patterns showed that the crystal structures of the SnxSy films transformed from the amorphous into the SnS orthorhombic structure when the deposition temperature was increased to 180 °C. As shown in Figure 3a, no peak was observed at 60, 100, and 140 °C, which indicates that the SnxSy films were amorphous [24]. At 180 °C, an intense peak was observed at 2θ = 31.86°, which reflects the preferential orientation of the SnS film along the (040) plane, according to the Joint Committee on Powder Diffraction Standards (JCPDS) data (No. 39-0354) [31].
The Raman spectra indicated that when the deposition temperature was equal to or lower than 140 °C, the SnxSy films consisted of SnS2, while at 180 °C, they transformed into SnS. As shown in Figure 3b, at the temperatures of 60, 100, and 140 °C, an obvious peak could be observed at 311.5 cm−1, while at 180 °C, peaks were observed at 161.6, 185.4, and 218.6 cm−1. These results are similar to those in previous studies. The Raman spectra have SnS2 bands at 312 and 215 cm−1 and SnS bands at 288, 220, 189, and 163 cm−1, as shown in Figure 3b [32,33].
Figure 3c,d shows the XPS Sn 3d and S 2p peaks of the SnxSy film grown at 140 °C, respectively. The binding energy was calibrated using the C 1s peak (284.5 eV). The XPS Sn 3d5/2 and S 2p3/2 peaks are observed at 486.76 and 161.76 eV, respectively. These values are consistent with those of a previously reported SnS2 (486.6 and 161.6 eV, as shown in Figure 3c,d, respectively) [24].
As shown in Figure 4a, the high-resolution transmission electron microscopy image indicated that ALD SnS2 film deposited at 140 °C had a 2D crystalline structure in an amorphous phase matrix. There were many laminar structures with irregular distribution inside the film. By measuring the distance of the five layers, it had a lattice spacing of 0.589 Å, corresponding to the (001) interplanar distance of hexagonal SnS2 [22]. However, the ordered arrangement was irregularly distributed within a short distance of a few nanometers. Both Sn and S atoms exhibited disordered amorphous structures in the 50 nm thick film and the other two dimensions. Besides, Figure 4b showed that the average ratio of Sn to S atoms was ~1:2, but its fluctuation was very large, indicating that the distribution of tin and sulfur atoms was not very orderly.
In this study, the XRD, Raman spectroscopy, and XPS analyses show that the SnxSy films consisted of amorphous SnS2 when the deposition temperature was equal to or lower than 140 °C. This result is consistent with HRTEM analysis. At 180 °C, the SnxSy films transformed into orthorhombic SnS films with the preferred crystal orientation along the (040) plane. This observation can be explained by the thin film growth mechanism. The thin film growth mechanism is determined by the adsorption process on the substrate supplied by the deposition temperature [24,34,35]. The ALD growth of SnxSy films as a function of temperature in our work was similar to previous study [24].

3.2. Optimization of the Optical Properties

The optical properties of the amorphous SnS2 films grown at different temperatures were measured in the UV–Vis range of 300 to 1400 nm. As shown in Figure 5, the absorbance of the amorphous SnS2 increases with the growth temperature. The optical band gap (Eg) was obtained by measuring the transmittance and using equations α = [ln(1⁄T)]/t and αE = A(E − Eg − Ep)n, where α is the absorption coefficient, T is the transmittance, t is the film thickness, E (hν) is the photon energy, A is a constant, Eg is the optical band gap, and Ep is the phonon energy. For direct transitions (Ep = 0), n is equal to 1/2 for the allowed transition and 3/2 for the forbidden transition. For indirect transitions, n = 2 for the allowed transition and n = 3 for the forbidden transition [24,25,35,36,37]. In this study, the values of α of all of the films obeyed the above equation with n = 1/2, which indicates that all of the optical transitions between the valence and conduction bands were direct allowed transitions. The optical band gap of the amorphous SnS2 film was estimated by determining the intercept of the linear extrapolation with the photon energy for the absorption onset of the (αhν)2 curve. Figure 5 (inset) shows (αhν)2 as a function of hν for each temperature; the results are similar to previous study, which proved by using the ALD with varying deposition temperature to adjust optical band gaps of the SnxSy films [24]. The summaries of crystal structure and optical band gap for each deposition temperature are shown in Table 1.

3.3. Photoelectrochemical Performances and Electrochemical Impedance Spectroscopy

3.3.1. Photoelectrochemical Performances

Linear sweep voltammetry plots of the 50-nm-thick amorphous SnS2 films grown at 60, 100, and 140 °C are shown in Figure 6a. Almost no photocurrent response was observed under dark conditions. However, under illumination, the SnS2 films very quickly responded to light. The photocurrent response increased with the applied voltage. As expected, the photocurrent response was the highest at 140 °C, as the lower optical band gap was beneficial to absorb and utilize more light energy. This result was three times higher than the photocurrent response of the SnS2 film grown at 60 °C. The SnS2 film grown at 140 °C exhibited high light–current density responses of −35.1 and 51.5 µA/cm2 at −0.6 and 0.8 V (vs. SCE), respectively. The light–current density responses were −12.4 and −20.2 µA/cm2 (−0.6 V vs. SCE) and 13.3 and 42.5 µA/cm2 (0.8 V vs. SCE) at 60 and 100 °C, respectively. This indicated that the ALD amorphous SnS2 films could be applied to hydrogen and oxygen evolution reactions, and the PEC performances of ALD amorphous SnS2 films could be optimized by varying the deposition temperature [38]. The amorphous SnS2 films have obvious photocurrent response to a negative voltage, but the photocurrent stability is very low.

