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. 2016 Jan 27;6:19945. doi: 10.1038/srep19945

Atomic-layer soft plasma etching of MoS2

Shaoqing Xiao 1,a,*, Peng Xiao 1,*, Xuecheng Zhang 1, Dawei Yan 1, Xiaofeng Gu 1, Fang Qin 2, Zhenhua Ni 3,b, Zhao Jun Han 4, Kostya (Ken) Ostrikov 4,5,6,c
PMCID: PMC4728689  PMID: 26813335

Abstract

Transition from multi-layer to monolayer and sub-monolayer thickness leads to the many exotic properties and distinctive applications of two-dimensional (2D) MoS2. This transition requires atomic-layer-precision thinning of bulk MoS2 without damaging the remaining layers, which presently remains elusive. Here we report a soft, selective and high-throughput atomic-layer-precision etching of MoS2 in SF6 + N2 plasmas with low-energy (<0.4 eV) electrons and minimized ion-bombardment-related damage. Equal numbers of MoS2 layers are removed uniformly across domains with vastly different initial thickness, without affecting the underlying SiO2 substrate and the remaining MoS2 layers. The etching rates can be tuned to achieve complete MoS2 removal and any desired number of MoS2 layers including monolayer. Layer-dependent vibrational and photoluminescence spectra of the etched MoS2 are also demonstrated. This soft plasma etching technique is versatile, scalable, compatible with the semiconductor manufacturing processes, and may be applicable for a broader range of 2D materials and intended device applications.

The electronic, mechanical, optoelectronic and catalytic properties of two-dimensional (2D) transition metal dichalcogenides (TMDs) such as MoS2 critically depend on the number of atomic stacking layers1,2,3,4,5,6,7,8,9,10. MoS2 has attracted rapidly growing attention from both academia and industry owing to its atomic-layer-dependent properties. Indeed, the electronic bandgap of MoS2 increases and transits from indirect to direct as the number of stacking layers decreases from multiple layers to monolayer11,12,13. Phase transition from semiconducting 2H to metallic 1T phases may also occur when the thickness is reduced to monolayer14,15. As such, atomically-thin MoS2 is a promising material for applications in valleytronic and optoelectronic devices, such as photodetectors, photovoltaics, and light emitters11,16,17; while multilayer MoS2 is suited for electronic and energy storage devices owing to its tunable bandgaps and loosely bound 2D atomic layers18,19,20.

However, exfoliated or synthesized MoS2 films usually contain non-uniform domains with different number of layers21. Post-growth thinning by methods of thermal annealing, laser and plasma etching has been actively pursued, but with only limited success20,21,22,23. For instance, thermal annealing has been applied to thin few-layer MoS2 flakes; yet the process was very time- and energy-consuming22,23. The thinned MoS2 films also possibly formed MoO3 due to high-temperature oxidation23 and showed non-uniform thickness across the surface and shrank laterally due to the uneven thermal sublimation effect22. Laser heating was also demonstrated to reduce the MoS2 thickness through thermal sublimation induced by light absorption21. However, monolayer domains were only achieved with careful control of the uniformity and dose of the laser exposure, which is challenging for scale-up8,21. In addition, argon-based plasmas facilitated layer-by-layer MoS2 thinning20, but may leave unwanted residues on the etched surface due to energetic Ar+ ion bombardment. It is therefore highly desired to develop a MoS2 thinning process with time- and energy-efficiency, ease to control and scale-up, and non-destruction to the remaining layers and substrate.

Here we report a soft, selective, high-throughput and uniform large-area plasma etching of MoS2. Compared to conventional plasma processes where energetic ions cause unwanted damage during etching, the present approach is based on reactive plasmas where the ion impact is intentionally reduced by generating the majority of the electrons with the energies insufficient for the effective ion generation or causing damage to the remaining MoS2 layers. The reactive radicals generated in such plasmas uniformly remove equal numbers of MoS2 layers irrespective of the initial thickness, without affecting the underlying SiO2 substrate and the exposed MoS2 layers. The etching rates can be tuned to achieve complete MoS2 removal and any desired number of atomic MoS2 layers including monolayer, starting from the pristine MoS2 domains of virtually any thickness. Layer-dependent vibrational and photoluminescence spectra of the etched MoS2 are also demonstrated. The process is fast, reproducible, and compatible with the established semiconductor microfabrication technologies, thus holding great promise to enable next-generation TMD-based devices.

