Exfoliated transition metal dichalcogenide nanosheets for supercapacitor and sodium ion battery applications.

Growing concerns regarding the safety, flammability and hazards posed by Li-ion systems have led to research on alternative rechargeable metal-ion electrochemical storage technologies. Among the most notable of these are Na-ion supercapacitors and batteries, motivated, in part, by the similar electrochemistry of Li and Na ions. However, sodium ion batteries (SIBs) come with their own set of issues, especially the large size of the Na+ ion, its relatively sluggish kinetics and low energy densities. This makes the development of novel materials and appropriate electrode architecture of absolute significance. Transition metal dichalcogenides (TMDs) have attracted a lot of attention in this regard due to their relative ease of exfoliation, diverse morphologies and architectures with superior electronic properties. Here, we study the electrochemical performance of Mo-based two-dimensional (2D) layered TMDs (e.g. MoS2, MoSe2 and MoTe2), exfoliated in a superacid, for battery and supercapacitor applications. The exfoliated TMD flakes were interfaced with reduced graphene oxide (rGO) to be used as composite electrodes. Electron microscopy, elemental mapping and Raman spectra were used to analyse the exfoliated material and confirm the formation of 2D TMD/rGO layer morphology. For supercapacitor applications in aqueous electrolyte, the sulfide-based TMD (MoS2) exhibited the best performance, providing an areal capacitance of 60.25 mF cm-2. For SIB applications, TMD electrodes exhibited significantly higher charge capacities than the neat rGO electrode. The initial desodiation capacities for the composite electrodes are 468.84 mAh g-1 (1687.82 C g-1), 399.10 mAh g-1 (1436.76 C g-1) and 387.36 mAh g-1 (1394.49 C g-1) for MoS2, MoSe2 and MoTe2, respectively. Also, the MoS2 and MoSe2 composite electrodes provided a coulombic efficiency of near 100 % after a few initial cycles.

Introduction

Batteries and supercapacitors are being considered for powering an increasingly diverse range of applications from stationary solar/wind energy farms, to electronic devices like wearable electronics and microchips [1]. To date, lithium-ion rechargeable systems have been at the forefront of devices for energy storage applications [2,3]. Advantages of Li-ion systems include the easy and reversible Li intercalation-deintercalation reaction due to lithium's small ionic size, portability and reasonably high volumetric energy densities [4,5]. However, Li-ion rechargeable systems also have their share of drawbacks, including the high cost of Li metal, flammability, undesirable side reactions and the formation of unwanted solid electrolyte interface (SEI) layers to name a few [6,7]. The high cost of Li especially hinders applications where large quantities are needed, i.e. in medium- and large-scale grid storage applications [8]. These drawbacks have encouraged an ongoing search for non-Li-ion-based rechargeable energy storage devices, among which Na, Mg, Al and K-ion systems are at the forefront [9-11]. Out of these, Na-ion rechargeable systems have received increasing attention because, as opposed to Li, Na resources are practically inexhaustible and evenly distributed around the world [8,12-14]. Also, since Na and Li are both alkali metals, it is likely that electrode materials for Li can be used for Na-ion systems [15]. A simple exchange, however, is not necessarily straightforward because Na and other metal-ions are much larger than Li-ions, and electrode designs must be altered to accommodate: (a) their slow diffusion kinetics in the bulk, and (b) structural changes in the host material associated with large volume changes upon bulky Na-ion insertion/extraction that causes capacity degradation [16,17].