3.3.2. Electrochemical Impedance Spectroscopy

In the Nyquist plots of the SnS2 films, the charge transfer control was mainly reflected in the high-frequency area, while the diffusion control was mainly reflected in the low-frequency area. In the typical equivalent circuit of the electrolytic cell, the electrochemical polarization and concentration difference exist simultaneously, as shown in Figure 6b, where Rs is the solution resistance, Cd is the electric double-layer capacitance, Rct is the charge transfer resistance, and Zw is the Warburg impedance [39]. Based on sequential self-limiting reactions, ALD amorphous SnS2 film is excellently uniform and close contact with the substrate over large areas, leading to very small impedance. Moreover, the SnS2 film fabricated at a higher temperature not only absorbs more light energy but also has a smaller impedance, so that the photocurrent density is higher.

3.3.3. Photocurrent Response Stabilities

The stabilities of the photocurrent responses of the films (fabricated at 140 °C) with thicknesses of 25, 50, 75, and 100 nm were evaluated at a voltage of 0.8 V for 360 s. The photocurrent response was initially stable when the film thickness was larger than 50 nm, as shown in Figure 6c. Although the photocurrent density of the film with 25 nm was very high at the moment of illumination (up to 88.0 µA/cm2), it rapidly decreased. When the thickness was larger than 50 nm, the photocurrent density became stable and decreased as the thickness increase. These results are expected; when the thickness of SnS2 film was 25 nm, photogenerated electrons were quickly transported to the electrode. However, the film was very thin so that the photocorrosion rapidly destroyed the double-layer structure. Films thicker than 50 nm could effectively stabilize the photocurrent by reducing the photocorrosion effect. However, the recombination of carrier and hole of the amorphous SnS2 film hindered the effective transmission of the photocurrent, which led to the decrease and stabilization of the photocurrent as the thickness increase. The photocurrent densities were 24.2 and 21.2 µA/cm2 at 75 and 100 nm, respectively. This is consistent with previous studies, which demonstrated that the nonmonotonous behavior of the photocurrent depends on the film thickness. It reaches its maximum under a certain thickness and then tends to stabilize [40,41,42].
In general, an excellent photocatalytic semiconducting material should have a high photoabsorption performance, high separation and transmission rates of photogenerated electrons and holes, and good stability [8]. The optimization of the optical band gap and thickness showed that the 50-nm-thick amorphous film deposited at 140 °C exhibited the best performances. The photocurrent density is higher than those of most crystalline SnS2 films. Furthermore, the measurement results of photoconversion efficiency [43,44,45,46] and the IPCE curve [22,47] of the 50-nm-thick SnS2 film deposited at 140 °C were shown in Figure S2. The maximum photoconversion efficiency (0.014%) was identified at ~0.553 V of bias (vs. SCE), and the highest IPCE value was up to 2.17% at 390 nm (0 V vs. RHE). Table 2 shows the PEC performances of SnS2 films reported in recent years. The photoelectron separation mechanism of these SnS2 films is discussed in Section 3.4.

