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  • Nano Express
  • Open Access

High-Yield Preparation and Electrochemical Properties of Few-Layer MoS2 Nanosheets by Exfoliating Natural Molybdenite Powders Directly via a Coupled Ultrasonication-Milling Process

Nanoscale Research Letters201611:409

  • Received: 28 June 2016
  • Accepted: 7 September 2016
  • Published:


Cost-effective and scalable preparation of two-dimensional (2D) molybdenum disulfide (MoS2) has been the bottleneck that limits their applications. This paper reports a novel coupled ultrasonication-milling (CUM) process to exfoliate natural molybdenite powders to achieve few-layer MoS2 (FL-MoS2) nanosheets in the solvent of N-methyl-2-pyrrolidone (NMP) with polyvinylpyrrolidone (PVP) molecules. The synergistic effect of ultrasonication and sand milling highly enhanced the exfoliation efficiency, and the precursor of natural molybdenite powders minimizes the synthetic cost of FL-MoS2 nanosheets. The exfoliation of natural molybdenite powders was conducted in a home-made CUM system, mainly consisting of an ultrasonic cell disruptor and a ceramic sand mill. The samples were characterized by X-ray diffraction, UV-vis spectra, Raman spectra, FT-IR, SEM, TEM, AFM, and N2 adsorption-desorption. The factors that influence the exfoliation in the CUM process, including the initial concentration of natural molybdenite powders (C in, 15–55 g L−1), ultrasonic power (P u, 200–350 W), rotation speed of sand mill (ω s, 1500–2250 r.p.m), exfoliation time (t ex, 0.5–6 h), and the molar ratio of PVP unit to MoS2 (R pm, 0–1), were systematically investigated. Under the optimal CUM conditions (i.e., C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m and R pm = 0.5), the yield at t ex = 6 h reaches 21.6 %, and the corresponding exfoliation rate is as high as 1.42 g L−1 h−1. The exfoliation efficiency of the CUM mode is much higher than that of either the ultrasonication (U) mode or the milling (M) mode. The synergistic mechanism and influencing rules of the CUM process in exfoliating natural molybdenite powders were elaborated. The as-obtained FL-MoS2 nanosheets have a high specific surface area of 924 m2 g−1 and show highly enhanced electrocatalytic performance in hydrogen evolution reaction and good electrochemical sensing property in detecting ascorbic acid. The CUM process developed has paved a low-cost, green, and highly efficient way towards FL-MoS2 nanosheets from natural molybdenite powders.


  • Coupled ultrasonication-milling process
  • Multi-forces synergistic exfoliation
  • Natural molybdenite powders
  • Few-layer MoS2 nanosheets
  • Liquid-phase exfoliation
  • Electrochemical performance
  • Layered materials


Since the discovery of graphene, two-dimensional (2D) nanomaterials have attracted highly increasing attention owing to their unique few-layer microstructures and resulting unprecedented functional properties [14]. Among them, the most typical 2D sample should be transition-metal dichalcogenides (TMDs), composed of covalently bonded transition-metal atoms (M) and chalcogen atoms (X = S, Se, Te) in a possible stoichiometric form of MX2 [5], such as MoS2 and WS2, of which each single-layer consists of two S atom layers and a layer of metal atoms sandwiched between the two S layers [6]. Owing to the suitable intrinsic indirect band gap (1.3 eV), MoS2 has attracted great attention and been thought as alternative promising next-generation 2D materials. When the layered MoS2 bulks are exfoliated into single-layered 2D nanosheets, their band gap increases from 1.3 to 1.9 eV [7, 8]. The interesting nanostructures and band gaps make MoS2 a useful active material in various fields, including energy storage and solar cells [914], catalysis [1519], sensing [1921], and electronic devices [2224]. As a major member of the TMD family, MoS2 has been known as a highly efficient catalyst for the hydro-desulfurization, reduction reaction of methyl orange by MoS2/montmorillonite [25] and hydrogen evolution reactions (HER) [2628]. Experimental and theoretical studies have verified that the catalytic activity of MoS2 is associated with metallic edges, whereas its semiconducting basal plane is catalytically inert [29]. Few-layer MoS2 (FL-MoS2) nanosheets can maximize the fraction of exposed edge sites and thus show highly enhanced catalytic performance [30]. FL-MoS2 nanosheets can also be used as electrochemical biosensors for the detection of glucose [31], acetaminophen (AC) [32], double-stranded DNA [33], ascorbic acid [34], and H2O2 [35] which show a high response due to the advantage of abundant exposed edges.

Scalable and cost-effective synthesis of high-quality FL-MoS2 nanosheets is one of the preconditions for their commercial applications. Up to now, the available methods for the preparation of monolayer or FL-MoS2 nanosheets can be categorized into two types: “bottom-up” growth and “top-down” exfoliation. For the “bottom-up” growth, solvothermal methods [3638], chemical vapor deposition [39, 40], and thermal decomposition [41, 42] have been developed to synthesize MoS2 nanocrystals with various shapes and sizes using molybdenum-containing chemicals as the Mo source. Unfortunately, the molybdenum-containing chemicals are expensive, and the morphology and size of MoS2 nanocrystals in the “bottom-up” growth are not easy to control. The “top-down” exfoliation, starting from three-dimensional (3D) layered bulks, is commonly used to prepare 2D nanomaterials. FL-MoS2 nanosheets have been synthesized by the “top-down” exfoliation, including micromechanical exfoliation [43, 44], chemical exfoliation through intercalation [4548], electrochemical exfoliation [49, 50], liquid-phase exfoliation (LPE) [5158], grinding-assisted liquid exfoliation [5961], and supercritical fluid exfoliation [62].

Micromechanical exfoliation, firstly developed to prepare graphene by exfoliating HOPG [63], can achieve isolated individual crystal planes (monolayers) with high crystal quality and macroscopic continuity, but its yield is too low to be of any practical applications. Chemical exfoliation usually necessitates intercalating various small species (i.e., organic molecules, alkali metals and transition-metal halides) into the interlayer spaces to achieve the exfoliation. In most cases, chemical exfoliation is time-consuming, sensitive to environmental conditions, and difficult to control the intercalated degree [49]. Electrochemical exfoliation, through a controllable lithiation process, has been developed to exfoliate the layered solids (i.e., MoS2, WS2, TiS2, TaS2, ZrS2, and graphite) as the cathode in an electrochemical setup, and the lithium-intercalation in the layered materials can be monitored and finely controlled during the discharge process [49], but high-cost and low yield limit its wide applications. Liquid-phase exfoliation (LPE) is one of the most common methods used in the exfoliation of layered solids recently [51]. The LPE process involves the following steps: (1) immersion of layered materials in a suitable solvent (i.e., NMP, DMF, THF, NVP, CAN, and DMSO), (2) exfoliation of layered materials, and (3) stabilization of exfoliated 2D materials [51]. Sufficient liquid immersion is one of the most effective and straightforward means to reduce the strength of the van der Waals attractions, where the potential energy between adjacent layers is mainly contributed by the dispersive London interactions. Although LPE can be scaled up, the solvents used are usual toxic and not environmentally friendly. Supercritical fluid exfoliation is the newly developed method to prepare few-layer nanosheets via the shearing force generated by the gas molecules in the supercritical condition [64]. To further improve the exfoliated efficiency, scientists have coupled various methods, i.e., the two-solvent grinding-assisted LPE process [65] and ionic liquid assisted grinding [35, 66], to exfoliate layered solids to make few-layer nanosheets. However, scalable, efficient, cost-effective, and high-yield synthesis of FL-MoS2 nanosheets is still challengeable.

Here, we develop a novel coupled ultrasonication-milling (CUM) process, as shown in Fig. 1, to exfoliate natural molybdenite powders to prepare FL-MoS2 nanosheets in a high-efficient manner via the synergistic effect of ultrasonication and sand milling. The precursor of natural molybdenite powders is directly from the molybdenite ore after a purification and superfine treatment. Molybdenite ore is abundant in China, and using natural molybdenite as the starting material can achieve a low-cost and low-carbon approach to make FL-MoS2 nanosheets. For the ultrasonic (U) exfoliation, the key point is the choice of suitable exfoliation solvent, and it is favorable to exfoliation when the surface tension of the solvent matches well with the surface energy of the layered bulk materials. The surface energy of MoS2 reported is ~75 mJ m−2, and the N-methyl-2-pyrrolidone (NMP) with a surface tension of 41 mN m−1 is found to be a good solvent for the exfoliation and dispersion of MoS2 nanomaterials [67]. NMP is therefore chosen as the exfoliation solvent in the exfoliation of natural molybdenite powders via the present CUM process. Because of the steric effect of polyvinylpyrrolidone (PVP) molecules, the exfoliating yield of FL-MoS2 via the CUM process with the aid of PVP under the optimal conditions reaches 21.6 %, much higher than those of the reported methods. The as-obtained FL-MoS2 nanosheets by the CUM process from natural molybdenite powders show highly electrochemical performance for hydrogen evolution reaction and sensing applications. The newly developed CUM process combines the advantage of both liquid-phase exfoliation (LPE) and mechanical exfoliation. The synergistic effect of the shear force generated by the high-speed sand mill and the cavitation by the liquid-phase ultrasonic process can highly accelerate the exfoliation of molybdenite powders. The key points of this work are to explore the influencing factors and possible synergistic effect during the CUM process.
Fig. 1
Fig. 1

Schematic diagram of the coupled ultrasonication-milling (CUM) strategy for exfoliating natural molybdenite powders to make few-layer MoS2 (FL–MoS2) nanosheets: a Components of the CUM system, b basic operational principle of the CUM system, and c exfoliation of natural molybdenite towards FL-MoS2 nanosheets by the CUM route


Materials and Setup

Natural molybdenite powders (particle size 3–5 μm; MoS2 content ≥99 %; Luoyang Exploiter Molybdenum Co. LTD, China), N-methyl-2-pyrrolidone (NMP, ≥ 99 %; DAMAO Tianjin), and polyvinyl pyrrolidone (PVP, Molecular weight 1000–1,300,000, AR, Kermel) were used as received. The CUM system was home-made, mainly consists of an ultrasonic processor (Nanjing Atpio Instruments Manufacturer, China) and a sand mill (NT-0.3 L, Longly, China), schematically shown in Fig. 1.

Exfoliation of Natural Molybdenite Powders by CUM Process

The exfoliation of natural molybdenite powders towards FL-MoS2 nanosheets was conducted in the home-made CUM system (Fig. 1) using NMP as the solvent containing PVP as the exfoliation agent at ~25 °C. The exfoliation of natural molybdenite powders by the CUM process was conducted under the similar conditions. Typically, natural molybdenite powders (~11.25 g) and PVP (~3.9 g) were dispersed in 250 mL of NMP, forming a mixture with an initial molybdenite concentration of 45 g L−1 and a PVP concentration of 15.6 g L−1. The above mixture was ultrasonically treated for ~20 min and then was poured into the sand mill. The synergistic exfoliation under milling and cavitation was kept for 4 h using the CUM process (Fig. 1). The diameter of the horn in the ultrasonication system was 10 mm, and the ultrasonication power was 280 W. The ultrasonication acted intermittently, i.e., 3 s on and 1 s off, avoiding damage to the ultrasonic processor because of heating. The rotation speed of the sand mill was kept at 2250 r.p.m. The as-obtained FL-MoS2 suspension was classified by centrifugation at various speeds to achieve FL-MoS2 dispersions. Some of the FL-MoS2 dispersions were centrifuged, washed carefully, and then freeze-dried to achieve FL-MoS2 nanosheets.

The initial concentration of natural molybdenite powders (C in,15–55 g L−1), ultrasonic power (P u, 200–350 W), rotation speed of sand mill (ω s, 1500–2250 r.p.m), exfoliation time (t ex, 0.5–6 h), and the molar ratio of PVP unit to MoS2 (R pm, 0–1) were chosen as the major influencing factors that were investigated systematically during the exfoliation. The exfoliation rate (R ex, g L−1 h−1) of FL-MoS2 nanosheets was measured by the FL-MoS2 concentration (C ti) in the upper dispersion after centrifuging the exfoliated suspension with a standing (more than ~24 h) at 1500 r.p.m for 45 min: R ex = (C t1 − C t2)/Δt = (C t1 − C t2)/(t 1 − t 2), where C t1 and C t2 were the FL-MoS2 concentrations of the upper dispersions obtained at exfoliation time t 1 and t 2, respectively. The exfoliation yield was defined as α = C 1/C 0 × 100 %, where C 1 was the FL-MoS2 concentration of the upper dispersion at the ending, and C 0 was the initial concentration of natural molybdenite powders. The FL-MoS2 concentration in the upper suspension was determined via the absorption coefficient (ε) at 670 nm according to the Beer-Lambert law (A/l = ε C) with a typically known concentration value (C’, g L−1). The concentration C was obtained by filtrating a certain amount (V, mL) of the target suspension, followed by washing, drying, and weighing the as-obtained solid species (m, mg): C’ = m/V [44]. The typical sample was made under the following parameters: R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, and t ex = 4 h. The FL-MoS2 dispersions and FL-MoS2 nanosheets were also prepared by the CUM process under various parameters (C in, P u, ω s, t ex, R pm) to investigate influencing factors.

In order to measure the exfoliation rate, a series of suspensions were sampled out for every 30 min and allowed to staying for ~24 h before centrifugation at 1500 r.p.m for 45 min. The absorption coefficients of the upper dispersions (2 mL) obtained by centrifugation were measured by UV-vis-IR absorption spectra. The concentrations of FL-MoS2 nanosheets in the upper dispersions were then calculated using the Beer-Lambert law.

For the purposes of comparison, the natural molybdenite powders were also exfoliated only using the ultrasonication or milling process. For the ultrasonication exfoliation (i.e., the U mode), 200 mL of NMP containing natural molybdenite powders (45 g L−1) and PVP (15.6 g L−1) was put in a wide-mouth bottle (250 mL) and ultrasonically treated for 4 h (280 W, 3 s on and 1 s off) using a φ10-mm horn. For the milling exfoliation using a sand mill (i.e., the M mode), the NMP mixture containing natural molybdenite powders (45 g L−1) and PVP (15.6 g L−1) was milled for 4 h using a rotation speed of 2250 r.p.m. Some of the MoS2 dispersions obtained by centrifugation at 1500 r.p.m for 45 min after standing for about 24 h were centrifuged once again at various speeds (e.g., 8000 r.p.m, 11,000 r.p.m) to achieve FL-MoS2 dispersions for further characterization and applications.

Characterization of FL-MoS2

The UV-vis spectra of the FL-MoS2 suspensions were recorded on a UV-1800PC spectrometer (Shanghai Mapada), and a quartz cell with a path length of 1.0 cm was used as the sample pool. The SEM images were obtained using a JEOL JSM-7500F scanning electron microscope, with an Au film coating (20 mA for 50 s) before SEM observation. The TEM images were measured using a field-emission transmission electron microscope (JEOL, JEM-2100) with an accelerating voltage of 200 kV. The Raman spectra were obtained using a Raman spectrometer (LabRAM HR Evolution, HORIBA JobinYvon, France) at 525 nm, and the powder samples were prepared on a SiO2/Si substrate. The X-ray diffraction (XRD) patterns were recorded on an XD-3 X-ray diffractometer (Beijing Purkinje General Instrument Co., Ltd., China) with a Cu Kα irradiation (λ = 0.15406 nm). The Fourier transformed infrared (FT-IR) spectra were recorded on a Bruker-Equinox 55 spectrometer in a transmittance mode in a wavenumber range of 4000 to 400 cm−1. The atomic force microscopy (AFM) measurement was performed on a Bruker NanoScope V instrument in a tapping mode. The N2 adsorption-desorption isotherms were obtained on a Surface Area and Porosity Analyzer (ASAP 2460, Micromeritics).

Test of Electrochemical Property

The electrochemical property of the FL-MoS2 nanosheets was characterized as electrocatalysts for hydrogen evolution reaction (HER) and as an active material for electrochemical sensors, respectively. For electrocatalytic applications, the upper FL-MoS2 dispersion obtained by centrifugation at 8000 r.p.m for 45 min was centrifuged once again at 10000 r.p.m for 45 min, and the as-obtained solid FL-MoS2 sample was used for HER test. To prepare electrodes, 4 mg of the FL-MoS2 nanosheets was dispersed in a mixture of Nafion (50 μL) and N, N-dimethylformamide (DMF, 950 μL) by sonication for more than 30 min to form a homogeneous ink. Before modification, the glassy carbon electrode (GCE) with a diameter of 3 mm was polished to a mirror finish using polish paper and alumina pastes of 50–70 μm and 30–50 nm, respectively, and then cleaned in an ultrasonic cleaner with acetone, alcohol, and water. Finally, 4 μL of the FL-MoS2 ink was carefully loaded onto the surface of the above GCE electrode to prepare electrodes modified with FL-MoS2 by allowing the liquids to evaporate under infrared light.

All electrochemical experiments were performed with a three-electrode system in which the Pt-wire electrode, saturated calomel electrode (SCE), and FL-MoS2-modified GCE (0.07 cm2) electrode were used as the counter, reference, and working electrodes, respectively. All measurements were carried out at room temperature. The HER activity was evaluated by linear sweep voltammetry conducted with a electrochemical working station (model CS310, Wuhan Correst Instruments Co., Ltd) with a scan rate of 2 mV s−1. The potential values with the reference of SCE electrode were calculated to be reverse hydrogen electrode (RHE): E (RHE) = E (SCE) + 0.241 V, in 0.5 M H2SO4. Cyclic voltammograms (CVs) were recorded in a potential range of −1.0–1.0 V to characterize the electrochemical sensing response to ascorbic acid (VC) at a potential scan rate of 20–150 mV s−1 in a solution consisting of 0.1 M KCl and ascorbic acid with different concentrations.

Results and Discussion

Exfoliation of Natural Molybdenite via the CUM Process

The exfoliation of natural molybdenite powders was conducted in a home-made coupled ultrasonication-milling (CUM) system. As Fig. 1a shows, this system consists of an ultrasonic instrument and a sand mill that are commercially available. Possible working mechanism in this CUM system can be described as Fig. 1b. Its unique feature is that the sand milling and ultrasonication can act at the same time. The major difference of between conventional wet ball milling and sand milling is their rotation speeds. The rotation speed of sand milling in this exfoliation is more than 2000 r.p.m, much higher than that of the conventional wet ball milling. Also, the special recycling in the sand milling can improve the exfoliation efficiency. With the CUM system, natural molybdenite powders can be exfoliated to few-layer MoS2 nanosheets via classification by centrifuging, as shown as Fig. 1c.

Natural molybdenite powders were exfoliated to FL-MoS2 via the CUM process using the synergistic effect of ultrasonic cavitation and shearing force (Fig. 1a). Figure 2 shows the SEM images of the pristine molybdenite powders and the FL-MoS2 nanosheets (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h). As Fig. 2a shows, the natural molybdenite consists of micro-scale powders with an irregular morphology and their particle sizes range 1–3 μm. Figure 2b shows the SEM image of the typical FL-MoS2 nanosheets, which were assembled to be thin films during the centrifugation by overlapping one another. The enlarged SEM image shown in Fig. 2c indicates that the FL-MoS2 nanosheets in the thin films are flexible nanosheets with a lateral length of several hundred nanometers.
Fig. 2
Fig. 2

SEM images of a the pristine natural molybdenite powders and b, c the FL-MoS2 nanosheets obtained by centrifugation at 5000–8000 r.p.m (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h)

Fig. 3
Fig. 3

Typical TEM observations of the FL-MoS2 nanosheets derived from natural molybdenite (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h): ad, g low-magnification TEM images, e, h SAED patterns, and f, i HRTEM images

Figure 3 shows the typical TEM observations of the FL-MoS2 nanosheets derived from natural molybdenite after centrifugation at 8000–10,000 r.p.m via the CUM process (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h). The low-magnification TEM image shown in Fig. 3a indicates that the FL-MoS2 nanosheets are individually dispersive and have a lateral size of 161 ± 66 nm according to the statistical data based on the TEM images. The enlarged TEM images in Fig. 3b–d, g show that the MoS2 nanosheets are very thin judged by the contrast. Figure 3e shows a selected area electron diffraction (SAED) pattern of a typical MoS2 nanosheets of Fig. 3d. The ordered diffraction lattice indicates the MoS2 nanosheet is single-crystal and can be readily indexed to a 2H-MoS2 phase. Its corresponding high-resolution TEM (HRTEM) image is shown in Fig. 3f, in which the highly ordered crystal lattice corroborates that the FL-MoS2 nanosheets, obtained via the CUM process, are of a perfect single-crystal nanostructure [50, 52]. The SAED pattern in Fig. 3h, corresponding to the lower particle of Fig. 3g, consists of two sets of ordered diffraction lattices, suggesting that two single-crystal MoS2 nanosheets are assembled together. Figure 3i shows the HRTEM image of the particle corner in Fig. 3g and no clear defects can be found in a large area [68]. From the TEM observations, one can conclude that the MoS2 sample obtained by exfoliating natural molybdenite powders via the CUM process takes on a thin plate-like morphology with lateral size of ~160 nm, and the FL-MoS2 nanosheets are of a perfect single-crystal structure.

Figure 4 shows the typical AFM images of the FL-MoS2 derived from natural molybdenite powders via the CUM process (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h) with centrifugation at 10,000 r.p.m. The AFM image in Fig. 4a shows the lateral size of the MoS2 nanosheets is about 100–250 nm, agreeing with the TEM observations (Fig. 3). Figure 4b–e show the AFM images of some typical MoS2 nanosheets with the corresponding height profiles (Fig. 4c, e). According to Fig. 4c, e, the thickness of the MoS2 nanosheets is about 1 nm, slightly larger than the thickness (~0.8 nm) of a single MoS2 layer exfoliated mechanically [43, 69]. This may be due to the presence of adsorbents on the nanosheets [70]. The AFM results, together with the TEM observations, corroborate that FL-MoS2 nanosheets, even single-layer ones, are successfully achieved via the CUM process using natural molybdenite powders as the starting materials.
Fig. 4
Fig. 4

Typical AFM images of the FL-MoS2 nanosheets derived from natural molybdenite powders (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, t ex = 4 h): a, b, d images, c a highth scan of the particle in b, and e a highth scan of the particle in d

Figure 5a shows the XRD patterns of the pristine natural molybdenite powders and the FL-MoS2 nanosheets exfoliated by the CUM process with centrifugation at 8000–10,000 r.p.m. For the natural molybdenite powders, the diffraction peaks at around 2θ = 14.2°, 32.4°, 33.23°, 35.6°, 44.0°, 50.0°, and 58.0° are assignable to the deflections from the planes of (002), (100), (101), (102), (104), (105), and (110) of a 2H-molybdenite (β-MoS2 or 2H-MoS2) with a hexagonal structure (space group: P63/mmc [194]) according to PDF # 37-1492. The cell parameters can be calculated to be a = 0.3181(3) nm, c = 1.234(1) nm, and cell vol. = 0.1082(2) nm3 using a program UnitCell (a method of TJB Holland and SAT Redfern 1995). The FL-MoS2 nanosheets show a similar XRD pattern, suggesting that the phase structure is not changed during the exfoliation by the CUM process, but the (002) peak broadens obviously. The calculated cell parameters of the FL-MoS2 nanosheets are a = 0.3180(4) nm, c = 1.235(2) nm, and cell vol. = 0.1081(3) nm3, similar to those of the natural molybdenite powders. The obvious broadening of the (002) diffraction peak after exfoliation indicates the FL-MoS2 nanosheets obtained by the CUM process have a small thickness [54], agreeing with the TEM, SEM, and AFM results.
Fig. 5
Fig. 5

a XRD patterns with normalized intensities of the pristine natural molybdenite and the exfoliated FL-MoS2 nanosheets obtained by centrifugation between 8000 and 10,000 r.p.m; b The UV-vis absorption spectra of (A) the FL-MoS2 suspension (the supernatant of the centrifugation at 8000 r.p.m) and (B) the FL-MoS2 suspension after standing for 42 days; c FT-IR spectra of the FL-MoS2 nanosheets obtained by centrifugation at 1500–8000 r.p.m and the pristine natural molybdenite; d Raman spectra for the pristine natural molybdenite (C) and the FL-MoS2 nanosheets (centrifugation at 1500–8000 r.p.m (D) and 8000–10,000 r.p.m (E), respectively, on a SiO2/Si substrate); e The N2 adsorption-desorption isotherms of the FL-MoS2 nanosheets (8000–10,000 r.p.m, S BET = 923.57 m2 g−1). All samples are obtained at the condition of R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m, and t ex = 4 h

Figure 5b shows the UV-vis spectra of the FL-MoS2 dispersions, i.e., (A) the supernatant just obtained by centrifugation at 8000 r.p.m for 45 min and (B) the one after standing for 42 days. One can find that the UV-vis absorption intensities at 605 and 667 nm of the FL-MoS2 dispersions before and after standing for 42 days are almost the same. Also, the color of the dark-green FL-MoS2 dispersion was not changed during the standing, and no sediment can be found at the bottom of the FL-MoS2 dispersion. The peaks at 667 and 605 nm arise from direct excitonic transitions at the K point of the Brillouin zone, and those at ~450 and ~400 nm can be assigned to the direct excitonic transition of the M point [65, 71]. This result confirms that the FL-MoS2 dispersion obtained by the CUM process is highly stable. Figure 5c shows the typical FT-IR spectra of the FL-MoS2 nanosheets and their precursor (i.e., the pristine molybdenite powder). The band at 475 cm−1 correspond to the characteristic vibration of the Mo-S bond due to the coupling vibration of Mo-S group, and the band at 3419 cm−1 corresponds to the stretching vibration of water molecules adsorbed on the surface, similar to literature [66]. The FL-MoS2 nanosheets and the pristine molybdenite powders have similar bands in their FT-IR spectra, indicating that no impurities were introduced during the exfoliation via the CUM process.

Raman spectra are also used to characterize the thickness of FL-MoS2 nanosheets. Figure 5d shows the Raman spectra of the pristine molybdenite powders and the solid FL-MoS2 nanosheets obtained after centrifugation at different centrifuging speeds (i.e., one FL-MoS2 sample obtained by centrifuging the supernatant of 1500 at 8000 r.p.m and the other one by centrifuging the supernatant of 8000 at 10,000 r.p.m). For the pristine molybdenite powders, a typical peak at 374.4 cm−1, known as E1 2g, originates from the in-plane vibration of the Mo-S bond, and an A1g peak at 400.4 cm−1 from out-of-plane vibrations is also observed [53]. After exfoliation by the CUM process, the E1 2g and A1g peaks of the FL-MoS2 nanosheets shift towards higher frequency (i.e., blueshift), and the peak difference between E1 2g and A1g is about 25 cm−1. The blueshift of peak A1g can be used to estimate the layer number of MoS2 nanosheets [69]. The higher centrifugation speed achieves smaller FL-MoS2 nanosheets. The blueshift of Raman shift indicates that the MoS2 nanosheets exfoliated by the CUM process consist of a large amount of thin MoS2 nanosheets with few layers [9].

Figure 5e shows the N2 adsorption-desorption isotherms of the FL-MoS2 nanosheets obtained by centrifuging the supernatant of 8000 at 10,000 r.p.m. The FL-MoS2 nanosheets do not show a porous microstructure. The BET specific surface area of the FL-MoS2 nanosheets is as high as 924 m2 g−1, whereas their precursor of the pristine molybdenite is only 29 m2 g−1.

X-ray photoelectron spectroscopy (XPS) was further used to characterize the chemical compositions of the FL-MoS2 nanosheets derived by the CUM process. Figure 6 shows the XPS spectra of the FL-MoS2 nanosheets obtained by centrifuging the supernatant of 1500 at 8000 r.p.m for 45 min. Figure 6a shows the survey. The major XPS peaks can be assignable to the elements of Mo, S, O, and C, and some weak peaks may correspond to Zr and Tc elements. Mo and S come from the FL-MoS2 nanosheets. The elements of O and C are due to the substances (e.g., PVP, CO2) adsorbed on the samples. The possible elements of Zr and Tc may come from the ultrasonication horn in the CUM system. Figure 6b shows the core XPS spectrum of Mo 3d. The strong peaks at around 229.0 and 232.1 eV correspond to Mo4+ 3d5/2 and Mo4+ 3d3/2, respectively, and the weak peak at 226.1 eV corresponds to S 2s [72]. Figure 6c shows the core XPS spectrum of S 2p, and the peaks at 163.0 and 161.8 eV correspond to the S 2p1/2 and S 2p3/2 orbitals of divalent sulfide ions, respectively. According to the XPS spectra, Mo and S in the FL-MoS2 are in good agreement with the binding energies of Mo4+ and S2− ions in the 2H-MoS2 phase.
Fig. 6
Fig. 6

X-ray photoelectron spectroscopy (XPS) of the FL-MoS2 nanosheets (1500–8000 r.p.m): a a survey scan, b Mo 3d, and c S 2p

Factors Influencing the Exfoliation in the CUM Process

To further understand the exfoliation of natural molybdenite powders using the CUM process, we carefully designed a series of control experiments to check the factors that influence the exfoliation. The concentrations of the FL-MoS2 nanosheets in the NMP suspensions were measured using the UV-vis-IR spectra mentioned in the experimental section. The influencing factors we checked included the exfoliation times, the initial concentrations of natural molybdenite powders, ultrasonic power, rotation speed of sand mill, and PVP concentration. Figures 7 and 8 show the typical results.
Fig. 7
Fig. 7

a The UV-vis-IR spectra of the FL-MoS2 suspensions (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m) with various exfoliation times (t ex); b the concentrations, and c yield of the FL-MoS2 suspensions after different exfoliation times

Fig. 8
Fig. 8

The effects of exfoliating parameters on the supernatant concentration (C ex), exfoliation rate and yield of FL-MoS2 nanosheets from natural molybdenite powders: ac the initial concentration of natural molybdenite (C in = 15–55 g L−1 when P u = 280 W, ω s = 2250 r.p.m, R pm = 1/2); (df) ultrasonic powers (P u = 200–350 W when C in = 45 g L−1, ω s = 2250 r.p.m, R pm = 1/2); gi rotation speeds (ω s = 1500–2250 r.p.m when C in = 45 g L−1, P u = 280 W, R pm = 1/2); jl molar ratios of PVP to MoS2 (R pm = 0–1 when C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m)

Figure 7a shows the UV-vis-IR absorption spectra of the FL-MoS2 suspensions in the CUM process (R pm = 1/2, C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m) with various exfoliation times (t ex = 0.5–6 h). All the UV-vis-IR spectra take on a similar profile and their absorbance values increases with the increase in the exfoliated time. Figure 7b shows the plot of the concentrations of the FL-MoS2 nanosheets versus the exfoliation times, obtained according to the Beer-Lambert law. One can see that the concentration of FL-MoS2 nanosheets in the NMP suspension increases linearly with the increase in exfoliation time [73]. The slope of the linear-fitting line can be seen as the exfoliation rate, and the exfoliation rate in the present condition reaches 1.42 g L−1 h−1. Figure 7c shows the yield of FL-MoS2 nanosheets at various exfoliation times. The yield increases linearly with the exfoliation time and reaches 21.6 % when the exfoliation time is 6 h.

The typical results on the factors that influence the exfoliation behavior in the CUM process are summarized in Fig. 8. Figure 8a–c show the effect of the initial concentrations (C in, 15–55 g L−1) of natural molybdenite powders on the exfoliation rate and yield of natural molybdenite powders (P u = 280 W, S r = 2250 r.p.m, R pm = 1/2). Figure 8a shows the change in the concentration of the FL-MoS2 (i.e., supernatants obtained by centrifuging at 1500 r.p.m for 45 min after settling for more than 24 h) as the exfoliation time increases with various initial concentrations of natural molybdenite powders. The exfoliation rate and yield with various initial concentrations of natural molybdenite powders are shown in Fig. 8b, c, respectively. The increase in the initial concentration of the molybdenite powders is favorable to enhance the exfoliation rate, but the yield is not in a similar case. Low initial concentration (15 g L−1) achieves a higher yield (~23 %) of FL-MoS2 nanosheets and makes better dispersion of FL-MoS2 nanosheets than the higher ones. Considering the exfoliation amount, we chose an initial molybdenite concentration of 45 g L−1 for the following exfoliation experiments. Figure 8d–f show the effect of ultrasonic powers (P u, 200–350 W) on the exfoliation behavior of natural molybdenite powders (C in = 45 g L−1, ω s = 2250 r.p.m, R pm = 1/2). One can see that the higher ultrasonic powers are helpful to improve the exfoliation rate and yield, but this effect is not so obvious. When the ultrasound power is 280 W, the exfoliation yield at 4 h reached highest value of ~20 %. As we know, the ultrasound at a low input power corresponds to the stable cavitation, and the knocking on the right sides of plates has little ability to destroy the covalently bonded S-Mo-S, while the knocking on their profiles can easily overcome van der Waals forces between MoS2 nanosheets. When the input power increases, the ultrasound corresponds to inertial cavitation, and the increase in the number of cavitation bubbles leads to a small amount of useful bubbles, weakening the knocking intensity [67]. Therefore, too high or too low sonication power is not beneficial to enhance the exfoliation yield. The ultrasonication power is determined at 280 W in the following experiments. Figure 8g–i show the effect of the rotation speed (ω s, 1500–2250 r.p.m) of the sand mill on the exfoliation rate and yield at similar conditions (C in = 45 g L−1, P u = 280 W, R pm = 1/2). The yield has the highest value when the rotation speed is 2250 r.p.m. A higher rotation speed is more favorable to overcome the van der Waals forces between the MoS2 layers and then leads to more defects which accelerate the exfoliation with the synergistic effect of ultrasound. Considering the safety and noise of the sand mill, a suitable rotation speed of 2250 r.p.m is chosen. Figure 8j–l show the effect of PVP concentrations (R pm, 0–1) on the exfoliation behavior (C in = 45 g L−1, P u = 280 W, ω s = 2250 r.p.m). The exfoliation rate and yield increase with the increase of the PVP concentration. PVP molecules in the CUM process act both as the dispersing agent and separating agent to prevent aggregation of the exfoliated MoS2 nanosheets. But, if the PVP concentration is too high, the viscosity of the suspension increase rapidly, and the high viscosity leads to a terrible fluidity, resulting in a bad effect on the exfoliation [74]. The PVP content used in the CUM process is kept at R pm = 1/2 in the present experiments.

To demonstrate the synergistic effect of milling and ultrasonication, we comparatively conducted exfoliation experiments under the similar conditions but using different exfoliation modes: coupled ultrasonication-milling (the CUM mode), milling (the M mode) and ultrasonication (the U mode). Figure 9 shows the exfoliation behavior using the three exfoliation modes (P u = 280 W, C in = 45 g L−1, ω s = 2250 r.p.m, R pm = 1/2). One can see that the CUM process is more efficient in the exfoliation of natural molybdenite powders to form FL-MoS2. The exfoliation yield of the CUM process is ~19.9 %, higher than that (18.4 %) of the M process and that (15.4 %) of the U process. The CUM process combines the advantages of both ultrasonic cavitation and shear action in the exfoliation process. During the exfoliation process, the high-speed rotating balls in the M mode knock the edges of the MoS2 layers and lead to a large amount of defects and cracks, which are in favor of the insertion of solvent molecules into the interlayer spaces and then overcome the van der Waals forces. Also, the CUM system can realize a continuous process: the milling and ultrasonication can work at the same time. The defects and cracks caused by the milling process are helpful to improve the shearing action of ultrasonication greatly. The shear action and the knocking of cavitation cut down and exfoliate layered molybdenite powders to form smaller and thinner MoS2 nanosheets, which are protected by the PVP molecules instantly.
Fig. 9
Fig. 9

Comparison of the exfoliation yield using different exfoliation mode (U ultrasonication, M milling, and CUM coupled ultrasonication-milling) under the condition of R pm = 1/2, C in = 45 g L−1, P u = 280 W and ω s = 2250 r.p.m

Considering the above results (Figs. 7, 8, and 9), one can safely conclude that the PVP content (R pm) has the most important effect on the exfoliation of natural molybdenite powders to FL-MoS2 nanosheets in the CUM process when compared with the other experimental parameters, including the initial concentration of natural molybdenite powders (C in), ultrasonic power (P u), and rotation speed of sand mill (ω s). The optimal experimental parameters in the CUM process can be determined as R pm = 1/2, C in = 45 g L−1, P u = 280 W, and ω s = 2250 r.p.m judging from the overall aspects. The exfoliation yield of FL-MoS2 nanosheets under the optimal condition for 6 h can reach 21.6 %.

Electrochemical Performance of FL-MoS2 Nanosheets Derived by the CUM Process

Electrochemical application is one of the most important aspects for the FL-MoS2 nanosheets. Figure 10 shows the electrocatalytic performance of the pristine molybdenite powders (A) and the FL-MoS2 nanosheets obtained by centrifugation at 1500–8000 r.p.m (B) and at 8000–10,000 r.p.m (C), respectively. Figure 10a shows the typical polarization curves, and their corresponding Tafel plots are shown in Fig. 10b. It is clear that the higher the centrifugation speed, the thinner the FL-MoS2 nanosheets are in the same exfoliation using the CUM process. As Fig. 10 shows, the FL-MoS2 nanosheets obtained at 8000–10,000 r.p.m (C) have the lowest onset overpotential and the largest exchange current density at a given overpotential among the three samples (A, B, and C). By fitting the Tafel plots linearly according to the equation of η = a + blog|j| (where η is overpotential, j is current density, and b is Tafel slope) [75], one can find that the FL-MoS2 nanosheets obtained at 8000–10,000 r.p.m have a Tafel slope of 156 mV dec−1, lower than that (165 mV dec−1) of the pristine molybdenite powders and that (160 mV dec−1) of the FL-MoS2 nanosheets obtained at 1500–8000 r.p.m. We note that the Tafel slope of the FL-MoS2 nanosheets obtained by the CUM process is a little larger than that of some MoS2 nanocrystals reported [30, 76]. For examples, a Tafel slope of ~120 mV dec−1 was reported for the MoS2 nanomaterials synthesized at a temperature of ~500 °C [76] and 140–145 mV dec−1 at a temperature of ~850 °C [30]. The better HER performance of MoS2-based composites has also been reported, resulting in a Tafel slope of 87 mV dec−1 for MoS2 and 51 mV dec−1 for O-MoS2/G [26]. The above samples were synthesized through a conventional hydrothermal reaction using fine chemical reagents as the starting materials. Also, hybridization with other species is another reason to improve their HER performance. Therefore, fine control in the size and morphology (i.e., more edge sites and smaller size) of the MoS2 nanosheets and hybridization with other functional species (i.e., graphene) are the possible directions to improve the electrochemical performance of the FL-MoS2 nanosheets obtained via the present CUM process from natural molybdenite. The larger Tafel slope obtained in the present work may be due to the difference of the natural molybdenite from other synthetic MoS2 in phase compositions. The low electrical conductivity, the possible re-stacking of FL-MoS2 nanosheets, the residue of PVP molecules, and the relatively high-temperature treatment in electrode preparation are also possible reasons that lead to a larger Tafel slope. To improve the electrical conductivity, carbon can be used to modify FL-MoS2 nanosheets to design highly efficient electrocatalysts for hydrogen evolution reaction and to obtain a lower Tafel slope (47 mV dec−1) [77]. Functional modification of the FL-MoS2 nanosheets is under way.
Fig. 10
Fig. 10

a The polarization curves and b Tafel plots of the pristine molybdenite (A) and FL-MoS2 nanosheets (B: 1500–8000 r.p.m; C: 8000–10,000 r.p.m)

The electrochemical sensing performance of the FL-MoS2 nanosheets was also investigated. Figure 11a shows the CV curves of the GCE modified with the FL-MoS2 nanosheets obtained at 8000–10,000 r.p.m in the presence of ascorbic acid (AA) aqueous solutions with different concentrations ([AA] = 0.5–2 mM, [KCl] = 0.1 M, scan rate = 50 mV s−1). Figure 11b shows the plots of the intensities of the anodic peak current versus the ascorbic acid concentration. The intensity of the CV peak current increases obviously with the increase in the concentration of ascorbic acid. The linear regression equation of the anodic peak obtained according to the CV curves in Fig. 11a is I (uA) = 2.08 (Vs−1) · [AA] (mM) – 4.5605, and R 2 = 0.98. The high correlation coefficient suggests a nice linearity correlation between the anodic peak current and ascorbic acid (AA) concentrations in a range of 0.5–2 mM. Unfortunately, the biosensor is of a poor performance, which is possibly caused by the low electrical conductivity of the MoS2 nanosheets. To anchor a second-phase particles on the MoS2 nanosheets is under our consideration to enhance their electrochemical sensing properties. Actually, MoS2 nanosheets have been used as the supporting material to stabilize metal nanoparticles (e.g., Au) to form hierarchical nanocomposites for the detection of chemical and biological molecules [78]. The FL-MoS2 nanosheets exfoliated by the CUM process can be a promising active material or support to construct electrochemical electrodes for the electrochemical detection of chemical and biological molecules.
Fig. 11
Fig. 11

a CV curves of the GC electrode modified with the FL-MoS2 nanosheets in the presence of ascorbic acid (AA) aqueous solutions with different concentrations ([KCl] = 0.1 M, scan rate = 50 mV s−1); b The plots of the intensities of the anodic peak current against the ascorbic acid concentration


In summary, a novel coupled ultrasonication-milling (CUM) process has been developed for the first time to exfoliate the natural molybdenite powders to synthesize FL-MoS2 nanosheets in the NMP solution using PVP as the exfoliation agent. The factors that influence the exfoliation behavior during the CUM process have been systematically investigated. The FL-MoS2 nanosheets obtained at the optimal conditions (i.e., initial molybdenite concentration = 45 g L−1, ultrasonic power = 280 W, rotation speed of sand mill = 2250 r.p.m, and the mole ratio of PVP to MoS2 = 0.5), taken on a thin single-crystal plate-like morphology, several nanometers in thickness and hundred nanometers in width. The as-obtained FL-MoS2 nanosheets have a high specific surface area of 924 m2 g−1, much larger than that (29 m2 g−1) of their precursor (i.e., molybdenite powders). The yield of FL-MoS2 nanosheets obtained by the CUM process for 6 h reaches to 21.6 %, much larger than that of the literature reported. Also, the CUM process has a higher yield than the ultrasonication (U) or milling (M) process, confirming that the synergistic effect of the ultrasonication and milling process is obvious in the exfoliation of natural molybdenite powders. The as-obtained FL-MoS2 nanosheets show highly enhanced electrocatalytic performance in hydrogen evolution reaction and good electrochemical sensing property in detecting ascorbic acid when compared with their precursor. The exfoliation of natural molybdenite via the coupled ultrasonication-milling process developed here provides a novel, green, efficient, scalable, and cost-effective approach to prepare FL-MoS2 nanosheets that are of promising applications as electrocatalytic and sensing-active materials.



Coupled ultrasonication-milling


Few-layer MoS2


Liquid-phase exfoliation




Molybdenum disulfide









The authors thank Prof. Hongxia Lu, Prof. Hongliang Xu, Prof. Hailong Wang, Dr. Bingbing Fan, Dr. Gang Shao, and Mr. Tao Li for their kind helps in some experiments. Chen thanks Dr. Guosheng Han for his help in the TEM observations.


This work was partly sponsored by National Natural Science Foundation of China (NSFC no. 51172211, 51574205), Program for Science and Technology Innovation Talents in Universities of Henan Province (14HASTIT011), Special Support Program for High-End Talents of Zhengzhou University (ZDGD13001), Program for High-level Talents of Dongguan University of Technology (G2009 06-17), and Plan for Scientific Innovation Talent of Henan Province (154100510003).

Authors’ Contributions

HD did experimental works and made a draft. KW did some of experimental works. RZ participated to the discussion. DC provided the idea, designed the experiment, and wrote and revised the paper. All authors read and approved the final manuscript.

Competing Interests

The authors declare that they have no competing interests.

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (, which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

School of Materials Science and Engineering, Zhengzhou University, Zhengzhou, 450001, People’s Republic of China
School of Chemical Engineering and Energy Technology, Dongguan University of Technology, Dongguan, 523808, People’s Republic of China
Laboratory of Aeronautical Composites, Zhengzhou Institute of Aeronautical Industry Management, Zhengzhou, 450046, People’s Republic of China


  1. Geim AK (2009) Graphene: status and prospects. Science 324:153–4View ArticleGoogle Scholar
  2. Hernande Y, Nicolosi V, Lotya M, Hernandez Y, Nicolosi V, Lotya M, Blighe FM, Sun ZY, De S, McGovern IT, Holland B, Byrne M, Gun'Ko YK, Boland JJ, Niraj P, Duesberg G, Krishnamurthy S, Goodhue R, Hutchison J, Scardaci V, Ferrari AC, Coleman JN (2008) High-yield production of graphene by exfoliation of graphite in surfactant/water solutions. Nat Nanotechnol 3:563–8View ArticleGoogle Scholar
  3. Lotya M, Hernandez Y, King PJ, King PJ, Smith RJ, Nicolosi V, Karlsson LS, Blighe FM, De S, Wang ZM, McGovern IT, Duesberg GS, Coleman JN (2009) Liquid phase production of graphene by exfoliation of graphite in surfactant/water solutions. J Am Chem Soc 131:3611–20View ArticleGoogle Scholar
  4. Xu HX, Suslick KS (2011) Sonochemical preparation of functionalized graphenes. J Am Chem Soc 133:9148–51View ArticleGoogle Scholar
  5. Benavente E, Ana MAS, Mendizabal F, Gonzalez G (2002) Intercalation chemistry of molybdenum disulfide. Coord Chem Rev 224:87–109View ArticleGoogle Scholar
  6. Jawaid A, Nepal D, Park K, Jespersen M, Qualley A, Mirau P, Drummy LF, Vaia RA (2016) Mechanism for liquid phase exfoliation of MoS2. Chem Mater 28:337–48Google Scholar
  7. Mak KF, Lee C, Hone J, Shan J, Heinz TF (2010) Atomically thin MoS2: a new direct-gap semiconductor. Phys Rev Lett 105:136805–8View ArticleGoogle Scholar
  8. Radisavljevic B, Radenovic A, Brivio J, Giacometti V, Kis A (2011) Single-layer MoS2 transistors. Nat Nanotechnol 6:147–150View ArticleGoogle Scholar
  9. Niu LY, Li K, Zhen HY, Chui YS, Zhang WJ, Yan F, Zheng ZJ (2014) Salt-assisted high-throughput synthesis of single- and few-layer transition metal dichalcogenides and their application in organic solar cells. Small 10:4651–7View ArticleGoogle Scholar
  10. Liu WS, Zhao CY, Zhou R, Zhou D, Liu ZL, Lu XH (2015) Lignin-assisted exfoliation of molybdenum disulfide in aqueous media and its application in lithium ion batteries. Nanoscale 7:9919–26View ArticleGoogle Scholar
  11. Liu YD, Ren L, Qi X, Yang LW, Hao GL, Li J, Wei XL, Zhong JX (2013) Preparation, characterization and photoelectrochemical property of ultrathin MoS2 nanosheets via hydrothermal intercalation and exfoliation route. J Alloy Compd 571:37–42View ArticleGoogle Scholar
  12. Eng AYS, Ambrosi A, Sofer Z, Simek P, Pumera M (2014) Electrochemistry of transition metal dichalcogenides: strong dependence on the metal-to-chalcogen composition and exfoliation method. ACS Nano 8:12185–98View ArticleGoogle Scholar
  13. Ma L, Huang GC, Chen WX, Wang Z, Ye JB, Li HY, Chen DY, Lee JY (2014) Cationic surfactant-assisted hydrothermal synthesis of few-layer molybdenum disulfide/grapheme composites: microstructure and electrochemical lithium storage. J Power Sources 264:262–71View ArticleGoogle Scholar
  14. Hwang H, Kim H, Cho J (2011) MoS2 nanoplates consisting of disordered graphene-like layers for high rate lithium battery anode materials. Nano Lett 11:4826–30View ArticleGoogle Scholar
  15. Jia SS, Yan Z, Zhang C, Liu ZY, Tjiu WW, Phang IY, Zhang Z, Pan JS, Liu TX (2013) Exfoliated MoS2 nanosheets as efficient catalysts for electrochemical hydrogen evolution. Electrochim Acta 109:269–75View ArticleGoogle Scholar
  16. Zheng XL, Xu JB, Yan KY, Wang H, Wang ZL, Yang SH (2014) Space-confined growth of MoS2 nanosheets within graphite: the layered hybrid of MoS2 and graphene as an active catalyst for hydrogen evolution reaction. Chem Mater 26:2344–53View ArticleGoogle Scholar
  17. Benson J, Li MX, Wang SB, Wang P, Papakonstantinou P (2015) Electrocatalytic hydrogen evolution reaction on edges of a few layer molybdenum disulfide nanodots. ACS Appl Mater Interfaces 7:14113–22View ArticleGoogle Scholar
  18. Chia XY, Ambrosi A, Sofer Z, Luxa J, Pumera M (2015) Catalytic and charge transfer properties of transition metal dichalcogenides arising from electrochemical pretreatment. ACS Nano 9:5164–79View ArticleGoogle Scholar
  19. Li DJ, Maiti UN, Lim J, Choi DS, Lee WJ, Oh Y, Lee GY, Kim SO (2014) Molybdenum sulfide/N-doped CNT forest hybrid catalysts for high-performance hydrogen evolution reaction. Nano Lett 14:1228–33View ArticleGoogle Scholar
  20. Rao CNR, Gopalakrishnan K, Maitra U (2015) Comparative study of potential applications of graphene, MoS2, and other two-dimensional materials in energy devices, sensors, and related areas. ACS Appl Mater Interfaces 7:7809–32View ArticleGoogle Scholar
  21. Sarkar D, Xie XJ, Kang JH, Zhang HJ, Liu W, Navarrete J, Moskovits M, Banerjee K (2015) Functionalization of transition metal dichalcogenides with metallic nanoparticles: implications for doping and gas-sensing. Nano Lett 15:2852–62View ArticleGoogle Scholar
  22. Krane N, Lotze C, Lager JM, Reecht G, Franke, KJ (2016) Electronic structure and luminescence of quasi-freestanding MoS2 nanopatches on Au(111). Nano Lett 16:5163–8Google Scholar
  23. Yu XY, Prevot MS, Sivula K (2014) Multiflake Thin film electronic devices of solution processed 2D MoS2 enabled by sonopolymer assisted exfoliation and surface modification. Chem Mater 26:5892–9View ArticleGoogle Scholar
  24. Sorkin V, Pan H, Shi H, Quek SY, Zhang YW (2014) Nanoscale transition metal dichalcogenides: structures, properties, and applications. Crit Rev Solid State Mater Sci 39:319–67View ArticleGoogle Scholar
  25. Peng K, Fu LJ, Ouyang J, Yang HM (2016) Emerging parallel dual 2D composites: natural clay mineral hybridizing MoS2 and interfacial structure. Adv Funct Mater 26:2666–75View ArticleGoogle Scholar
  26. Guo JX, Li FF, Sun YF, Zhang X, Tang L (2015) Oxygen-incorporated MoS2 ultrathin nanosheets grown on graphene for efficient electrochemical hydrogen evolution. J Power Sources 291:195–200View ArticleGoogle Scholar
  27. Li F, Li J, Lin XQ, Li XZ, Fang YY, Jiao LX, An XC, Fu Y, Jin J, Li R (2015) Designed synthesis of multi-walled carbon nanotubes@Cu@MoS2 hybrid as advanced electrocatalyst for highly efficient hydrogen evolution reaction. J Power Sources 300:301–8View ArticleGoogle Scholar
  28. Voiry D, Salehi M, Silva R, Fujita T, Chen MW, Asefa T, Shenoy VB, Eda G, Chhowalla M (2013) Conducting MoS2 nanosheets as catalysts for hydrogen evolution reaction. Nano Lett 13:6222–7View ArticleGoogle Scholar
  29. Guardia L, Paredes JI, Munuera JM, Villar-Rodil S, Ayan-Varela M, Martinez-Alonso A, Tascon JMD (2014) Chemically exfoliated MoS2 nanosheets as an efficient catalyst for reduction reactions in the aqueous phase. ACS Appl Mater Interfaces 6:21702–10View ArticleGoogle Scholar
  30. Yu YF, Huang SY, Li YP, Steinmann SN, Yang WT, Cao LY (2014) Layer-dependent electrocatalysis of MoS2 for hydrogen evolution. Nano Lett 14:553–8View ArticleGoogle Scholar
  31. Huang JW, Dong ZP, Li YR, Li J, Tang WJ, Yang HD, Wang J, Bao Y, Jin J, Li R (2013) MoS2 nanosheet functionalized with Cu nanoparticles and its application for glucose detection. Mater Res Bull 48:4544–7View ArticleGoogle Scholar
  32. Huang KJ, Wang L, Li J, Liu YM (2013) Electrochemical sensing based on layered MoS2-graphene composites. Sens Actuators B 178:671–7View ArticleGoogle Scholar
  33. Zhu CF, Zeng ZY, Li H, Li F, Fan CH, Zhang H (2013) Single-layer MoS2-based nanoprobes for homogeneous detection of biomolecules. J Am Chem Soc 135:5998–6001View ArticleGoogle Scholar
  34. Su S, Sun HF, Xu F, Yuwen LH, Wang LH (2013) Highly sensitive and selective determination of dopamine in the presence of ascorbic acid using gold nanoparticles-decorated MoS2 nanosheets modified electrode. Electroanal 25:2523–9View ArticleGoogle Scholar
  35. Wang TY, Zhu HC, Zhuo JQ, Zhu ZW, Papakonstantinou P, Lubarsky G, Lin J, Li MX (2013) Biosensor based on ultrasmall MoS2 nanoparticles for electrochemical detection of H2O2 released by cells at the nanomolar level. Anal Chem 85:10289–95View ArticleGoogle Scholar
  36. Huang KJ, Zhang JZ, Shi GW, Liu YM (2014) Hydrothermal synthesis of molybdenum disulfide nanosheets as supercapacitors electrode material. Electrochim Acta 132:397–403View ArticleGoogle Scholar
  37. Shi SP, D aqiang Gao DQ, Xia BR, Liu PT, Xue DS (2015) Enhanced hydrogen evolution catalysis in MoS2 nanosheets by incorporation of a metal phase. J Mater Chem A3:24414–21Google Scholar
  38. Zhang K, Kim HJ, Shi XJ, Lee JT, Choi JM, Song MS, Park JH (2013) Graphene/acid coassisted synthesis of ultrathin MoS2 nanosheets with outstanding rate capability for a lithium battery anode. Inorg Chem 52:9807–12View ArticleGoogle Scholar
  39. Zhan YJ, Liu Z, Najmaei S, Ajayan PM, Lou J (2012) Large-area vapor-phase growth and characterization of MoS2 atomic layers on a SiO2 substrate. Small 8:966–971View ArticleGoogle Scholar
  40. Wang XS, Feng HB, Wu YM, Jiao LY (2013) Controlled synthesis of highly crystalline MoS2 flakes by chemical vapor deposition. J Am Chem Soc 135:5304–7View ArticleGoogle Scholar
  41. George AS, Mutlu Z, Ionescu R, Wu RJ, Jeong JS, Bay HH, Chai Y, Mkhoyan KA, Ozkan M, Ozkan CS (2014) Wafer scale synthesis and high resolution structural characterization of atomically thin MoS2 layers. Adv Funct Mater 24:7461–6View ArticleGoogle Scholar
  42. Liu KK, Zhang WJ, Lee YH, Lin YC, Chang MT, Su CY, Chang CS, Li H, Shi YM, Zhang H, Lai CS, Li LJ (2012) Growth of large-area and highly crystalline MoS2 thin layers on insulating substrates. Nano Lett 12:1538–44View ArticleGoogle Scholar
  43. Li H, Wu JMT, Yin ZY, Zhang H (2014) Preparation and applications of mechanically exfoliated single-layer and multilayer MoS2 and WSe2 nanosheets. Acc Chem Res 47:1067–75View ArticleGoogle Scholar
  44. Varrla E, Backes C, Paton KR, Harvey A, Gholamvand Z, McCauley J, Coleman JN (2015) Large-scale production of size-controlled MoS2 nanosheets by shear exfoliation. Chem Mater 27:1129–39View ArticleGoogle Scholar
  45. Ambrosi A, Sofer Z, Pumera M (2015) Lithium intercalation compound dramatically influences the electrochemical properties of exfoliated MoS2. Small 11:605–12View ArticleGoogle Scholar
  46. Lukowski MA, Daniel AS, Meng F, Forticaux A, Li LS, Jin S (2013) Enhanced hydrogen evolution catalysis from chemically exfoliated metallic MoS2 Nanosheets. J Am Chem Soc 135:10274–7View ArticleGoogle Scholar
  47. Zheng J, Zhang H, Dong SH, Liu YP, Nai CT, Shin HS, Jeong HY, Liu B, Loh KP (2014) High yield exfoliation of two-dimensional chalcogenides using sodium naphthalenide. Nat Commun 5:2995–3001Google Scholar
  48. Jeffery AA, Nethravathi C, Rajamathi M (2014) Two-dimensional nanosheets and layered hybrids of MoS2 and WS2 through exfoliation of ammoniated MS2 (M = Mo, W). J Phys Chem C 118:1386–96View ArticleGoogle Scholar
  49. Zeng ZY, Yin ZY, Huang X, Li H, He QY, Lu G, Boey F, Zhang H (2011) Single-layer semiconducting nanosheets: high-yield preparation and device fabrication. Angew Chem Int Ed 50:11093–7View ArticleGoogle Scholar
  50. Liu N, Kim P, Kim JH, Ye JH, Kim S, Lee CJ (2014) Large-area atomically thin MoS2 nanosheets prepared using electrochemical exfoliation. ACS Nano 8:6902–10View ArticleGoogle Scholar
  51. Coleman JN, Lotya M, O’Neill A, Bergin SD, King PJ, Khan U, Young K, Gaucher A, De S, Smith RJ, Shvets IV, Arora SK, Stanton G, Kim HY, Lee K, Kim GT, Duesberg GS, Hallam T, Boland JJ, Wang JJ, Donegan JF, Grunlan JC, Moriarty G, Shmeliov A, Nicholls RJ, Perkins JM, Grieveson EM, Theuwissen K, McComb DW, Nellist PD, Nicolosi V (2011) Two-dimensional nanosheets produced by liquid exfoliation of layered materials. Science 331:568–71View ArticleGoogle Scholar
  52. Nicolosi V, Chhowalla M, Kanatzidis MG, Strano MS, Coleman JN (2013) Liquid exfoliation of layered materials. Science 340:1226419View ArticleGoogle Scholar
  53. Halim U, Zheng CR, Chen Y, Lin ZY, Jiang S, Cheng R, Huang Y, Duan XF (2013) A rational design of cosolvent exfoliation of layered materials by directly probing liquid–solid interaction. Nat Commun 4:2213–9View ArticleGoogle Scholar
  54. Bang GS, Nam KW, Kim JY, Shin J, Choi JW, Choi SY (2014) Effective liquid-phase exfoliation and sodium ion battery application of MoS2 nanosheets. ACS Appl Mater Interfaces 6:7084–9View ArticleGoogle Scholar
  55. Muscuso L, Cravanzola S, Cesano F, Scarano D, Zecchina A (2015) Optical, vibrational and structural properties of MoS2 nanoparticles obtained by exfoliation and fragmentation via ultrasound cavitation in isopropyl alcohol. J Phys Chem C 119:3791–801View ArticleGoogle Scholar
  56. Ravula S, Essner JB, Baker GA (2015) Kitchen-inspired manochemistry: dispersion, exfoliation, and hybridization of functional MoS2 nanosheets using culinary hydrocolloids. Chem Nano Mat 1:167–77Google Scholar
  57. Guan GJ, Zhang SY, Liu SH, Cai YQ, Low M, Teng CP, Phang IY, Cheng Y, Duei KL, Srinivasan BM, Zheng YG, Zhang YW, Han MY (2015) Protein induces layer-by-layer exfoliation of transition metal dichalcogenides. J Am Chem Soc 137:6152–5View ArticleGoogle Scholar
  58. Gopalakrishnan D, Damien D, Shaijumon MM (2014) MoS2 quantum dot-interspersed exfoliated MoS2 nanosheets. ACS Nano 8:5297–303View ArticleGoogle Scholar
  59. Zhang X, Lai ZC, Liu ZD, Tan CL, Huang Y, Li B, Zhao MT, Xie LH, Huang W, Zhang H (2015) A facile and universal top-down method for preparation of monodisperse transition-metal dichalcogenide nanodots. Angew Chem Int Ed 54:5425–8View ArticleGoogle Scholar
  60. Carey BJ, Daeneke T, Nguyen EP, Wang YC, Zhen Ou J, Zhuiykov S, Kalantar-zadeh K (2015) Two solvent grinding sonication method for the synthesis of two-dimensional tungsten disulphide flakes. Chem Commun 51:3770–3View ArticleGoogle Scholar
  61. Yao YG, Lin ZY, Li Z, Song XJ, Moona KS, Wong CP (2012) Large-scale production of two-dimensional nanosheets. J Mater Chem 22:13494–9View ArticleGoogle Scholar
  62. Wang Y, Zhou CH, Wang WC, Zhao YP (2013) Preparation of two dimensional atomic crystals BN, WS2, and MoS2 by supercritical CO2 assisted with ultrasound. Ind Eng Chem Res 52:4379–82View ArticleGoogle Scholar
  63. Jin Z, Lomeda JR, Price BK, Lu W, Zhu Y, Tour JM (2009) Mechanically assisted exfoliation and functionalization of thermally converted graphene sheets. Chem Mater 21:3045–7View ArticleGoogle Scholar
  64. Qi YH, Wang N, Xu Q, Li HX, Zhou PS, Lu X, Zhao GQ (2015) A green route to fabricate MoS2 nanosheets in water-ethanol-CO2. Chem Commun 51:6726–9View ArticleGoogle Scholar
  65. Nguyen EP, Carey BJ, Daeneke T, Ou JZ, Latham K, Zhuiykov S, Kalantar-zadeh K (2015) Investigation of two-solvent grinding-assisted liquid phase exfoliation of layered MoS2. Chem Mater 27:53–9View ArticleGoogle Scholar
  66. Zhang WT, Wang YR, Zhang DH, Yu SX, Zhu WX, Wang J, Zheng FQ, Wang SX, Wang JL (2015) A one-step approach to the large-scale synthesis of functionalized MoS2 nanosheets by ionic liquid assisted grinding. Nanoscale 7:10210–7View ArticleGoogle Scholar
  67. Shen JF, He YM, Wu J, Gao CT, Keyshar K, Zhang X, Yang YC, Ye MG, Vajtai R, Lou J, Ajayan PM (2015) Liquid phase exfoliation of two-dimensional materials by directly probing and matching surface tension components. Nano Lett 15:5449–54View ArticleGoogle Scholar
  68. Qiao W, Yan SM, He XM, Song XY, Li ZW, Zhang X, Zhong W, Du YW (2014) Effects of ultrasonic cavitation intensity on the efficient liquid-exfoliation of MoS2 nanosheets. RSC Adv 4:50981–7View ArticleGoogle Scholar
  69. Eda G, Yamaguchi H, Voiry D, Fujita T, Chen MW, Chhowalla M (2011) Photoluminescence from chemically exfoliated MoS2. Nano Lett 11:5111–6View ArticleGoogle Scholar
  70. Lee C, Yan HG, Brus LE, Heinz TF, Hone J, Ryu S (2010) Anomalous lattice vibrations of single and few-layer MoS2. ACS Nano 4:2695–700View ArticleGoogle Scholar
  71. Wang KP, Wang J, Fan JT, Lotya M, O’Neill A, Fox D, Feng YT, Zhang XY, Jiang BX, Zhao QZ, Zhang HZ, Coleman JN, Zhang L, Blau WJ (2013) Ultrafast saturable absorption of two-dimensional MoS2 nanosheets. ACS Nano 7:9260–7View ArticleGoogle Scholar
  72. Hu LR, Ren YM, Yang HX, Xu Q (2014) Fabrication of 3D hierarchical MoS2/polyaniline and MoS2/C architectures for lithium-ion battery applications. ACS Appl Mater Interfaces 6:14644–52View ArticleGoogle Scholar
  73. Smith RJ, King PJ, Lotya M, Wirtz C, Khan U, De S, O’Neill A, Duesberg GS, Grunlan JC, Moriarty G, Chen J, Wang JZ, Minett AI, Nicolosi V, Coleman JN (2011) Large-scale exfoliation of inorganic layered compounds in aqueous surfactant solutions. Adv Mater 23:3944–8View ArticleGoogle Scholar
  74. Bari R, Parviz D, Khabaz F, Klaassen CD, Metzler SD, Hansen MJ, Khare R, Green MJ (2015) Liquid phase exfoliation and crumpling of inorganic. Phys Chem Chem Phys 17:9383–93View ArticleGoogle Scholar
  75. Zhang ZY, Li WY, Yuen MF, Ng TW, Tang YB, Lee CS, Chen XF, Zhang WJ (2015) Hierarchical composite structure of few-layers MoS2 nanosheets supported by vertical graphene on carbon cloth for high-performance hydrogen evolution reaction. Nano Energy 18:196–204View ArticleGoogle Scholar
  76. Kong DS, Wang HT, Cha JJ, Pasta M, Koski KJ, Yao J, Cui Y (2013) Synthesis of MoS2 and MoSe2 films with vertically aligned layers. Nano Lett 13:1341–7View ArticleGoogle Scholar
  77. Dou S, Wu JH, Tao L, Shen AL, Huo J, Wang SY (2016) Carbon-coated MoS2 nanosheets as highly efficient electrocatalysts for the hydrogen evolution reaction. Nanotechnology 27:45402–7View ArticleGoogle Scholar
  78. Chao J, Zou M, Zhang C, Sun HF, Pan D, Pei H, Su S, Yuwen LH, Fan CH, Wang LH (2015) A MoS2-based system for efficient immobilization of hemoglobin and biosensing applications. Nanotechnology 26:274005–13View ArticleGoogle Scholar


© The Author(s). 2016