As noted above, the application of Na-ions as charge carriers imposes unique limitations on the electrode material, and therefore the design and development of novel materials and their architectures are of absolute importance [18]. Transition metal dichalcogenides (TMDs) have drawn significant research attention lately because of their unique properties [19-21]. This class of materials can offer two-dimensional (2D) layered morphologies that exhibit large surface areas, and enhanced electrochemical kinetics coupled with low volume changes upon ionic intercalation. For example, Balasingam et al. studied few-layered MoSe2 nanosheets prepared by hydrothermal techniques for supercapacitor applications [20]. An optimum capacitance of 49.7 F g−1 was obtained with a 75% capacitance retention after 10 000 cycles of operation. WS2 ‘nanoribbons’ have been studied as a supercapacitor electrode in a potassium electrolyte, and results have indicated the 1 T atomic configuration to perform better than its 2H counterpart [22]. The 1 T nanoribbon produced an optimum areal capacitance of 2813 µF cm−2 which was about 12 times greater than the 2H type [22]. A recent report on MoS2 electrodes for Na-ion batteries showed double the capacity value of the Na/MoS2 theoretical capacity [23]. This observation is important because graphite, which can also exhibit 2D layered morphology, exhibits almost negligible capacity and cyclability towards Na [24]. It was speculated that a conversion-type reaction could be responsible for high capacity. MoSe2 nanoplates have been studied as anodes in sodium ion batteries (SIBs). The nanoplates were fabricated by pyrolysis and initial charge and discharge capacities of 1400 C g−1 and 1846.8 C g−1 were obtained at a rate of 0.1 C. However, the capacity decayed to about 1400 C g−1 after 50 cycles of operation. The reduction was attributed to change in the lattice structure of MoSe2 from octahedron to a tetrahedral due to Na ion intercalation [25]. David et al. have studied MoS2/graphene composite free-standing anodes in SIB systems [23]. Their composite anode demonstrated a stable charge capacity of 828 C g−1 with a 99% coulombic efficiency.

A detailed comparative study of the family of TMDs, especially as electrodes in sodium ion supercapacitor systems, is lacking in the literature. In this manuscript, a novel superacid-assisted exfoliation technique is used to study the electrochemical behaviour of TMDs as potential electrode materials for sodium ion supercapacitors and batteries. This manuscript, therefore, aims to study the effect of exfoliating these materials in a novel way, as well as to study their viability as energy storage materials and to probe into their electrochemical phenomena under both aqueous and organic electrolyte environments.

Experimental

Synthesis of exfoliated or acid-treated TMD nanosheets

TMD powders (99%, Sigma Aldrich)[1] were sonicated for 30 min in concentrated superacid (pH < −1 and density 1.75 g ml−1, Sigma™) to form a solution (concentration of solution ≈ 2 mg ml−1) for exfoliating TMD flakes. Two types of superacids were used: chlorosulfonic acid (superacid, 99%, Sigma Aldrich) and methanesulfonic acid. Note that the superacid was added very slowly (so as to prevent an exothermic reaction) to the TMD powder in an argon-filled glovebox (dew point −50°C, the low dew point being necessary so that the moisture content is minimal as superacid is to be used). The solution was then carefully quenched in 1.0 l of distilled water (performed with extreme caution in a glovebox). Additional dilution with DI water was done to reduce the solution acidity. The supernatant containing the (lighter) exfoliated flakes was pipetted from the top portion of the solution and dried in a conventional oven to obtain dry superacid treated TMD nanosheets. This process is based on the rationale that the protonation of the TMDs in solution (by the dissociation of the chlorosulfonic acid), coupled with the sonication, provides the energy necessary to overcome the weak van der Waals forces of attraction between the bulk TMD sheets.

Synthesis of graphene oxide

Sodium nitrate, potassium permanganate, sulfuric acid, hydrogen peroxide (31.3% solution in water), hydrochloric acid (30% solution in water), and methanol (99.9%) were purchased from Fisher Scientific. All materials were used as received without further purification. Hummer's method was used to make graphene oxide [26].

Synthesis of rGO/TMD composite paper

A total of 15 mg of GO and 22.5 mg of acid-treated TMD nanosheets were added to a 1 : 1 volume fraction solution of water and isopropanol. The mixture was sonicated for 60 min (Branson Sonifier) to disperse the nanosheets in the solution. The composite suspension was then vacuum-filtered using a 47 mm diameter, 10 µm pore size, filter membrane (HPLC grade, Millipore). TMD/GO composite paper thus obtained was dried in an oven at 70°C overnight and subsequently reduced at 500°C for 2 h, and again at 900°C for 5 min in argon. The samples are denoted hereafter as rGO for neat rGO, and MoS2, MoSe2, and MoTe2 for the respective TMDs, each of which comprises approximately 20% by mass rGO as the conducting agent.

Instrumentation for structural characterization

Transmission electron microscope (TEM) images were digitally acquired by the use of a Phillips CM100 operated at 100 kV. Raman spectroscopy was performed by a Horiba Jobin Yvon LabRam ARAMIS confocal Raman microscope using a He-Ne laser (approx. 632.8 nm). Energy dispersive spectra (EDS) were collected using a Zeiss Gemini scanning electron microscope (SEM) at 10–30 keV. To observe the layered electrode morphology cross-section, a focused Ga+ ion beam (Zeiss Auriga FIB-SEM) was used to cut notches at the edges of the exfoliated TMD composite structures.

Fabrication of electrodes, cell assembly and electrochemical testing

For use in supercapacitors in aqueous electrolyte, 20–30 mg of active material (TMD powder) was thoroughly ground with 5% by mass PVDF (binder) and C black (for improving electronic conductivity) each. The grinding was done in a mortar-pestle with the dropwise addition of N-methyl pyrrolidone (NMP) solvent such that a viscous slurry was obtained with a ‘honey-like’ consistency. The slurry was then pasted on stainless steel substrates and dried overnight in a box-furnace at 55°C. For electrochemical testing as supercapacitors, a 3-electrode set-up was used with a Pt wire counter-electrode, and an Ag/AgCl reference electrode in a 1 M aqueous Na2SO4 electrolyte. Cyclic voltammetry (CV) was performed within a range of 0.0–0.8 V at scan rates of 5, 50, 100, 200 and 500 mV s−1, using a CHI™ 660 E electrochemical workstation. This same workstation was used for performing electrochemical impedance spectroscopy (EIS) in 1 M aqueous Na2SO4 solution. Galvanostatic charge-discharge (GCD) was performed at current densities of 0.5, 1.0, 1.5 and 2.0 mA cm−2 using the same workstation. The set-up of the 3-electrode system is such that the electrode needs to be supported by a clip and a free-standing electrode's structural integrity was compromised under the tensile stress from the clip. Hence, a stainless steel current collector was used during this testing.

For applications in batteries in organic electrolyte, the free-standing rGO/TMD composite papers were used directly as the working electrodes. 14.3 mm diameter electrodes were punched out of the composite paper. Electrochemical analysis was performed using coin cells (CR 2032) and a two-electrode set-up was employed. 1 M NaClO4 (Alfa Aesar) in (1 : 1 volume fraction) dimethyl carbonate : ethylene carbonate (DMC:EC) served as the electrolyte. A 25 µm thick glass separator soaked in electrolyte was placed between the working electrode and pure Na metal (14.3 mm diameter, 75 µm thick) to be used as the counter-electrode. GCD analysis was performed between 2.25 V and 10 mV versus Na/Na+ using a multichannel BT2000 Arbin test unit.

Results and discussion

Structural and phase characterization

TEM imaging and EDS

TEM imaging is necessary not only to understand the structure and morphology of the exfoliated sheets, but also to observe whether the acid-based exfoliation process has been successful in providing the sheet-like microstructure that is desired. The TEM images of the exfoliated TMD samples in figure 1a–c demonstrate the formation of triangular or rhomboidal sheets. The images indicate the formation of a stacked, few-layered morphology and the absence of single-layered flakes can be attributed to the volume/morphology of the bulk TMD precursor, the type and strength of acid used, and the power used during the sonication process [27]. Optimization of the sonication process should be able to provide a direct correlation with number of layers and the type of morphology obtained. Also, the observation that the flakes range in linear dimensions between 50 and 100 nm is consistent with earlier work by the same group [23]. The exfoliated TMD sample images demonstrate a homogeneous and defect-free morphology, especially at the sheet edges. It can be inferred from these observations that the homogeneous nature of the flaky and rigid nanosheets will tend to prevent their restacking and maintain their 2D morphology throughout the cell cycling. It is also pertinent to note that in figure 1c, some dots are observed at the edge of the MoTe2 sample. These dots seen at the edge of the MoTe2 can have two probabilities. Firstly, it can be hypothesized that very small amounts of the exfoliated MoTe2 may have restacked together. This is a feature of exfoliated TMDs and a similar appearance has also been reported in the literature [28,29]. Secondly, it is also possible that all of the bulk MoTe2 obtained commercially may not have been in layered form and there may have been a very small fraction in a non-layered form. Consequently, on exfoliation, these non-layered parts did not exfoliate out and are observed as particulate ‘dots’ in the TEM. Of course, they are a very small fraction of the entire sample and the TEM image proves that.

Figure 1.

TEM micrographs and EDS of the exfoliated TMD samples. Panels (a–c) are TEM images of the exfoliated TMD samples exhibiting a homogeneous multi-layered nanosheet morphology. Scale bars = 100 nm, (d) EDS of the MoS2 sample demonstrating the characteristic Mo and S peaks, along with a Cu peak from the substrate (e) EDS of the MoSe2 sample demonstrating the characteristic Mo and Se peaks, (f) EDS of the MoTe2 sample indicating characteristic Mo and Te peaks.

Figure 1d shows an EDS of the exfoliated MoS2 sample where characteristic Mo and S peaks (Lα and Kα) can be observed. Figure 1e,f similarly show EDS survey spectra of the exfoliated MoSe2 and the exfoliated MoTe2 samples. The characteristic Mo (Kα and Lα) and Se (Kα, Kβ and Lβ) and Te (Lα and Lβ) spectral lines can be observed. Another important observation is the absence of any impurity peaks, especially Cl− peaks from residual chlorosulfonic acid. This indicates the phase purity of the exfoliated samples, thereby further confirming the results seen in the Raman spectra for these samples. However, it is understood that there may be some trace amounts of Cl− which is beyond the resolution limit of the EDX instrument.

Raman spectra

Figure 2a–c shows Raman spectra of the exfoliated MoS2, MoSe2 and MoTe2, respectively. Characteristic E2 g and A1 g peaks can be observed for all the samples. The A1 g mode indicates the out-of-plane vibration of the chalcogen species, whereas the E2 g mode is an indicator of in-plane vibrations of the Mo species [30]. It is to be noted that the observed sharp peaks of the A1 g modes are mainly due to the interaction of the incident laser beam with the direct band gap, resulting in resonance [31,32]. The peak positions also indicate the formation of few-layered samples. For a monolayer, there is only one active vibrational mode that can be usually observed. However, for the MoSe2 sample, the A1 g mode at 240 cm−1 is visible as a sharp peak in figure 2b. Also, the E12 g and the A1 g modes are observed in all the cases, indicating the existence of several layers. This is especially true for the MoTe2 sample, which shows several auxiliary peaks indicating the formation of multiple layers [33].

Figure 2.

Raman spectra of the exfoliated TMD samples. Panels (a–c) are the Raman spectra of the exfoliated MoS2, MoSe2 and MoTe2 samples. The characteristic vibration modes of the sample (A1g and E2g) corresponding to their out-of-plane and in-plane vibrations, seen as peaks in the spectra have been labelled for the respective TMDs.

The absence of impurity peaks demonstrates that the superacid-based exfoliation process has not resulted in the dissolution of sulfur or formation of impurity phases. EDS results in the next section support this conclusion.

Cross-sectional imaging and elemental mapping of the exfoliated layers

Figure 3 shows the 2D exfoliated TMD sample structures in greater detail. The MoS2, MoSe2 and MoTe2 samples are shown in figure 3a–c, respectively. Images on the left are low-magnification secondary electron images, in which each sample exhibits a uniform appearance over a large area. The white arrows point to 100 µm wide notches FIB-milled into small pieces of each of the three exfoliated TMD samples. Images in the middle show the notch cross-section where the layered morphology and individual flakes of the TMD material can be observed. Images on the right show X-ray maps superimposed on the secondary electron images. The X-ray maps and the cross-sectional images suggest that the exfoliated MoS2 sample exhibits a distinct layered morphology compared to the MoSe2 and MoTe2 samples, with several TMD flakes sandwiched between rGO layers. It is important to note that the X-ray maps suggest the composition is relatively uniform. If individual ‘islands’ had been observed throughout the flake, this could have contributed to inhomogeneities that would be detrimental towards electrochemical performance.

Figure 3.

Images and elemental maps of the exfoliated, layered structures: (a) MoS2, (b) MoSe2 and (c) MoTe2. Each set of three images shows a low magnification survey image (left, with arrows indicating the 100 nm wide FIB-milled notch), a cross-section view of the structure (middle), and an X-ray map (right) with inset element colour key. Scale bars are 10 µm.

Electrochemical performance analysis

Supercapacitor performance

Electrochemical performance of the exfoliated TMD powders as supercapacitors is shown in figure 4a–d.

Figure 4.

Electrochemical performance of exfoliated TMD electrodes in aqueous media as supercapacitor electrodes. (a) CV of the exfoliated TMD electrodes in 1 M aq. Na2SO4 performed at a scan rate of 200 mV s−1, showing characteristic double layer capacitance behaviour, (b) corresponding specific capacitances of the TMD electrodes at 5, 50, 100, 200 and 500 mV s−1 with the MoS2 electrode providing the best performance, (c) first cycle GCD curves of the exfoliated TMD electrodes obtained at a current density of 1 mA cm−2, (d) corresponding specific capacitances for the various TMD electrodes at current densities of 0.5, 1.0, 1.5 and 2.0 mA cm−2, with MoS2 demonstrating superior performance.

Figure 4a shows the CV results from exfoliated TMD electrodes collected at a 200 mV s−1 scan rate. All samples exhibit a rectangular CV curve, indicating double layer capacitive behaviour and suggesting that charge is stored along the electrode surface. It is observed that greater electrochemical surface areas are obtained as a consequence of the layered morphology, which enhances the ability to store charge at the interface. Increasing scan rates produced larger areas enclosed by the CV curve along with higher peak currents; however, no distinct redox peaks were observed. Figure 4b shows the capacitances obtained for the same samples at CV scan rates from 5 to 500 mV s−1. Results demonstrate that MoS2 performs the best, providing a maximum areal capacitance of 60.25 mF cm−2.

Figure 4c shows the first cycle GCD curves of the exfoliated TMD electrodes. The symmetric GCD curves correspond to a reversible electrochemical process with reduced hysteresis losses [34]. Here too, the MoS2 sample performs better than the others, with a maximum areal capacitance of 22.5 mF cm−2 at a current density of 0.5 mA cm−2. This can be attributed to the quality of exfoliation leading to better electrochemical properties of MoS2, which fits well with the cross-sectional images seen in figure 3. Figure 4d shows that the areal capacitances converge to similar values for all the samples at high current rates (approx. 2 mA cm−2). This can be attributed to the significantly reduced ionic diffusion at such high current rates. These results corroborate ab initio studies of MoSe2 electrodes as supercapacitors for Na-ion systems [35].

The capacitance values obtained in this manuscript represent the lower limit for the exfoliated TMD samples. This is because the samples were directly used after the exfoliation process without optimizing for the quality of output, i.e. quality and number of layers formed. Also, though characterization techniques demonstrate no impurity phases present, there may be electrochemically competing phases present which may not have been detected. A post-exfoliation ‘cleansing’ of the TMD samples may also improve the capacitance.

Electrochemical impedance spectroscopy

EIS was performed for further understanding the electrochemical behaviour of the materials synthesized. From figure 5, the Nyquist plot shows that for the three TMD/rGO materials studied, the semicircle, at the high-frequency region, is attributed to pseudocapacitive and double-layer (EDL) processes. Importantly, one thing that may contribute toward the fast-charge faradaic processes for TMDs is the fact that such species possess different oxidation states [36]. Thus, the capacitance may be a combination of EDL and faradaic charge storage processes [37].

Figure 5.

Electrochemical impedance spectra of the exfoliated TMD/rGO composite anodes. Panels (a–c) represent the EIS of the MoS2/rGO, MoSe2/rGO and MoTe2/rGO samples, respectively, performed in aqueous 1 M Na2SO4 solution. All samples exhibit the characteristic inverted semicircle in the high-frequency regime and a linear trajectory in the low-frequency regime.

The canonical circuit, proposed by Tilak et al., was employed to simulate the results [38]. This circuit, as shown in scheme 1, is composed of the following elements: bulk equivalent series resistance of the solution (Resr), charge transfer resistance (Rct), capacitance of the electric double layer (CPE EDL), and the capacitance related to the pseudocapacitive reactions (CPE) [39]. It is worth mentioning that the capacitors in parallel (CPE EDL and CPE) are equivalent to ZCPE = 1/Y0(jω), a variable which accounts for the dispersion phenomena inherent from electrodes surface, which are non-homogeneous; and for the adsorption of ions from the electrolyte. Thus, these processes are simulated and quantified within the range 0 ≤ n ≤ 1.

Scheme 1.

Equivalent circuit corresponding to the EIS analysis, consisting of the individual resistive and capacitive components.

From the circuit above, it is possible to obtain the contributions by each parameter i.e. bulk equivalent series resistance of the solution (Resr), charge transfer resistance (Rct), capacitance of the electric double layer (CPE EDL) and the capacitance related to the pseudocapacitive reactions (CPE); these values are provided in table 1.

Table 1.

Listing of values of the individual resistive and capacitive components for each exfoliated TMD/rGO composite.

impedance element	MoS2	MoSe2	MoTe2
Resr (Ω)	0.905	1.20	0.684
Rct (Ω)	4.15	3.86	5.32
CPE EDL – YEDL (μΩ−1 * sn)	32.9 (n = 0.702)	14.3 (n = 0.891)	31.1 (n = 0.67)
CPE θ – Yθ (μΩ−1 * sn)	387 (n = 0.763)	22.2 (n = 0.819)	61.5 (n = 0.80)

Battery performance

The performance of the TMD composite papers as anodes in Na/Na+ half cells is provided in figure 6a–g.

Figure 6.

Electrochemical performance of TMD composite electrodes in Na/Na+ half-cell. (a,c,e,g) are the GCD curves of the first and second cycles for the MoS2, MoSe2, MoTe2 and rGO electrodes demonstrating their characteristic behaviour towards Na+ ion interaction, (b,d,f,h) are the corresponding dQ/dV plots of the composite TMD electrodes exhibiting the characteristic sodiation and desodiation peaks. (1 mAh g−1 = 3.6 C g−1). Permission for reuse of data for figures (b,g,h) obtained from ACS publications [23].

Figure 6a,c,e,g are the first and second cycle GCD curves for the exfoliated TMD electrodes (MoS2, MoSe2 and MoTe2) and the rGO electrodes, respectively. The exfoliated MoS2, MoSe2 and the MoTe2 composite paper samples demonstrate the first cycle sodiation (discharge) capacities of 468.84 mAh g−1 (1687.82 C g−1), 399.1 mAh g−1 (1436.76 C g−1) and 387.36 mAh g−1 (1394.49 C g−1), whereas their charge (desodiation) capacities are 512.25 mAh g−1 (1844.1 C g−1), 251.86 mAh g−1 (906.73 C g−1) and 214.62 mAh g−1 (772.66 C g−1). These charge capacities are approximately 2.5–3 times greater than that of the rGO electrode, which delivers a first cycle charge capacity of 81.5 mAh g−1 (293.4 C g−1) as observed in figure 6h. The authors would like to point out that these capacities are for free-standing TMD composite paper electrodes without any additive binder contributions. Also, the capacities obtained in the present manuscript are comparatively higher than some of the values that have been reported in the literature [40,41].

However, the rGO paper showed significantly higher charge capacity than commercial graphite (293.4 C g−1 versus approx. 126 C g−1) for the Na/Na+ half-cell [42]. The voltage profile curves showed that the oxidation/reduction mechanism of TMD composite electrodes with respect to sodium exhibited two distinct plateaus and were very different when compared to the sloped rGO discharge curve. Differential capacity (dQ/dV) curves were plotted (figure 6b,d,f,h) to study the Na+ ion interaction with the TMD and the rGO electrodes in greater detail. Since each peak corresponds to a specific reaction and certain peaks disappeared after the first cycle, those peaks (e.g. 0.5 V and 0.6 V for MoSe2, 0.69 V for MoTe2) can be ascribed to the formation of an SEI layer15. In the second cycle, all TMD electrodes showed two insertion peaks (approx. 0.15 V and approx. 1.34 V to 1.46 V) and two extraction peaks (approx. 0.5 and approx. 1.5 V to 1.7 V), which indicates distinct sodiation and desodiation in the TMD composite electrodes.

From figure 6a MoS2 demonstrates a two-step interaction with Na ions at approximately 0.9 V and approximately 0.75 V. In this interaction, cations are intercalated into the ordered MoS2 structure, leading to a conversion reaction in which the material degrades into Mo and Na2S, as previously reported [23].

For MoSe2, ionic interaction with the structure results in its transformation from a semiconductor to a metal. Wang et al. have demonstrated that when Na+ ions intercalate into MoSe2, equal amounts of electrons also enter to maintain overall electrical neutrality and these electrons insert themselves into the t2g orbitals of Mo [25]. It is this that results in the transition to a metallic stage. Also, it has been shown that Na+ ion intercalation can occur at two different sites in the MoSe2 lattice: at a tetrahedral or an octahedral location. For MoSe2, the plateau at approximately 0.65 V corresponds to the formation of NaxMoSe2, whereas the other plateau at around 0.4 V corresponds to reduction of Mo4+ to Mo and the formation of Na2Se [25].

The reaction mechanism is similar for MoTe2, which has a plateau corresponding to the formation of metallic Mo and Na2Te [43]. The conversion reaction in this case is as follows:

It is noted that all the TMD samples undergo a large first cycle capacity loss (especially MoS2), which is attributed to the SEI layer formation which impedes the charge transfer process initially. Also, structural changes occur during the initial cycles as a result of the transformation process and side reactions with the electrolyte also contribute to the first cycle loss. It is to be also noted that the difference in the cathodic and anodic peak locations for the TMDs with different chalcogen atoms are due to interfacial Na+ ion storage, interaction/storage of Na+ ions in different defective sites of each crystal and its constituent layers [44]. It is understood that the presence of rGO enhances the performance of these exfoliated TMDs. rGO not only increases electronic conductivity, but also helps prevent the restacking of the exfoliated TMD layers by acting as support and relieving the stress produced to the cell cycling [23,45].

The neat rGO electrode only showed a broad plateau during the extraction half, indicating insufficient intercalation.

Capacity retention data for various electrodes up to 20 cycles are presented in figure 7a. After the completion of 20 cycles, MoS2 demonstrated a capacity retention of approximately 83% (leaving aside the first cycle loss) followed by MoSe2 (63.44%) and MoTe2 (53.98%). Furthermore, the TMD electrodes reached near 100% cycling efficiency after the second discharge and remained constant up to the 20th cycle. Therefore, an analysis of the GCD and preliminary cell cycling results demonstrates the promise of our novel exfoliated free-standing TMD materials as negative electrodes for SIB applications. Additionally, as seen in figure 7b, all TMD electrodes showed first cycle efficiency in excess of approximately 50% compared to rGO, which demonstrated only 10.16%.

Figure 7.

Capacity retention and coulombic efficiency curves. (a) Capacity retention trend and (b) coulombic efficiency trends showing the superior performance of TMD composite electrodes over standalone rGO electrode.

Conclusion

A superacid-based technique was used to successfully exfoliate Mo-based layered TMDs. Detailed structural and elemental characterization indicates the formation of phase pure few-layered TMD nanosheets, thereby demonstrating the efficacy of the process. The characterization process has also shown that sheets are usually homogeneous and the acid-based process has not resulted in any dissolution of the material. The exfoliated sheets were then combined with rGO to form composite paper electrodes for electrochemical energy storage applications.

For battery configuration, all the TMD composite electrodes perform better than rGO, providing an initial charge capacity of 468.84 mAh g−1, 399.10 mAh g−1 and 387.36 mAh g−1 for MoS2, MoSe2 and MoTe2, respectively. TMD electrodes also provide steady coulombic efficiencies (close to 100% after a few cycles) and capacity values at least approximately 2.5 to 3 times those of neat rGO electrode. The electrochemical analyses, especially the incremental capacity curves, illustrate the Na+ ion interaction mechanisms in the TMDs, with the transformation reaction regimes clearly distinguished for each electrode. The results offer promise for the use of TMD-based electrodes in electrochemical energy storage systems.