3.4. Mechanisms of Photoelectron Separation and Photoelectrochemical Water Splitting

3.4.1. Mechanism of Photoelectron Separation

It is well known that the basic characteristics of crystalline materials are the periodic arrangements of their constituent atoms, which could lead to anisotropic physical and chemical properties. However, for amorphous materials, the arrangement of atoms is not regular, and thus they are isotropic. Sun et al. [47] reported that freestanding SnS2 single-layers (three atomic layers’ thickness) exhibited a quite high photocurrent density of 2.75 mA/cm2 at 1.0 V vs. Ag/AgCl, more than 70 times higher than that of bulk SnS2. This is mainly attributed to the very large specific surface area, high percentage of disordered surface atoms, significantly better grain boundary connectivity, and intimate contact with the substrate. In addition, Guangbo Liu et al. [22] showed that vertically aligned 2D SnS2 NSs with full coverage on FTO (SnS2⊥FTO) exhibited a high photocurrent density of 1.73 mA/cm2 at 1.4 V vs. RHE, which is significantly higher than that of their parallel counterpart photoelectrode (SnS2//FTO). A schematic of the photoelectron transfer to the electrode is shown in Figure 7a. The good results can be attributed mainly to the SnS2 vertical growth and close contact with the substrate. The results indicated that the single-crystal structure is very favorable for the rapid separation and transfer of photoelectrons, as there are few obstacles to the movement of electrons within the crystal and the tight bonding with the substrate can reduce the resistance. However, it is usually very difficult to fabricate SnS2 in large areas with an ultrathin single-crystal structure or to control the growth direction of all of the crystalline SnS2 regions.
Jing et al. [12] studied PEC properties of SnS2 nanoparticles, SnS2 NSs, and 3D flower-like SnS2, with photocurrent densities of 13, 10, and 7.5 µA/cm2 at 1.0 V (vs. Ag/AgCl), respectively. SEM images showed that the SnS2 films were formed by random superposition of many small particles, NSs, or flower-like nanostructures. The highest photocurrent density of the SnS2 nanoparticles is attributed mainly to the best contact surface, highest interaction force, and preferred growth of crystal planes, compared with the other two materials. Monodisperse SnS2 NSs have been studied by Yu et al. [8], while Cheng et al. [9] studied vertical SnS2 NSs, whose photocurrent densities were 11.7 and 16.6 µA/cm2 at 0.8 and 0 V (vs. SCE), respectively. Their SEM morphologies are similar to those of the SnS2 NSs and 3D flower-like SnS2 studied by Jing, but the coverage seems to be better. A schematic of the photogenerated electron transfer from the NS to the electrode is shown in Figure 7b [8,12]. The photocurrent densities in these studies are significantly lower than that of the above monocrystalline SnS2. This can be attributed mainly to the superposition of many crystal particles, which lead to a large number of grain boundaries, as well as to the decrease in the tightness with the substrate. Both of these factors significantly affect the separation and transmission of photogenerated electrons.
A schematic of the photogenerated electron transfer from amorphous SnS2 to the electrode is shown in Figure 7c. It is well known that the arrangement of atoms is not regular in amorphous materials. The ALD amorphous SnS2 film is closely connected with the substrate, without any influence of grain boundaries. These facilitate charge carriers transfer between the film and conductive substrate [29]. However, the photogenerated electrons are also easy to recombine inside the film. Hence, as the thickness decreases, more photoelectrons move to the electrode before recombining. Considering the above-mentioned effects of light absorption and photocorrosion, the optimal stable photocurrent density was acquired at 50 nm deposited at 140 °C. This value is better than that of the above polycrystalline SnS2. It is worth noting that the working electrode structure, solution, and illumination conditions are different in each experiment. Therefore, we cannot directly accurately compare the photocurrent density values obtained from the different experimental systems. However, the above experiments confirmed that the crystal structure, SnS2 morphology, and state of bonding with the substrate have large impacts on the photocurrent response. In addition, in the experiment in this study, the amorphous films prepared by the ALD not only avoid the influence of defects such as grain boundaries, but also contribute to the improvement in photocurrent density by the smooth film tightly bound to the substrate. Furthermore, the photocurrent density was threefold increased by adjusting the optical band gap and thickness of the film. Therefore, it was reasonable that the 50-nm-thick amorphous SnS2 film grown at 140 °C exhibited the higher photocurrent density.

3.4.2. Mechanism of Photoelectrochemical Water Splitting

Based on the above discussion and experimental results, the effect of SnS2 in PEC water splitting can be illustrated. As shown in Figure 7d, the complete PEC water splitting reaction involves three main processes. The first process is light absorption by the SnS2 photoelectrode. A photogenerated electron–hole pair is created as SnS2 absorbs a photon with an energy larger than its optical band gap. Therefore, the optical band gap is an important factor determining the degree of light energy absorption, which could be optimized in this study by adjusting the temperature of the SnS2 fabrication. The second process is the separation and transmission of photogenerated electron-hole pairs. These electrons are transported to the FTO electrode after the excitation to the conduction band, while the holes are in the valence band. In this process, the effective separation and transmission are necessary as electron–hole pairs can recombine at the surface or in the bulk. Therefore, the SnS2 film thickness is optimized. The third process is the surface reaction, where holes can cause an oxygen evolution reaction in the solution [38,48].

4. Conclusions

SnS2 amorphous films were fabricated by ALD and applied for the first time to PEC experiments. The 50-nm-thick SnS2 film fabricated at 140 °C had the maximum photocurrent density of 51.5 µA/cm2 at 0.8 V (vs. SCE), which is better than those of most polycrystalline SnS2 films. This demonstrated that the amorphous SnS2 films could be used for PEC water splitting. Furthermore, by comparing the mechanism of the photogenerated electron transfer from the amorphous, monocrystalline, and polycrystalline SnS2 to the electrode, the reason for high photocurrent density of thin amorphous SnS2 film was explained theoretically. Last, the schematic of the PEC water splitting mechanism was presented.

Supplementary Materials

The following are available online at https://www.mdpi.com/2079-4991/9/8/1083/s1. Figure S1: Photos of 50-nm-thick SnxSy films which in the growth of the glass substrates at different deposition temperatures. Figure S2: Photoconversion efficiency (a) and IPCE curve (b) of the 50-nm-thick SnS2 film deposited at 140 °C.

Author Contributions

Conceptualization, W.H. and H.S.C.; Investigation, W.H. and T.T.H.; Resources, D.K. and Chang, H.S.; Writing—original draft preparation, W.H.

Funding

This research was funded by a Korea Institute of Energy Technology Evaluation and Planning (KETEP) grant funded by the Korea government (MOTIE) (No. 20173010012940); the National Research Lab program of the National Research Foundation of Korea (NRF) (No. 2018R1A2A1A05023126).

Conflicts of Interest

The authors declare no conflicts of interest.