Results

In contrast to the traditional plasma etching processes, the soft plasma etching relies on SF6+N2 precursors dissociated in low-power, low-density radio-frequency plasma source (Supplementary Figure S1). Energetic ions can be minimized in such plasmas to significantly reduce structural damage to the 2D films. Specifically, the etching reactions used in this process are:

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The key features of this plasma-based process include: (i) strong oxidant NF3 from reaction (1) can simultaneously react with both Mo and S; (ii) by-products MoF4, MoF3, F2 and SF4 of reactions (1–3) are volatile and are removed without residues on the etched surface, although some of these by-products are not so environment-friendly; (iii) the precursors and reaction by-products have negligible etching effect on the SiO2/Si substrate so that a highly-selective etching between MoS2 and SiO2 can be achieved; (iv) the rates of the soft etching can be effectively controlled by the plasma power density to enable fine (~0.8 mW/cm3) and fast (~1.2 mW/cm3) etching modes where any pre-determined number of MoS2 layers can be removed; (v) same number of MoS2 layers is removed uniformly across the domains with very different original number of layers. The soft etching mode is effective below the critical value (~1.5 mW/cm3) of the input power density. Beyond this critical value, structural damages to MoS2 emerge, i.e., harsh etching mode. More details are provided below.

Figure 1a–c show the etching result of a 4-layer MoS2 flake at an input power of 0.8 mW cm−3. The number of layers of pristine MoS2 flake was determined by optical contrast and atomic force microscopy (AFM), by assuming 0.7 nm as the thickness of a single S-Mo-S layer. From these images, it is found that 2 layers (~1.4 nm) and 1 layer (~0.7 nm) of MoS2 were successfully removed in two consecutive steps of 4 and 3 min, respectively. For comparison, thermal annealing in vacuum required 1 hr to remove 1 layer of MoS222. Figure 1d–f show the etching result of a thick MoS2 flake starting with ~40 layers at an input power density of 1.2 mW cm−3. ~20 layers (~15 nm) of the MoS2 flake were removed in each step with the duration of 8 min, demonstrating the fast rate and high efficiency of this technique.

Figure 1. Plasma-etched MoS2 flakes at different input power densities.

Figure 1

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(a) Pristine MoS2 flake showing 1 and 3 layers; (b) MoS2-free (0L) and monolayer (1L) after 4 min fine plasma etching at 0.8 mW/cm3; and (c) MoS2-free surface after another 3 min fine etching at 0.8 mW/cm3. (d) Pristine MoS2 flake with ~40 layers; (e) ~20 layers after 8 min fast plasma etching at 1.2 mW/cm3; (f) MoS2-free surface after another 8 min fast etching at 1.2 mW/cm3. (g) The etched thickness as a function of time at 0.8 and 1.2 mW/cm3. (h) Large-area pristine MoS2 flake with ~90 layers; (i) MoS2 monolayer etched from the sample (h) using a combination of fast (first) and fine etching processes. All the scale bars in (a–i) are 10 μm.

Remarkably, the present plasma thinning method had negligible etching effect to the SiO2/Si substrate. In a control experiment, we have covered half area of the SiO2/Si substrate by a shadow mask and treated it under the same SF6+N2 plasma conditions at either 0.8 or 1.2 mW cm−3 for 2 hr. No obvious boundaries or steps between the treated and the covered areas could be found from both AFM and optical images (Supplementary Figure S2), suggesting that the SF6+N2 plasma chemistry is highly selective to MoS2. As the SiO2/Si substrate is generally used as a reference in the AFM measurements to calculate the number of MoS2 layers, this allowed us to precisely determine the etching rate at different input power densities.

Figure 1g plots the etched thickness as a function of etching time at the power densities of 0.8 and 1.2 mW/cm3. Interestingly, the etching rates were low in the first 2–3 min in both cases. This can be explained by considering that reaction (1) requires certain time for the plasma to dissociate the SF6 molecules and produce enough NF3 radicals to etch MoS2, particularly at the beginning of the plasma discharge. The etching rates became stable after 3 min, as demonstrated by the linear fitting curves in Fig. 1g. The etching rates were about 2.8 and 3.6 nm/min for the power densities of 0.8 and 1.2 mW/cm3, respectively. Therefore, the former is referred as the fine etching mode because the low etching rate is best suited for high-precision removal of MoS2 atomic layers. On the other hand, the latter case is referred to as the fast etching mode which has higher etching rates and is more efficient for etching thicker MoS2 films.