References

  1. Kemppainen, E.; Halme, J.; Lund, P. Physical Modeling of Photoelectrochemical Hydrogen Production Devices. J. Phys. Chem. C 2015, 119, 21747–21766. [Google Scholar] [CrossRef] [Green Version]
  2. Hou, Y.; Vidu, R.; Stroeve, P. Solar Energy Storage Methods. Ind. Eng. Chem. Res. 2011, 50, 8954–8964. [Google Scholar] [CrossRef]
  3. Butler, S.Z.; Hollen, S.M.; Cao, L.; Cui, Y.; Gupta, J.A.; Gutiérrez, H.R.; Heinz, T.F.; Hong, S.S.; Huang, J.; Ismach, A.F.; et al. Progress, Challenges, and Opportunities in Two-Dimensional Materials beyond Graphene. ACS Nano 2013, 7, 2898–2926. [Google Scholar] [CrossRef] [PubMed]
  4. Su, T.; Shao, Q.; Qin, Z.; Guo, Z.; Wu, Z. Role of Interfaces in Two-Dimensional Photocatalyst for Water Splitting. ACS Catal. 2018, 8, 2253–2276. [Google Scholar] [CrossRef]
  5. Xu, Y.; Zhao, W.; Xu, R.; Shi, Y.; Zhang, B. Zhang, Synthesis of Ultrathin CdS Nanosheets as Efficient Visible-Light-Driven Water Splitting Photocatalysts for Hydrogen Evolution. Chem. Commun. 2013, 49, 9803–9805. [Google Scholar] [CrossRef] [PubMed]
  6. Xie, J.; Zhang, H.; Li, S.; Wang, R.; Sun, X.; Zhou, M.; Zhou, J.; Lou, X.W.; Xie, Y. Defect-Rich MoS2 Ultrathin Nanosheets with Additional Active Edge Sites for Enhanced Electrocatalytic Hydrogen Evolution. Adv. Mater. 2013, 25, 5807–5813. [Google Scholar] [CrossRef]
  7. Oh, S.; Kim, J.B.; Song, J.T.; Oh, J.; Kim, S.H. Atomic Layer Deposited Molybdenum Disulfide on Si Photocathodes for Highly Efficient Photoelectrochemical Water Reduction Reaction. J. Mater. Chem. A 2017, 5, 3304–3310. [Google Scholar] [CrossRef]
  8. Yu, J.; Xu, C.Y.; Ma, F.X.; Hu, S.P.; Zhang, Y.W.; Zhen, L. Monodisperse SnS2 Nanosheets for High-Performance Photocatalytic Hydrogen Generation. ACS Appl. Mater. Interfaces 2014, 6, 22370–22377. [Google Scholar] [CrossRef]
  9. Cheng, Z.; Wang, F.; Shifa, T.A.; Liu, K.; Huang, Y.; Liu, Q.; Jiang, C.; He, J. Carbon Dots Decorated Vertical SnS2 Nanosheets for Efficient Photocatalytic Oxygen Evolution. Appl. Phys. Lett. 2016, 109, 053905. [Google Scholar] [CrossRef]
  10. Tu, J.R.; Shi, X.F.; Lu, H.W.; Yang, N.X.; Yuan, Y.J. Facile Fabrication of SnS2 Quantum Dots for Photoreduction of Aqueous Cr(VI). Mater. Lett. 2016, 185, 303–306. [Google Scholar] [CrossRef]
  11. Liu, J.H.; Huang, G.F.; Huang, W.Q.; Miao, H.; Zhou, B.X. Morphology-Controlled SnS2 Nanostructures Synthesized by Refluxing Method with High Photocatalytic Activity. Mater. Lett. 2015, 161, 480–483. [Google Scholar] [CrossRef]
  12. Jing, L.; Xu, Y.; Chen, Z.; He, M.; Xie, M.; Liu, J.; Xu, H.; Huang, S.; Li, H. Different Morphologies SnS2 Supported on 2D G-C3N4 for Excellent and Stable Visible Light Photocatalytic Hydrogen Generation. ACS Sustain. Chem. Eng. 2018, 6, 5132–5141. [Google Scholar] [CrossRef]
  13. Lin, Y.T.; Shi, J.B.; Chen, Y.C.; Chen, C.J.; Wu, P.F. Synthesis and Characterization of Tin Disulfide (SnS2) Nanowires. Nanoscale Res. Lett. 2009, 4, 694–698. [Google Scholar] [CrossRef] [PubMed]
  14. Li, M.; Liu, E.; Hu, H.; Ouyang, S.; Xu, H.; Wang, D. Surfactant-Free Synthesis of Single Crystalline SnS2 and Effect of Surface Atomic Structure on the Photocatalytic Property. Int. J. Photoenergy 2014, 2014, 1–7. [Google Scholar]
  15. Zhao, W.; Wei, Z.; Ma, L.; Liang, J.; Zhang, X. Ag2S Quantum Dots Based on Flower-Like SnS2 as Matrix and Enhanced Photocatalytic Degradation. Materials 2019, 12, 582. [Google Scholar] [CrossRef] [PubMed]
  16. Ansari, S.A.; Cho, M.H. Growth of Three-Dimensional Flower-Like SnS2 on G-C3N4 Sheets as an Efficient Visible-Light Photocatalyst, Photoelectrode, and Electrochemical Supercapacitance Material. Sustain. Energ. Fuels 2017, 1, 510–519. [Google Scholar] [CrossRef]
  17. Yin, K.; Zhang, M.; Hood, Z.D.; Pan, J.; Meng, Y.S.; Chi, M. Self-Assembled Framework Formed during Lithiation of SnS2 Nanoplates Revealed by in Situ Electron Microscopy. Acc. Chem. Res. 2017, 50, 1513–1520. [Google Scholar] [CrossRef]
  18. Wang, J.; Luo, C.; Mao, J.; Zhu, Y.; Fan, X.; Gao, T.; Mignerey, A.C.; Wang, C. Solid-State Fabrication of SnS2/C Nanospheres for High-Performance Sodium Ion Battery Anode. ACS Appl. Mater. Interfaces 2015, 7, 11476–11481. [Google Scholar] [CrossRef]
  19. Kovacic, M.; Katic, J.; Kusic, H.; Bozic, A.L.; Hukovic, M.M. Elucidating the Photocatalytic Behavior of TiO2-SnS2 Composites Based on Their Energy Band Structure. Materials 2018, 11, 1041. [Google Scholar] [CrossRef]
  20. Song, H.S.; Li, S.L.; Gao, L.; Xu, Y.; Ueno, K.; Tang, J.; Cheng, Y.B.; Tsukagoshi, K. High-Performance Top-Gated Monolayer SnS2 Field-Effect Transistors and Their Integrated Logic Circuits. Nanoscale 2013, 5, 9666–9670. [Google Scholar] [CrossRef]
  21. Burton, L.A.; Whittles, T.; Hesp, D.; Linhart, W.M.; Skelton, J.M.; Hou, B.; Webster, R.; O’Dowd, G.; Christian, R.; Cherns, D.; et al. Electronic and Optical Properties of Single Crystal SnS2: An Earth-Abundant Disulfide Photocatalyst. J. Mater. Chem. A 2016, 4, 1312–1318. [Google Scholar] [CrossRef]
  22. Liu, G.; Li, Z.; Hasan, T.; Chen, X.; Zheng, W.; Feng, W.; Jia, D.; Zhou, Y.; Hu, P. Vertically Aligned Two-Dimensional SnS2 Nanosheets with a Strong Photon Capturing Capability for Efficient Photoelectrochemical Water Splitting. J. Mater. Chem. A 2017, 5, 1989–1995. [Google Scholar] [CrossRef]
  23. Liu, G.; Qiu, Y.; Wang, Z.; Zhang, J.; Chen, X.; Dai, M.; Jia, D.; Zhou, Y.; Li, Z.; Hu, P. Efficiently Synergistic Hydrogen Evolution Realized by Trace Amount of Pt-Decorated Defect-Rich SnS2 Nanosheets. ACS Appl. Mater. Interfaces 2017, 9, 37750–37759. [Google Scholar] [CrossRef]
  24. Ham, G.; Shin, S.; Park, J.; Choi, H.; Kim, J.; Lee, Y.-A.; Seo, H.; Jeon, H. Tuning the Electronic Structure of Tin Sulfides Grown by Atomic Layer Deposition. ACS Appl. Mater. Interfaces 2013, 5, 8889–8896. [Google Scholar] [CrossRef]
  25. Ham, G.; Shin, S.; Park, J.; Lee, J.; Choi, H.; Lee, S.; Jeon, H. Engineering the Crystallinity of Tin Disulfide Deposited at Low Temperatures. RSC Adv. 2016, 6, 54069–54075. [Google Scholar] [CrossRef]
  26. Johnson, R.W.; Hultqvist, A.; Bent, S.F. A Brief Review of Atomic Layer Deposition: From Fundamentals to Applications. Mater. Today 2014, 17, 236–246. [Google Scholar] [CrossRef]
  27. Zhuiykov, S. Development of Ultra-Thin 2D Semiconductors by Atomic Layer Deposition, 2nd ed.; Woodhead Publishing: Cambridge, UK, 2018; pp. 251–294. [Google Scholar]
  28. Buchholz, D.B.; Liu, J.; Marks, T.J.; Zhang, M.; Chang, R.P.H. Control and Characterization of the Structural, Electrical, and Optical Properties of Amorphous Zinc−Indium−Tin Oxide Thin Films. ACS Appl. Mater. Interfaces 2009, 1, 2147–2153. [Google Scholar] [CrossRef]
  29. Shang, M.; Qi, H.; Du, C.; Huang, H.; Wu, S.; Zhang, J.; Song, W. One-Step Electrodeposition of High-Quality Amorphous Molybdenum Sulfide/RGO Photoanode for Visible-Light Sensitive Photoelectrochemical Biosensing. Sens. Actuators B Chem. 2018, 266, 71–79. [Google Scholar] [CrossRef]
  30. Merki, D.; Fierro, S.; Vrubel, H.; Hu, X. Amorphous Molybdenum Sulfide Films as Catalysts for Electrochemical Hydrogen Production in Water. Chem. Sci. 2011, 2, 1262–1267. [Google Scholar] [CrossRef]
  31. Sinsermsuksakul, P.; Heo, J.; Noh, W.; Hock, A.S.; Gordon, R.G. Atomic Layer Deposition of Tin Monosulfide Thin Films (P1-31). Adv. Energy Mater. 2011, 1, 1116–1125. [Google Scholar] [CrossRef]
  32. Price, L.; Parkin, I.; Hardy, A.; Clark, R. Atmospheric Pressure Chemical Vapor Deposition of Tin Sulfides (SnS, Sn2S3, and SnS2) on Glass. Chem. Mater. 1999, 11, 1792–1799. [Google Scholar] [CrossRef]
  33. Ahn, J.H.; Lee, M.J.; Heo, H.; Sung, J.H.; Kim, K.; Hwang, H.; Jo, M.H. Deterministic Two-Dimensional Polymorphism Growth of Hexagonal n-Type SnS2 and Orthorhombic p-Type SnS Crystals. Nano Lett. 2015, 15, 3703–3708. [Google Scholar] [CrossRef]