By combining the fine and fast etching modes, domains of the arbitrary number of layers of MoS2 can be uniformly thinned across the sample. As shown in Fig. 1h,i and S3, a pristine MoS2 flake with 90 layers (~63 nm) and a size of ~60 μm was firstly subjected to the fast etching mode at 1.2 mW/cm3 for 20 min. This led to a thinned MoS2 flake with only 3 layers (~2.4 nm). Then, the MoS2 flake was further etched under the fine mode for another 4 min, resulting in the formation of monolayer MoS2. The height of the MoS2 monolayer (~1.0 nm) was slightly larger compared to the monolayer MoS2 obtained by mechanical exfoliation24, which can be attributed to surface corrugation or the presence of adsorbed or trapped molecules13.

Importantly, the surface roughness of etched samples remained unchanged as compared to the pristine samples (Supplementary Figure S3), suggesting that the plasma etching process is indeed soft with the minimum damage induced. The layers that were left underneath after the etching were homogeneous. This is in stark contrast to the laser thinning method where ~3 times larger surface roughness was observed, possibly due to the different reaction rates of S and Mo atoms and/or the unremoved MoS2 traces on the surface21. The smooth surface obtained in the present soft plasma etching processes can be largely attributed to the NF3 radicals which etch both Mo and S uniformly to form volatile by-products. In addition, the domain sizes of the MoS2 flakes were not noticeably affected throughout the whole process, as compared to the conventional thermal or laser-based methods which significantly reduce the surface area of MoS2 domains21,22.

Our plasma etching technique can also realize layer-by-layer thinning of MoS2 films with the domains of different number of layers. This aspect is particularly important because of the uneven thickness and patchy domains of the commonly produced MoS2 films. Figure 2a shows a representative etched sample consisting of sub-monolayer (SM), single, bi-, tri-, and multilayers, where the number of layers at distinct regions can be easily identified by both AFM and optical measurements (Fig. 2a–c). Notably, *SiO2 in the figure represents the exposed SiO2 surface after the complete removal of top MoS2 layers. It was also found that no residues were left for any layers with above 3 layers. However, for the incomplete removal of monolayer MoS2 that resulted in the SM area, a large number of MoS2 residues were identified (Fig. 2b). Scattered MoS2 residues were also found on 1-layer (1L) and 2-layer (2L) areas from Fig. 2b, although these residues were far less than that on the SM area. These observations suggested that the substrate had an impact in the etching process, particularly when the number of MoS2 layers is less than 3 layers. This substrate effect may be caused by the interactions between long-range van der Waals (vdW) and short-range polar and molecular forces25,26, which becomes negligible when the number of layers is large. Figure 2d shows the sample further subjected to a fine etching mode for another 7 min. Seven atomic layers were removed uniformly from the domains with more than 7 layers prior to etching, while only smooth SiO2 on the surface were found for domains with less than 7 layers. These results corroborate the large-area, uniform etching of MoS2 films using the soft plasma technique.

Figure 2.

Figure 2

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(a) The optical image of a representative etched sample consisting of flakes with the different number of layers including 1, 2, 3, 8, 19, 22, and 71 layers. SM denotes the MoS2 residues due to imcomplete removal of monolayer. (b) AFM image of the area squared in (a). (c) AFM depth profiles showing 1, 2 and 3 layers of MoS2 as marked by blue lines in (b). (d) The optical image of the same sample after another 7 min fine etching showing that 7 MoS2 layers have been removed uniformly from all domains starting with more than 7 layers.

It should be noted that a height difference was observed between the bottom *SiO2 (0 layer areas) and the surrounding SiO2 (labeled as SiO2 in both optical and AFM images) in Figs 1b,c and 2a,d. This is because the pristine samples used for soft etching had been subjected to SF6+N2+H2 plasma treatment in the beginning at an input power density of 4 mW/cm3 for 20 min. Adding H2 into the plasma can effectively promote the etching of SiO2 and cleaning of substrate. About 20 nm SiO2 was etched after this step while no etching of MoS2 was found. The optical images of MoS2 sample before and after SF6+N2+H2 plasma treatment are shown in Figure S4. This observation demonstrated the easy control over selective etching between SiO2 and MoS2 by simply changing the plasma etchant gases. Details are out of scope of the present work but will be a subject of future studies.