  34. Ohring, M. Materials Science of Thin Films, 2nd ed.; Academic Press, A division of Harcourt, Inc.: London, UK, 2018; pp. 251–294. [Google Scholar]
  35. Majumder, S.; Mendhe, A.C.; Kim, D.; Sankapal, B.R. CdO Nanonecklace: Effect of Air Annealing on Performance of Photo Electrochemical Cell. J. Alloys Compd. 2019, 788, 75–82. [Google Scholar] [CrossRef]
  36. Devika, M.; Reddy, K.T.R.; Reddy, N.K.; Ramesh, K.; Ganesan, R.; Gopal, E.S.R.; Gunasekhar, K.R. Microstructure Dependent Physical Properties of Evaporated Tin Sulfide Films. J. Appl. Phys. 2006, 100, 023518. [Google Scholar] [CrossRef]
  37. Matmin, J.; Jalani, M.A.; Osman, H.; Omar, Q.; Ab’lah, N.; Elong, K.; Kasim, M.F. Photochemical Synthesis of Nanosheet Tin Di/Sulfide with Sunlight Response on Water Pollutant Degradation. Nanomaterials 2019, 9, 264. [Google Scholar] [CrossRef]
  38. Huang, P.-C.; Shen, Y.-M.; Brahma, S.; Shaikh, M.O.; Huang, J.-L.; Wang, S.-C. SnSx (x = 1, 2) Nanocrystals as Effective Catalysts for Photoelectrochemical Water Splitting. Catalysts 2017, 7, 252. [Google Scholar] [CrossRef]
  39. Deng, F.; Zhao, L.; Pei, X.; Luo, X.; Luo, S. Facile in Situ Hydrothermal Synthesis of G-C3N4/SnS2 Composites with Excellent Visible-Light Photocatalytic Activity. Mater. Chem. Phys. 2017, 189, 169–175. [Google Scholar] [CrossRef]
  40. Kment, S.; Cada, M.; Hubicka, Z.; Krysa, J.; Kmentova, H.; Olejnicek, J.; Cilova, Z.Z.; Zboril, R. Role of Ion Bombardment, Film Thickness and Temperature of Annealing on PEC Activity of Very-Thin Film Hematite Photoanodes Deposited by Advanced Magnetron Sputtering. Int. J. Hydrog. Energy 2016, 41, 11547–11557. [Google Scholar] [CrossRef]
  41. Saracco, G.; Barbero, G.; Hernández, S.; Alexe-Ionescu, A.L. Non-Monotonic Dependence of the Current Density on the Thickness of the Photoactive Layer. J. Electroanal. Chem. 2017, 788, 61–65. [Google Scholar] [CrossRef]
  42. Hernández, S.; Saracco, G.; Barbero, G.; Alexe-Ionescu, A.L. Role of the Electrode Morphology on the Optimal Thickness of BiVO4 Anodes for Photoelectrochemical Water Splitting Cells. J. Electroanal. Chem. 2017, 799, 481–486. [Google Scholar] [CrossRef]
  43. Hieu, H.N.; Dung, N.Q.; Kim, J.; Kim, D. Urchin-Like Nanowire Array: A Strategy for High-Performance ZnO-Based Electrode Utilized in Photoelectrochemistry. Nanoscale 2013, 5, 5530–5538. [Google Scholar] [CrossRef]
  44. Shi, J.; Hara, Y.; Sun, C.; Anderson, M.A.; Wang, X. Three-Dimensional High-Density Hierarchical Nanowire Architecture for High-Performance Photoelectrochemical Electrodes. Nano Lett. 2011, 11, 3413–3419. [Google Scholar] [CrossRef]
  45. He, S.; Meng, Y.; Cao, Y.; Huang, S.; Yang, J.; Tong, S.; Wu, M. Hierarchical Ta-Doped TiO2 Nanorod Arrays with Improved Charge Separation for Photoelectrochemical Water Oxidation under FTO Side Illumination. Nanomaterials 2018, 8, 983. [Google Scholar] [CrossRef]
  46. Parkinson, B. On the Efficiency and Stability of Photoelectrochemical Device. Acc. Chem. Res. 1984, 17, 431–437. [Google Scholar] [CrossRef]
  47. Sun, Y.; Cheng, H.; Gao, S.; Sun, Z.; Liu, Q.; Leu, Q.; Lei, F.; Yao, T.; He, J.; Wei, S.; et al. Freestanding Tin Disulfide Single-Layers Realizing Efficient Visible-Light Water Splitting. Angew. Chemie Int. Ed. 2012, 51, 8727–8731. [Google Scholar] [CrossRef]
  48. Jiang, C.; Moniz, S.J.A.; Wang, A.; Zhang, T.; Tang, J. Photoelectrochemical Devices for Solar Water Splitting —Materials and Challenges. Chem. Soc. Rev. 2017, 46, 4645–4660. [Google Scholar] [CrossRef]
Nanomaterials 09 01083 g001 550
Figure 1. Growth rates of the SnxSy films at deposition temperatures in the range of 60 to 180 °C. The thickness of the SnxSy film linearly increased with the number of growth cycles at 140 °C (inset).
Figure 1. Growth rates of the SnxSy films at deposition temperatures in the range of 60 to 180 °C. The thickness of the SnxSy film linearly increased with the number of growth cycles at 140 °C (inset).
Nanomaterials 09 01083 g001
Nanomaterials 09 01083 g002 550
Figure 2. SEM micrographs of the SnxSy films deposited at (a) 140 °C and (b) 180 °C on the Si wafer. The insets show the cross sections of the SnxSy films. (c) Atomic force microscopy (AFM) micrograph of the surface of the SnxSy film grown at 140 °C on the Si wafer. The root mean square roughness is 0.401 nm.
Figure 2. SEM micrographs of the SnxSy films deposited at (a) 140 °C and (b) 180 °C on the Si wafer. The insets show the cross sections of the SnxSy films. (c) Atomic force microscopy (AFM) micrograph of the surface of the SnxSy film grown at 140 °C on the Si wafer. The root mean square roughness is 0.401 nm.
Nanomaterials 09 01083 g002
Nanomaterials 09 01083 g003 550
Figure 3. (a) XRD patterns of the SnxSy films deposited at 60, 100, 140, and 180 °C on the glass substrate. The crystal structures of the SnxSy films below 140 °C were amorphous, while at 180 °C they transformed into orthorhombic SnS with the preferred crystal orientation along the (040) plane. (b) Raman spectra of the SnxSy films grown at 60, 100, 140, and 180 °C on the glass substrate. The SnxSy films consisted of SnS2 at 60, 100, and 140 °C, while at 180 °C they transformed into SnS. X-ray photoelectron spectroscopy (XPS) of (c) Sn 3d and (d) S 2p peaks of the SnS2 film grown at 140 °C on the silicon wafer.
Figure 3. (a) XRD patterns of the SnxSy films deposited at 60, 100, 140, and 180 °C on the glass substrate. The crystal structures of the SnxSy films below 140 °C were amorphous, while at 180 °C they transformed into orthorhombic SnS with the preferred crystal orientation along the (040) plane. (b) Raman spectra of the SnxSy films grown at 60, 100, 140, and 180 °C on the glass substrate. The SnxSy films consisted of SnS2 at 60, 100, and 140 °C, while at 180 °C they transformed into SnS. X-ray photoelectron spectroscopy (XPS) of (c) Sn 3d and (d) S 2p peaks of the SnS2 film grown at 140 °C on the silicon wafer.
Nanomaterials 09 01083 g003
Nanomaterials 09 01083 g004 550
Figure 4. HRTEM image (a) and TEM-EDX line scanning profile (b) of the SnxSy films deposited at 140 °C on the Si wafer.
Figure 4. HRTEM image (a) and TEM-EDX line scanning profile (b) of the SnxSy films deposited at 140 °C on the Si wafer.
Nanomaterials 09 01083 g004
Nanomaterials 09 01083 g005 550
Figure 5. Absorbances and optical band gaps (inset) of the amorphous SnS2 films fabricated at different temperatures. The absorbance increased with the growth temperature, and the optical band gaps of the amorphous SnS2 were 2.80, 2.68, and 2.52 eV at 60, 100, and 140 °C, respectively.
Figure 5. Absorbances and optical band gaps (inset) of the amorphous SnS2 films fabricated at different temperatures. The absorbance increased with the growth temperature, and the optical band gaps of the amorphous SnS2 were 2.80, 2.68, and 2.52 eV at 60, 100, and 140 °C, respectively.
Nanomaterials 09 01083 g005
Nanomaterials 09 01083 g006 550
Figure 6. (a) Linear sweep voltammetry plots of the 50-nm-thick amorphous SnS2 films deposited at 60, 100, and 140 °C. (b) Nyquist plots and equivalent circuit of the 50-nm-thick amorphous SnS2 films deposited at 60, 100, and 140 °C. (c) Photocurrent response stabilities of the 25-, 50-, 75-, and 100-nm-thick amorphous SnS2 films fabricated at 140 °C. The stabilities of the photocurrent light-on–off responses were evaluated at 0.8 V (vs. SCE) during 360 s.
Figure 6. (a) Linear sweep voltammetry plots of the 50-nm-thick amorphous SnS2 films deposited at 60, 100, and 140 °C. (b) Nyquist plots and equivalent circuit of the 50-nm-thick amorphous SnS2 films deposited at 60, 100, and 140 °C. (c) Photocurrent response stabilities of the 25-, 50-, 75-, and 100-nm-thick amorphous SnS2 films fabricated at 140 °C. The stabilities of the photocurrent light-on–off responses were evaluated at 0.8 V (vs. SCE) during 360 s.