The etched MoS2 is further characterized by Raman spectroscopy, which is a sensitive technique to determine the number of layers in ultrathin MoS2 flakes24,27,28,29. According to previous studies24,28, the peak positions of in-plane vibrational Inline graphic mode and out-of-plane vibrational A1g mode vary monotonously with the number of MoS2 layers. Specifically, when the number of layers is decreased, A1g shifts to lower frequencies due to weaker van der Waals forces which mostly affect the out-of-plane vibrations, while Inline graphic shifts to higher frequencies owing to the decreased dielectric screening of the long-range Coulombic interactions22,30,31. Figure 3a compares the Raman spectra obtained from different regions of an etched MoS2 sample (displayed in Fig. 2a), including SM area and numbers of 1, 2, 3, 8, 19, 22 and 71 layers. It is found that the A1g peak shifted slightly to lower frequencies as the number of layers decreased, especially in the 1–8 layers range, while the Inline graphic peak shifted up to higher frequencies. These Raman shifts are consistent with the predicted characteristics of thinned MoS2 layers.

Figure 3.

Figure 3

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(a) Raman spectra of the etched MoS2 flakes with different thickness and MoS2 sub-monolayer. (b) The difference in Raman shifts between the Inline graphic and A1g peaks plotted as a function of the number of MoS2 layers. MoS2 layers thinned by the laser and thermal methods21,22 are also included for comparison. (c) PL spectra of the etched MoS2 flakes with different thickness and MoS2 sub-monolayer. (d) The wavelength and intensity of the prominent PL peak plotted as a function of the number of MoS2 layers.

Quantitatively, we also calculated the frequency difference between Inline graphic and A1g in the plasma etched samples, as shown in Fig. 3b. The frequency difference decreased gradually from about 25 cm−1 for bulk film to 21.7 cm−1 for monolayer MoS2. This frequency shift is similar to the results obtained by other post-growth thinning methods, but the frequency difference value of the plasma-thinned monolayer or bilayer is larger than that of the pristine MoS2 produced by mechanical exfoliation20,22,24,28. Like other post-growth thinning methods such as laser thinning or chemical methods13,21, this discrepancy can be attributed to the presence of a small number of traces of MoS2 residues on the surface of the plasma-thinned monolayer or bilayer, as demonstrated in Fig. 2b. While this made the present etching method slightly inferior to Ar+ plasma method20 in thinning monolayer or bilayer, it is more efficient and credible in thinning thick layers. Interestingly, the frequency difference of SM area showed a further decrease as compared to that of monolayer MoS2, possibly due to the quantum confinement effect arising from the reduced lateral size of MoS2 residues.

In addition to the Raman vibrational fingerprints, ultrathin MoS2 layers also exhibit unique signatures in their PL spectra. Figure 3c shows the PL spectra of MoS2 with 1, 2, 3, 8, 19, 22 and 71 layers, as well as SM area. Two peaks located at ~670 and ~615 nm were identified in ultrathin layers (<8 layers), corresponding to the excitonic transitions between the minimum of the conduction band and the maxima of the two splitted valence bands, i.e., the A1 and B1 excitons in MoS211,16. In particular, the PL intensity increased gradually along with the decrease of the number of MoS2 layers, in a good agreement with previous reports11,16. Figure 3d shows the variations of peak position and intensity of the dominant PL peak as a function of the atomic layer numbers. As seen, the peak showed a blueshift from 673 to 666 nm as MoS2 was thinned to monolayer, suggesting the increased bandgap energy. The monolayer produced the highest PL intensity, which can be ascribed to the indirect to direct bandgap transition8,16. Interestingly, the SM area also exhibited a broad PL peak at ~660 nm with slightly reduced intensity as compared to that of monolayer MoS220. Such observation may be attributed to the additional quantum confinement effect arising from the reduced lateral size and/or the distorted S-Mo-S sandwich structure in MoS2 residues.

It was noted that our soft plasma etching regime of MoS2 films was controlled by the input power density of the radio-frequency ICP source. The etching becomes harsh at a critical value of about 1.5 mW/cm3. Below this critical input power density, the MoS2 thinning process is dominated by radical reactions based on the SF6+N2 plasma chemistry. While at higher power densities, more high-energy electrons are generated, which enhances ion production and leads to uncontrollable damage to the samples through ion impact. In particular, at the input power density of 2 mW/cm3 the roughness of etched MoS2 samples increased significantly, with craters and pinholes clearly seen on the surface (Supplementary Figure S5).

To further explore the effect of the plasma electrons on the specific etching mode, we measured the electron energy distribution function (EEDF) using a Langmuir probe. The measurements were performed in a wide range of bias voltage, providing the I-V characteristic. The EEDF is generally defined as the second-order derivative of the measured I-V curve and can be expressed by the following equation32,33:

graphic file with name srep19945-m8.jpg

where A is the surface collection area of the Langmuir probe, e is the electron charge, and me is electron mass. The electron density ne and electron temperature Te can be derived from the measured EEDF by assuming a Maxwellian distribution32,33:

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Figure 4a shows the experimental EEDF curves at the three input power densities of 0.8, 1.2 and 2 mW/cm3, corresponding to the fine and fast regimes of the soft etching mode, and the harsh etching mode, respectively. Figure 4b shows the values of ne and Te calculated based on Equations (5) and (6) respectively. It can be clearly seen that as long as the input power density was lower than the critical value of 1.5 mW/cm3, the electron temperature and density were below 0.4 eV and ~108 cm−3, respectively. These values were much lower compared to the conventional plasmas generated in the capacitively or inductively coupled configurations. As such, the fraction of electrons causing precursor ionization and dissociation was lower, so was the probability of ion-induced damage of underlying MoS2 layers. Furthermore, negligible high-energy electron tail (>2 eV) was observed in the EEDF, suggesting that electron-impact ionization and dissociation of the reactive radicals was not effective. Consequently, the effects of chemical reactions dominated over the ion bombardment in the MoS2 thinning process.

Figure 4.

Figure 4

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(a) The electron energy distribution function (EEDF) of the E-mode SF6+N2 discharges at three typical input power densities; (b) the corresponding calculated values of electron density (ne) and electron temperature (Te).

When the power density exceeded the critical value, the energy and density of electrons and ions increased significantly which may start to cause structural damage to the sample. The presence of higher-energy electrons (>2.0 eV) may also disrupt the S-Mo-S structure as the energy required to create vacancies in MoS2 is as low as 2.12 eV34. Another adverse effect is heat-induced evaporation, which may lead to surface defects at random positions. Nevertheless, as long as the input power density is lower than the critical value, the surface of multilayer MoS2 obtained by the soft plasma etching remains very smooth and the number of removed atomic layers is uniform across the whole sample surface. Furthermore, some encouraging results have been obtained on the atomic-layer soft etching of MoSe2 thin films (Figure S6), suggesting that this technique is also applicable to other TMDs. The comparative advantages of the present soft plasma etching techniques over other existing techniques are also summarized in Supplementary Table S1.

In summary, we have demonstrated a versatile and effective plasma technique for the soft, selective, and uniform layer-by-layer etching of MoS2 using SF6 + N2 precursors. Using the plasma power densities below the critical value of ~1.5 mW/cm3, equal number of MoS2 atomic layers can be removed from all the MoS2 areas irrespective of their original thickness. Large-area MoS2 flakes with arbitrary number of layers can be effectively thinned by combining the fine and fast etching modes switched-over by the power density of the plasma discharge. The plasma chemistry is highly-selective to MoS2 with negligible etching of the SiO2/Si substrate. The surface of etched MoS2 samples remained homogeneous and smooth with no shrinkage in the original domain sizes. The present approach is generic and may be used in the development of plasma-based etching processes of other TMDs pursued for applications in next-generation electronic, optoelectronic and other integrated devices and systems. It could also be promising for the catalytic applications of MoS2 since plasma treatment is one of the important techniques for generating active sites in MoS2 layers35. Furthermore, our results may contribute to the development of soft plasma etching processes for large-scale semiconductor microfabrication technologies.

Methods

MoS2 preparation and plasma thinning

Thick MoS2 layers were fabricated by mechanical exfoliation from bulk single-crystal MoS2 and deposited onto a Si/SiO2 (300 nm) substrate. These multilayers were characterized by a combination of optical microscopy, atomic force microscopy (AFM) and Raman spectroscopy. A planar low-frequency (0.5 MHz) inductively-coupled plasma (ICP) source was applied to etch the MoS2 multilayers without any external heating. The plasma was excited in the E-mode of ICP with the precursor gases of N2 and SF6 fed at the flow rates of 1.0 and 4.5 sccm, respectively. The E-mode discharge can be stably maintained at very low input power densities so that the ion density was too low to induce destructive ion bombardment onto the processed samples36. Whether the plasma etching is soft or harsh depended strongly on the input power density, with a critical value of ~1.5 mW/cm3. Therefore, we adopted two low input power densities at 0.8 and 1.2 mW/cm3 for the fine and fast etching processes, respectively. The schematics of experimental setup of the E-mode ICP source is presented in Figure S1.

Characterization

The optical contrast images were obtained using a Leica 4200 Optical Microscopy. The Raman and photoluminescence (PL) spectra were recorded using a LabRAM HR Evolution Raman system with 532 nm laser excitation. The laser power at the sample was lower than 0.5 mW to avoid any laser-induced heating. To obtain the Raman images, an X-Y stage was used to move the sample with a 200 nm step, and the corresponding Raman spectrum was recorded at every point. AFM is carried out using a Bruker Dimension ICON system in the tapping mode.

Additional Information

How to cite this article: Xiao, S. et al. Atomic-layer soft plasma etching of MoS2. Sci. Rep. 6, 19945; doi: 10.1038/srep19945 (2016).

Supplementary Material

Supplementary Information
srep19945-s1.pdf (1.1MB, pdf)

Acknowledgments

This work is partially supported by the National Nature Science Foundation under Grants 61404061, 61422503 and 51302028, the Natural Science Foundation of Jiangsu Province, China under Grants BK20140168 and BK2012110, the Joint Innovation Project of Jiangsu Province under Grants BY2014023-19 and BY2013015-19, the Fundamental Research Funds for the Central Universities of China under Grants JUSRP51323B and JUSRP11460, the 111 Project under Grant B12018, Australian Research Council (DE130101264, FT100100303) and CSIRO’s Science Leadership Program.

Footnotes

Author Contributions P.X. and S.X. initiated the research and worked on plasma treatment, Raman and photoluminescence measurements and analysis of MoS2 properties. X.Z. and D.Y. performed optical microscopy measurements. F.Q. performed AFM measurements. X.G., Z.N. and K.O. advised on planning and executing the research. All authors discussed the results. S.X., Z.J.H. and K.O. wrote the manuscript.

References

  1. Berkdemir A., Cutierrez H. R., Betello-Mendez A. R., Perea-Lopez N., Elias A. L., Chia C. I., Wang B., Crespi V. H., Lopez-Urias F. & Charlier J. C. Identification of Individual and Few Layers of WS2 Using Raman Spectroscopy. Scientific Reports 3, 1755 (2013). [Google Scholar]
  2. McCreary K. M., Hanbicki A. T., Robinson J. T., Cobas E., Culbertson J. C., Friedman A. L., Jernigan G. G. & Jonker B. T. Large-Area Synthesis of Continuous and Uniform MoS2 Monolayer Films on Graphene. Advanced Functional Materials 24, 6449–6454 (2014). [Google Scholar]
  3. Huang J. K., Pu J., Hsu C. L., Chiu M. H., Juang Z. Y., Chang Y. H., Chang W. H., Iwasa Y., Takenobu T. & Li L. J. Large-Area Synthesis of Highly Crystalline WSe2 Mono layers and Device Applications. Acs Nano 8, 923–930 (2014). [DOI] [PubMed] [Google Scholar]
  4. Xu M. S., Liang T., Shi M. M. & Chen H. Z. Graphene-Like Two-Dimensional Materials. Chemical Reviews 113, 3766–3798 (2013). [DOI] [PubMed] [Google Scholar]
  5. Lee Y. H., Yu L. L., Wang H., Fang W. J., Ling X., Shi Y. M., Lin C. T., Huang J. K., Chang M. T., Chang C. S., Dresselhaus M., Palacios T., Li L. J. & Kong J. Synthesis and Transfer of Single-Layer Transition Metal Disulfides on Diverse Surfaces. Nano Letters 13, 1852–1857 (2013). [DOI] [PubMed] [Google Scholar]
  6. Huang X., Zeng Z. Y. & Zhang H. Metal Dichalcogenide Nanosheets: Preparation, Properties and Applications. Chemical Society Revviews 42, 1934–1946 (2013). [DOI] [PubMed] [Google Scholar]
  7. Chhowalla M., Shin H. S., Eda G., Li L. J., Loh K. P. & Zhang H. The Chemistry of Two-dimensional Layered Transition Metal Dichalcogenide Nanosheets. Nature Chemistry 5, 263–275 (2013). [DOI] [PubMed] [Google Scholar]
  8. Wang Q. H., Kalantar-Zadeh K., Kis A., Coleman J. N. & Strano M. S. Electronics and Optoelectronics of Two-dimensional Transition Metal Dichalcogenides. Nature Nanotechnology 7, 699–712 (2012). [DOI] [PubMed] [Google Scholar]
  9. Lee Y. H., Zhang X. Q., Zhang W. J., Chang M. T., Lin C. T., Chang K. D., Yu Y. C., Wang J. T. W., Chang C. S., Li L. J. & Lin T. W. Synthesis of Large-Area MoS2 Atomic Layers with Chemical Vapor Deposition. Advanced Materials 24, 2320–2325 (2012). [DOI] [PubMed] [Google Scholar]
  10. Shi Y. M., Huang J. K., Jin L. M., Hsu Y. T., Yu S. F., Li L. J. & Yang H. Y. Selective Decoration of Au Nanoparticles on Monolayer MoS2 Single Crystals. Scientific Reports 3, 1839 (2013). [DOI] [PMC free article] [PubMed] [Google Scholar]
  11. Mak K. F., Lee C., Hone J., Shan J. & Heinz T. F. Atomically Thin MoS2: A New Direct-Gap Semiconductor. Physcal Review Letters 105, 136805 (2010). [DOI] [PubMed] [Google Scholar]
  12. Kuc A., Zibouche N. & Heine T. Influence of Quantum Confinement on the Electronic Structure of the Transition Metal Sulfide TS2. Physical Review B. 83, 245213 (2011). [Google Scholar]
  13. Eda G., Yamaguchi H., Voiry D., Fujita T., Chen M. W. & Chhowalla M. Photoluminescence from Chemically Exfoliated MoS2. Nano Letters 11, 5111–5116 (2011). [DOI] [PubMed] [Google Scholar]
  14. Lin Y. C., Dumcencon D. O., Huang Y. S. & Suenaga K. Atomic Mechanism of the Semiconducting-to-Metallic Phase Transition in Single-layered MoS2. Nature Nanotechnology 9, 391–396 (2014). [DOI] [PubMed] [Google Scholar]
  15. Yamaguchi H., Blancon J. C., Kappera R., Lei S. D., Najmaei S., Mangum B. D., Gupta G., Ajayan P. M., Lou J., Chhawalla M., Crochet J. J. & Mohite A. D. Spatially Resolved Photoexcited Charge-Carrier Dynamics in Phase-Engineered Mono Layer MoS2. Acs Nano 9, 840–849 (2015). [DOI] [PubMed] [Google Scholar]
  16. Splendiani A., Sun L., Zhang Y. B., Li T. S., Kim J., Chim C. Y., Galli G. & Wang F. Emerging Photoluminescence in Monolayer MoS2. Nano Letters 10, 1271–1275 (2010). [DOI] [PubMed] [Google Scholar]
  17. Tonndorf P., Schmidt R., Bottger P., Zhang X., Borner J., Liebig A., Albrecht M., Kloc C., Gordan O., Zahn D. R. T., de Vasconcellos S. M. & Bratschitsch R. Photoluminescence Emission and Raman Response of Monolayer MoS2, MoSe2, and WSe2. Optics Express 21, 4908–4916 (2013). [DOI] [PubMed] [Google Scholar]
  18. Kibsgaard J., Chen Z. B., Reinecke B. N. & Jaramillo T. F. Engineering the Surface Structure of MoS2 to Preferentially Expose Active Edge Sites for Electrocatalysis. Nature Materials 11, 963–969 (2012). [DOI] [PubMed] [Google Scholar]
  19. Xu X., Liu W., Kim Y. & Cho J. Nanostructured Transition Metal Sulfides for Lithium Ion Batteries: Progress and Challenges. Nano Today 9, 604–630 (2014). [Google Scholar]
  20. Liu Y. L., Nan H. Y., Wu X., Pan W., Wang W. H., Bai J., Zhao W. W., Sun L. T., Wang X. R. & Ni Z. H. Layer-by-Layer Thinning of MoS2 by Plasma. Acs Nano 7, 4202–4209 (2013). [DOI] [PubMed] [Google Scholar]
  21. Castellanos-Gomez A., Barkelid M., Goossens A. M., Calado V. E., van der Zant H. S. J. & Steele G. A. Laser-Thinning of MoS2: On Demand Generation of a Single-Layer Semiconductor. Nano Letters 12, 3187–3192 (2012). [DOI] [PubMed] [Google Scholar]
  22. Lu X., Utama M. I. B., Zhang J., Zhao Y. Y. & Xiong Q. H. Layer-by-layer Thinning of MoS2 by Thermal Annealing. Nanoscale 5, 8904–8908 (2013). [DOI] [PubMed] [Google Scholar]
  23. Wu J., Li H., Yin Z. Y., Li H., Liu J. Q., Cao X. H., Zhang Q. & Zhang H. Layer Thinning and Etching of Mechanically Exfoliated MoS2 Nanosheets by Thermal Annealing in Air. Small 9, 3314–3319 (2013). [DOI] [PubMed] [Google Scholar]
  24. Zhang L. L., Liang G., Peng G., Zou F., Huang Y. H., Croft M. C. & Ignatov A. Significantly Improved Electrochemical Performance in Li3V2(PO4)(3)/C Promoted by SiO2 Coating for Lithium-Ion Batteries. Journal of Physical Chemistry C 116, 12401–12408 (2012). [Google Scholar]
  25. Seemann R., Herminghaus S. & Jacobs K. Dewetting Patterns and Molecular Forces: A Reconciliation. Physical Review Letters 86, 5534–5537 (2001). [DOI] [PubMed] [Google Scholar]
  26. Han Z. J. & Tay B. K. Dewetting of polymer films by ion implantation. European Physical Journal E 28, 273–278 (2009). [DOI] [PubMed] [Google Scholar]
  27. Li S. L., Miyazaki H., Song H., Kuramochi H., Nakaharai S. & Tsukagoshi K. Quantitative Raman Spectrum and Reliable Thickness Identification for Atomic Layers on Insulating Substrates. Acs Nano 6, 7381–7388 (2012). [DOI] [PubMed] [Google Scholar]
  28. Lee C., Yan H., Brus L. E., Heinz T. F., Hone J. & Ryu S. Anomalous Lattice Vibrations of Single- and Few-Layer MoS2. Acs Nano 4, 2695–2700 (2010). [DOI] [PubMed] [Google Scholar]
  29. Ferrari A. C., Meyer J. C., Scardaci V., Casiraghi C., Lazzeri M., Mauri F., Piscanec S., Jiang D., Novoselov K. S., Roth S. & Geim A. K. Raman Spectrum of Graphene and Graphene Layers. Physical Review Letters 97, 187401 (2006). [DOI] [PubMed] [Google Scholar]
  30. Molina-Sanchez A. & Wirtz L. Phonons in Single-layer and Few-layer MoS2 and WS2. Physical Review B 84, 155413 (2011). [Google Scholar]
  31. Li H., Zhang Q., Yap C. C. R., Tay B. K., Edwin T. H. T. & Olivier A. & Baillargeat D. From Bulk to Monolayer MoS2: Evolution of Raman Scattering. Advanced Functional Materials 22, 1385–1390 (2012). [Google Scholar]
  32. Godyak V. A., Piejak R. B., Alexandrovich B. M. & Kolobov V. I. Hot Plasma and Nonlinear Effects in Inductive Discharges. Physics of Plasmas 6, 1804–1812 (1999). [Google Scholar]
  33. Lieberman M. A. & Lichtenberg A. J. Principles of Plasma Discharges and Materials Processing. 2nd ed., Wiley-Interscience: Hoboken, N.J., 2005.
  34. Hong J. H., Hu Z. X., Probert M., Li K., Lv D. H., Yang X. N., Gu L., Mao N. N., Feng Q. L., Xie L. M., Zhang J., Wu D. Z., Zhang Z. Y., Jin C. H., Ji W., Zhang X. X., Yuan J. & Zhang Z. Exploring Atomic Defects in Molybdenum Disulphide Monolayers. Nature Communications 6, 6293 (2015). [DOI] [PMC free article] [PubMed] [Google Scholar]
  35. Li H., Tsai C., Koh A. L., Cai L., Contryman A. W., Fragapane A. H., Zhao J., Han H. S., Manoharan H. C., Abild-Pedersen F., Norskov J. K. & Zheng X. Activating and Optimizing MoS2 Basal Planes for Hydrogen Evolution Through the Formation of Strained Sulphur Vacancies. Nature Materials 10.1038/nmat4465 (2015). [DOI] [PubMed] [Google Scholar]
  36. Xiao S. Q., Xu S. & Ostrikov K. Low-temperature Plasma Processing for Si Photovoltaics. Materials Science & Engineering R-Reports 78, 1–29 (2014). [Google Scholar]

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