Nanomaterials 09 01083 g006
Nanomaterials 09 01083 g007 550
Figure 7. (a–c) Schematics demonstrating the efficient photon capture and charge transport from SnS2 to the FTO electrode: (a) monocrystalline, (b) polycrystalline, and (c) amorphous SnS2. The gray spheres represent tin atoms, while the yellow spheres represent sulfur atoms. (d) Schematic of SnS2 used in PEC water splitting. The main processes include (I) light energy absorption, (II) photoelectron–hole pair separation and transport, and (III) surface redox reaction.
Figure 7. (a–c) Schematics demonstrating the efficient photon capture and charge transport from SnS2 to the FTO electrode: (a) monocrystalline, (b) polycrystalline, and (c) amorphous SnS2. The gray spheres represent tin atoms, while the yellow spheres represent sulfur atoms. (d) Schematic of SnS2 used in PEC water splitting. The main processes include (I) light energy absorption, (II) photoelectron–hole pair separation and transport, and (III) surface redox reaction.
Nanomaterials 09 01083 g007
Table
Table 1. The summaries of crystal structure and optical band gap for each deposition temperature.
Table 1. The summaries of crystal structure and optical band gap for each deposition temperature.
Deposition Temperature (°C)Crystal StructureOptical Band Gap (eV)
60SnS2 Amorphous2.80
100SnS2 Amorphous2.68
140SnS2 Amorphous2.52
180SnS orthorhombic1.78
Table
Table 2. Comparison of the SnS2 photoelectrochemical (PEC) performances with those in other studies.
Table 2. Comparison of the SnS2 photoelectrochemical (PEC) performances with those in other studies.
No.Working Electrode StructurePhotocurrent Density (µA/cm2)Reference Electrode (Applied Potential)SolutionIrradiationReference (Year)
1Glass/ITO/SnS2 (single-layer)2750Ag/AgCl (1.0 V)0.5 M Na2SO4300 W Xe lamp irradiation (λ > 420 nm)47 (2012)
2Glass/ITO/SnS2 (bulk)<5
3Glass/ITO/SnS2 NSs (with PVP)11.7SCE (0.8 V)0.5 M Na2SO4300 W Xe lamp illumination (λ > 420 nm)8 (2014)
4Glass/ITO/SnS2 NSs (without PVP)3.7
5Glass/ITO/SnS2 NSs (water and 0.5 g PVP)2.3
6Glass/FTO/Ni/SnS2/C (FNSC)38.6SCE (0 V)0.5 M Na2SO4Xenon lamp, 100 mW cm-2 (λ > 420 nm)9 (2016)
7Glass/FTO/Ni/SnS2 (FNS)19.8
8Glass/FTO/SnS2 (FS)16.6
9CC⊥SnS21920RHE (1.4 V)0.5 M Na2SO4AM 1.5 G 100 mW cm−2 solar light22 (2017)
10Glass/FTO⊥SnS21730
11Glass/FTO//SnS2910
12Glass/Cr/Au/SnS2−2Ag/AgCl (−0.4 V)0.25 M H2SO4Simulated AM 1.5 sunlight (100 mW cm−2)38 (2017)
13Glass/Cr/Au/SnS2195Ag/AgCl (0.8 V)
14g-C3N4/SnS2 nanoparticle13Ag/AgCl (1.0 V)0.5 M Na2S300 W xenon lamp (λ > 400 nm)12 (2018)
15g-C3N4/SnS2 NS10
16g-C3N4/3D flower-like SnS27.5
17Glass/FTO/SnS2 (amorphous)−35.1SCE (−0.6 V)0.25 M H2SO4Simulated AM 1.5 sunlight (100 mW cm−2)This study
18Glass/FTO/SnS2 (amorphous)51.5SCE (0.8 V)
ITO: indium tin oxide; PVP: polyvinylpyrrolidone; CC: carbon cloth; 3D: three-dimensional.

Share and Cite

MDPI and ACS Style

Hu, W.; Hien, T.T.; Kim, D.; Chang, H.S. Enhancement in Photoelectrochemical Performance of Optimized Amorphous SnS2 Thin Film Fabricated through Atomic Layer Deposition. Nanomaterials 2019, 9, 1083. https://doi.org/10.3390/nano9081083

AMA Style

Hu W, Hien TT, Kim D, Chang HS. Enhancement in Photoelectrochemical Performance of Optimized Amorphous SnS2 Thin Film Fabricated through Atomic Layer Deposition. Nanomaterials. 2019; 9(8):1083. https://doi.org/10.3390/nano9081083

Chicago/Turabian Style

Hu, Weiguang, Truong Thi Hien, Dojin Kim, and Hyo Sik Chang. 2019. "Enhancement in Photoelectrochemical Performance of Optimized Amorphous SnS2 Thin Film Fabricated through Atomic Layer Deposition" Nanomaterials 9, no. 8: 1083. https://doi.org/10.3390/nano9081083

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop