A microscopic understanding of the growth mechanism of two-dimensional materials is of particular importance for controllable synthesis of functional nanostructures. Because of the lack of direct and insightful observations, how to control the orientation and the size of two-dimensional material grains is still under debate. Here we discern distinct formation stages for MoS2 flakes from the thermolysis of ammonium thiomolybdates using in situ transmission electron microscopy. In the initial stage (400 °C), vertically aligned MoS2 structures grow in a layer-by-layer mode. With the increasing temperature of up to 780 °C, the orientation of MoS2 structures becomes horizontal. When the growth temperature reaches 850 °C, the crystalline size of MoS2 increases by merging adjacent flakes. Our study shows direct observations of MoS2 growth as the temperature evolves, and sheds light on the controllable orientation and grain size of two-dimensional materials.
Two-dimensional (2D)-layered MoS2 has shown great potential for various applications, including electronics1,2,3,4,5, optoelectronics6,7,8,9, photonics10,11,12, sensors13,14,15,16, catalysis17,18,19,20,21, biomedicine22 and energy storage23,24,25. Interestingly, the terrace and the edge sites of MoS2 exhibit specific physical and chemical properties26,27. Horizontal MoS2 flakes with the basal plane exposed, possessing lots of terrace sites and few dangling bonds, have been demonstrated for field-effect transistors and photoelectric devices4,7. In contrast, vertically aligned MoS2 structures with high-density edge sites, which are abundant with d-orbital electrons that facilitate the bonding with other elements, have been used for hydrogen evolution reaction, oxygen evolution reaction and gas adsorption20,21. It is a crucial issue to control the orientation of MoS2 in the horizontal or vertical direction on substrates for different applications. Chemical vapour deposition (CVD) is regarded as a deterministic method for controllable fabrication of 2D materials28,29,30,31 by which both the vertical and the horizontal MoS2 structures have been fabricated32,33, and there was also effort in revealing the underlying growth mechanism of MoS2 (ref. 34). Compared with sulfurization of Mo, MoO3 and MoCl5, the growth of MoS2 by the thermolysis of ammonium thiomolybdates ((NH4)2MoS4) has the advantages of single-precursor source, large growth window and the potential for mass production35. However, it still remains unclear how to control the orientation (vertical or horizontal) and grain size of MoS2 flakes by the thermolysis of (NH4)2MoS4.
Technical advances in transmission electron microscopy (TEM) with high spatial and temporal resolution allow us to monitor the real-time growth processes at an atomic scale and to understand the growth mechanism of low-dimensional materials36,37. Significant progresses have been made in figuring out the mechanisms behind sophisticated physicochemical processes using dedicated TEMs, such as the CaCO3 nucleation38, Pt3Fe nanoparticles’ attachment39 and Y2BaCuO5 nanowire growth40. TEM observations of the growth of 2D materials remains rather limited because of the critical challenges on obtaining high-resolution images at high temperature while maintaining the 2D materials’ growth in steps.
In this work, we use a heating stage with a Si3N4 membrane inside TEM to in situ observe the thermolysis of (NH4)2MoS4 and the subsequent crystallization behaviour of MoS2. We show that vertically aligned MoS2 flakes can be grown by a rapid temperature ramp, and further transit into horizontally aligned MoS2 flakes with the increasing temperature, which can be understood as a result of the minimization of the system energy, in good agreement with our theoretical calculations. The grain size of MoS2 flakes can be enlarged through oriented attachment and Ostwald ripening mechanisms by further increasing growth temperature or providing more precursors.
Selected-area electron diffraction evolved with temperature
To dynamically monitor the thermolysis of (NH4)2MoS4 and the crystallization process of MoS2 inside TEM (see Fig. 1a and Supplementary Fig. 1, the experimental design for this work), we first carried out electron diffraction analysis across a wide temperature range, from room temperature to 900 °C. Figure 1b–e shows the evolution of selected-area electron diffraction (SAED) patterns with the increasing temperature. From room temperature to 400 °C, no diffraction pattern is exhibited (Fig. 1b), indicating that the precursor is kept at its amorphous state. When the temperature reaches 400 °C, blurred diffraction rings emerge (Fig. 1c). The SAED patterns in Fig. 1c can be well indexed to a MoS2 structure with the space group of P63/mmc (JCPDS card No. 77-1716), implying that crystallization is initialized from this stage. Supplementary Fig. 2 shows the energy-dispersive X-ray spectra (EDS) acquired at room temperature and 400 °C. The increased atomic ratio of Mo/S from 1/4 (at room temperature) to 1/2 (at 400 °C) further confirms the decomposition of (NH4)2MoS4 into MoS2 at 400 °C. It has been reported that the thermolysis of (NH4)2MoS4 in an N2 environment resulted in the production of MoS2 via the following equations35,41:
The simultaneous thermogravimetric and differential scanning calorimetry (TGA/DSC) analysis of (NH4)2MoS4 precursor under flowing N2 (Supplementary Fig. 3) also verifies the foregoing chemical reactions. The different MoS2 formation temperatures in TEM and TGA/DSC (400 °C in TEM, while above 800 °C in TGA/DSC) can be ascribed to the different heating atmospheres. The temperature for forming MoS2 in high vacuum (TEM chamber) is relatively lower than that in a protective gas flow (in TGA/DSC).
With the increasing temperature, the diffraction rings became sharper, brighter and more discrete (also refer to Supplementary Fig. 4), suggesting the improvement of crystallinity and the increase in the crystal size. While the temperature reaches up to 900 °C, the continuous diffraction ring becomes blurred and a lot of bright spots appear (Fig. 1e). The emerging diffraction spots belong to metallic Mo (JCPDS card No. 89-5156), which is very likely to be resulted from the decomposition of MoS2 at high temperature (MoS2→Mo+2S↑). On the basis of these observations, we can propose that the crystallization of MoS2 occurs at 400–900 °C in vacuum, and the MoS2 crystals grow rapidly in size after 800 °C. The subsequent analysis is to sequentially capture systematical high-resolution TEM (HRTEM) micrographs as a function of increasing temperatures in this range.
Layer-by-layer growth of vertical MoS2 structures
At 400 °C, the sample is found to be slightly crystallized into loosely packed small clusters (1–3 nm) from the original amorphous precursor. Figures 2 and 3a show that the (002) edge sites of MoS2 are exposed, implying that the MoS2 slabs adopt a vertical growth and stand upright on the Si3N4 support at this stage. The interlayer distance of MoS2 slabs is ∼0.6 nm, similar to the value in bulk counterpart. Although the surface energy of the MoS2 edge sites is larger than that of the terrace sites by 2 orders of magnitude42, our result is in accordance with the previous ex situ rapid growth of MoS2 by the sulfurization of Mo layers, in which the MoS2 structure also adopts a vertical orientation in certain circumstances32,33.
We further captured a movie (Supplementary Movie 1) to vividly describe the dynamics of the vertical growth of MoS2 layers at 400 °C, and the snapshot frames are presented as Fig. 2a–d, exhibiting a layer-by-layer vertical growth. Figure 2a shows a four-layered vertical MoS2 slab surrounded by the amorphous precursor. With the continuous heating, the monomers are attached on the existing MoS2 cluster, and subsequently grow new slab to match the size of the existing ones. It is noteworthy that the growth of new layers is initialized from the step edges of the previous ones because step edges are more energetically active (see Fig. 2b,d). This finding is partially matched to the earlier observations by Helveg et al.34, in which new MoS2 slab started growth on old ones from either the middle part or the edge part. In addition, our results also suggest that the MoS2 cluster shows negligible in-plane growth throughout our observations, as shown in Fig. 2a–d, because the formation of new layers is more energetically favourable than the elongation of the existing layers. The whole process is schematically illustrated in Fig. 2e.
As shown in Fig. 3a–e, it is remarkable that the exposed MoS2 (002) planes gradually disappear instead of getting larger as the growth temperature continuously increases. The insets in Fig. 3a,c,e present the corresponding fast Fourier transform patterns, showing a continuous decrease in the brightness of the (002) halo ring; in contrast, the brightness of the (100) halo ring greatly increases (also see Fig. 3f for the statistical counts of vertical MoS2 structures throughout Fig. 3a–e). This implies that the preferred orientation of MoS2 on Si3N4 is changed from the vertical direction towards the horizontal one, namely, exposing their terrace sites instead of edge sites. The orientation of the MoS2 slabs with respect to the electron beam has a determinative impact on the TEM contrast. The substantial image contrast of MoS2 (002) basal plane can only be retained while it is ±9° within the electron beam direction; larger tilted angle weakens the contrast and the slabs become unrecognizable from the support substrates34,43,44. Therefore, it is reasonable to infer that a grain rotation process happens at this stage (see also Supplementary Fig. 5). The MoS2 clusters rotated from vertical to horizontal on the substrate during the heating between 400 and 780 °C, as depicted in Fig. 3h. We repeatedly grew MoS2 at 780 °C and found that the as-grown polycrystalline MoS2 flakes are horizontally orientated, in good agreement with previous CVD growth results from either gas-phase or solid-phase precursors at similar temperatures30,45.
The initial formation of vertically aligned MoS2 structures and its subsequent rotation to horizontal structure are very likely to be driven by reducing total system energy and eliminating crystal defects. To investigate the evolution of total system energy during the transition, we performed the first-principles calculations concerning the surface energy and the interfacial energy between MoS2 and Si3N4 substrates, which are two major factors contributing to the total system energy. First, the surface energy during the transition from vertical structure (corresponding to the surface with the Miller index (100)) to horizontal structure (corresponding to the (001) surface is calculated). Our calculation results show that the (001) surface has much lower surface energy (0.0277, eV Å−2) than (100) surface in the rational chemical potential region. The sulfur-terminated structure (that is, (100)-S2) with the surface energy of 0.1794, eV Å−2 is found to be the most stable termination in the surfaces with the (100) Miller index. Second, the interfacial energy between MoS2 and Si3N4 substrates are different for vertical and horizontal MoS2 structures because the dangling bonds are present in the (100) surface but absent in the (001) surface. The interfacial energies for vertical and horizontal structures are −0.1173 and −0.0046, eV Å−2, respectively. Clearly, the interfacial energy for vertical MoS2 structure is much smaller than the horizontal structure.
Generally, the interfacial energy reduces the system energy, while the surface energy raises it. As shown above, the surface energy of vertical MoS2 structure is larger than that of horizontal structure; however, the interfacial energy is much smaller. Therefore, the competition between surface energy and interfacial energy of MoS2 structures determines the preferred growth orientation. To illustrate this mechanism, we evaluate the energies of MoS2 structures in different orientations as a function of the volumes. Since the height of the structure is limited in the growth of vertical MoS2, the energy is minimized with a constraint, in which the height of particle is less than 15 Å. The corresponding energy density, the optimal length, width and height of different surface orientations as a function of volumes are summarized in Fig. 3g and Supplementary Fig. 6 (see also Supplementary Note 1). We can find that the vertically aligned MoS2 prefers to adopt a box with large length and height but small width, whereas the horizontally aligned MoS2 tends to lateral growth, in which the length, which is equal to width, is much larger than height. As shown in Fig. 3g, at the beginning of crystallization, the size is small, and hence the vertical structure has lower energy than the horizontal one. The energy difference increases with volumes and the height of vertical structure also increases. Since the height of structure is limited in the subsequent growth, the energy difference between the two orientations becomes small. When the volume is larger than the critical value, the horizontal structure becomes more stable than the vertical growth. This simplified thermodynamic model on the basis of surface energy and interfacial energy from density functional theory calculation is well consistent with the above experimental results, implying the feasibility of a vertical-to-horizontal transition during the growth (Fig. 3h).
Furthermore, defects may also play an important role in the aforementioned vertical-to-horizontal transition. At the initial stage (for example, Fig. 3a at 400 °C), the twisty MoS2 fringes in the HRTEM image imply substantial presence of in-plane defects (for example, dislocations, localized disordering and amorphization), resulting from a low-degree crystallization. These defects further increase the (001) surface energy on the basis of the above computation. Upon this circumstance, the vertical structure is more energetically stable than the horizontal one. However, accompanied by the rising temperature (that is, better crystallinity), the amount of defects will consequentially decrease (verified by that the lattice fringes are getting less twisty throughout Fig. 3a–d), leading to a synchronized decrease in (001) surface energy, and, hence, a vertical-to-horizontal transition.
Formation of horizontal MoS2 flakes
Thereafter, MoS2 particles began to precipitate from 820 °C, as shown in Fig. 4 and Supplementary Fig. 7. The red arrows in Supplementary Fig. 7A denote the precipitated MoS2 crystals. The average grain size of MoS2 crystals is enlarged with the increase in the temperature (820–850 °C, Fig. 4 and Supplementary Fig. 7), namely, 3.2 nm at 820 °C, 6.5 nm at 840 °C and 18.5 nm at 850 °C. Figure 4e shows the histograms of the MoS2 flake size as a function of the increasing temperature, in line with our previous SAED analysis in Fig. 1 and Supplementary Fig. 4. Moreover, the dynamics of the increased flake size was recorded and presented in Fig. 5 and Supplementary Movie 2. In Fig. 5a, two isolated MoS2 flakes (I and II), with exposed (103) planes but different orientations, are in contact with each other. These two flakes experienced obvious rotation of crystal orientation to match and align their (103) planes (Fig. 5b) before the disappearance of their grain interface (Fig. 5c). Finally, the coalescence of flakes I and II produces a new flake (III) with relaxed surface (Fig. 5d). The foregoing process refers to typical oriented attachment mechanism37,46,47. This mechanism differs from conventional crystal growth mechanism, in which high-energy facets grow faster via monomer-by-monomer attachment. We also notice that the conventional Ostwald ripening growth pathway also coexists in the process by directly providing monomers, as shown in Supplementary Movie 2, where the small particle fed the large one and became even larger48. Finally, when the temperature is raised to 850 °C, the shape of the MoS2 crystals experienced a dramatic change by facet development via mass redistribution. A majority of the MoS2 crystals reshaped to closely packed, quasi-hexagonal nanoflakes with faceted outlines (see Fig. 4d and Supplementary Fig. 7C, the red arrows in Fig. 4d denoted 120° angles), in good consistence with the CVD result using (NH4)2MoS4 in dimethylformamide as the gas-phase precursor49. The atomic-resolution HRTEM image in Supplementary Fig. 7c corresponds to highly crystalline nature of these nanoflakes, and the associated fast Fourier transform pattern (inset in Supplementary Fig. 7C) displayed a typical sixfold symmetry expected for MoS2 along its  direction. Figure 4f shows the ex situ Raman spectra of the fresh E-chip, the (NH4)2MoS4 precursor and the as-grown MoS2 (annealed at 850 °C for 30 min). No Raman signal is observed from the E-chip or the precursor, while two characteristic Raman modes of MoS2, the in-plane mode E12g and out-of-plane mode A1g, are clearly exhibited in the spectrum of the as-grown sample. Notice that the peak intensity of E12g is over 50% of the A2g peak, indicating the horizontal growth of the MoS2 structure32,50. The separation of the two Raman peaks is ∼25.5 cm−1, suggesting that the MoS2 are four to five layers51, in good agreement with our in situ observations.
The lateral size of the MoS2 nanoflakes in our experiment is only around tens of nanometres, which is close to that by previous CVD growth and hinders its applications for transistors, sensors and so on. This small size is possibly resulted from the limited source and the restricted mass transport ability of MoS2 species in the all-solid environment on the substrate surface35. To evaluate the possibility of growing relative large-size flakes using this method, we further carried out a secondary in situ growth on the same E-chip, and the results are summarized as Supplementary Fig. 8. Evidently, the second growth of MoS2 follows the same mechanism as revealed above (refer to discussions of Supplementary Note 2). The resulting flakes are much larger than the first growth in size (from an average size of ∼20 nm after the first growth to ∼35 nm after the second growth, corresponding to an increase of ∼75%). This implies the potential in growing large-size flakes under the condition that sufficient sources are provided. In this perspective, the as-revealed mechanism should be of general applicability in other synthesis approaches (for example, CVD method) leading to MoS2 microsized flakes or even other 2D-layered transition metal dichalcogenides.
Hence, the overall growth mechanism for MoS2 from solid precursor at high temperature was disclosed. The growth can be divided into two stages: first, the low-temperature vertical stage (below 800 °C, Fig. 3, and the schemes in Figs 2, 3) and, second, the high-temperature horizontal stage (above 800 °C, Fig. 4). At the low-temperature region, the MoS2 growth generally includes the decomposition of solid precursor, the layer-by-layer growth of vertically aligned structures and the successive vertical-to-horizontal transition. Afterwards, at the high-temperature region, the MoS2 nanocrystals spontaneously precipitate, increase the crystalline size via multiple growth pathways and form hexagonal nanoflakes.
In summary, we observed the dynamic growth of 2D MoS2 structure on an amorphous substrate by using an in situ TEM upon heating a solid precursor. We microscopically identified a two-step mechanism during the crystallization of MoS2. Our study using in situ TEM technique provides fundamental understanding on synthesis of the emerging 2D materials and paves the way to rational design of functional nanostructures.
High purity of (NH4)2MoS4 (Sigma-Aldrich, 99.97%) was dissolved in dimethylformamide to form a 1 wt% solution, which was then sonicated for 10 min before being used.
The in situ growth experiment described in this work was conducted on a Protochips Aduro double-tilted platform using heating E-chip specimen support that provides atomic resolution at a thermal ramping rate of up to 106°C s−1 with highly accurate temperature control of specimen inside a TEM. The TEM sample was prepared by drop-casting the above-mentioned solution on a Si3N4 membrane (Si3N4 thickness of ∼50 nm) supported by a silicon E-Chip, which was then naturally dried in air. TEM observations were conducted on a JEM-2100F field-emission transmission electron microscope operating at 200 kV, equipped with an Oxford INCA x-sight EDS Si(Li) detector. Before every experiment, the specimen was heated to 100 °C using 10 °C s−1 increments, and stayed at this temperature for 15 min to remove any possible organic residuals. For the initial SAED survey, the sample was heated from 100 to 900 °C at a rate of 1 °C s 1 and 5 min holding time at every 10 °C to identify the important temperature points. For subsequent TEM/HRTEM analysis, the sample was heated from 100 to 850 °C at a rate of 1 °C s−1 and 30 min holding time at each temperature for a detailed observation. Such in situ experiments were implemented twice to confirm the structural evolution of MoS2. During the observations, the sample was irradiated with a focused electron beam with a current density of ca. 65 pA cm−2 (measured from the fluorescent screen), and the image was recorded with a Gatan SC1000 ORIUS CCD camera with a short exposure time (∼1 s). The electron beam was blanked whenever possible to minimize beam effects on the sample. All reported temperatures are based on the Protochips calibration. It is also essential to assess that the in situ growth is a result of thermally assisted evolution or electron-induced process. Therefore, we designed control experiments with and without constant electron beam irradiation on the samples, and systematically investigated the effects of the electron beam irradiation on the growth dynamics. The detailed procedure and results are described in Supplementary Fig. 9 and Supplementary Note 3.
Simultaneous TGA/DSC analysis were performed on a NETZSCH STA 449 C Jupiter System under flowing N2. Raman measurement was taken using a Horiba Jobin Yvon LabRAM HR System with a laser wavelength of 488 nm. The laser spot size is ∼1 μm with 1.48 mW power. The Raman spectrum was collected with a × 100 Olympus objective lens with a numerical aperture of 0.8, and the acquisition time was set to 5 s. The matched CCD (charge-coupled device) is CCD-7041 from Horiba Jobin Yvon. The Si peak at 520 cm−1 was used for precalibration in the experiments.
The density functional theory calculations have been performed by using the Vienna ab initio simulation package code52,53 within the projector augmented-wave method54,55. General gradient approximations in the Perdew–Burke–Ernzerhof implementation56 were chosen for the exchange correlation function. A plane-wave basis set expanded in energy with a cutoff of 400 eV is used in the calculation. The surfaces have been modelled by a symmetric slab containing eight Mo atom layers and a large vacuum of at least 15 Å. The corresponding oxygen layers are used in the calculation according to different termination and surface orientations. To compare the stability of surfaces with different Miller indices, we calculated their surface free energy following the approach developed by Reuter and Scheffler57. Taking hexagonal Si3N4 (space group P63) as an illustrative substrate, we also calculated the interfacial energy of both surfaces. The (2 × 1) MoS2 (100)/Si3N4 (001) and (2 × 2) MoS2 (001)/Si3N4 (001) structures are used to model the interfaces. In addition, the corresponding interfacial energies are defined by , in which E and S represent the total energy and area of different systems, respectively. To determine the relative stability of the particles with different orientations, the energy of MoS2 particles relative to bulk MoS2 is also evaluated. The (100) ((001)) and (010) index planes are supposed to expose at the side of the particle with (001) ((100)) orientation. The relative energy density per volume thus can be calculated by
in which l, w, h and v are the length, width, height and volume of the particles, σ100(001) and γ100(001) represent surface energy and interfacial energy, respectively. Note that the miller index (100) ((001)) of the MoS2 particle used here corresponds to the vertical (horizontal) growth in article.
The data that support the findings of this study are available from the corresponding author upon request.
How to cite this article: Fei, L. et al. Direct TEM observations on growth mechanisms of two-dimensional MoS2 flakes. Nat. Commun. 7:12206 doi: 10.1038/ncomms12206 (2016).
Guo, Y. et al. Charge trapping at the MoS2-SiO2 interface and its effects on the characteristics of MoS2 metal-oxide-semiconductor field effect transistors. Appl. Phys. Lett. 106, 103109 (2015).
Qiu, H. et al. Hopping transport through defect-induced localized states in molybdenum disulphide. Nat. Commun. 4, 2642 (2013).
Zhou, C. et al. Low voltage and high ON/OFF ratio field-effect transistors based on CVD MoS2 and ultra high-k gate dielectric PZT. Nanoscale 7, 8695–8700 (2015).
Mak, K. F., McGill, K. L., Park, J. & McEuen, P. L. The valley Hall effect in MoS2 transistors. Science 344, 1489–1492 (2014).
Radisavljevic, B., Radenovic, A., Brivio, J., Giacometti, V. & Kis, A. Single-layer MoS2 transistors. Nat. Nanotechnol. 6, 147–150 (2011).
Liu, X. et al. Top–down fabrication of sub-nanometre semiconducting nanoribbons derived from molybdenum disulfide sheets. Nat. Commun. 4, 1776 (2013).
Wang, Q. H., Kalantar-Zadeh, K., Kis, A., Coleman, J. N. & Strano, M. S. Electronics and optoelectronics of two-dimensional transition metal dichalcogenides. Nat. Nanotechnol. 7, 699–712 (2012).
Koppens, F. H. L. et al. Photodetectors based on graphene, other two-dimensional materials and hybrid systems. Nat. Nanotechnol. 9, 780–793 (2014).
Lopez-Sanchez, O., Lembke, D., Kayci, M., Radenovic, A. & Kis, A. Ultrasensitive photodetectors based on monolayer MoS2 . Nat. Nanotechnol. 8, 497–501 (2013).
Li, W. et al. Broadband optical properties of large-area monolayer CVD molybdenum disulfide. Phys. Rev. B 90, 195434 (2014).
Yin, X. et al. Edge nonlinear optics on a MoS2 atomic monolayer. Science 344, 488–490 (2014).
Xia, F., Wang, H., Xiao, D., Dubey, M. & Ramasubramaniam, A. Two-dimensional material nanophotonics. Nat. Photon. 8, 899–907 (2014).
Loan, P. T. K. et al. Graphene/MoS2 heterostructures for ultrasensitive detection of DNA hybridisation. Adv. Mater. 26, 4838–4844 (2014).
Zhang, Y. et al. Single-layer transition metal dichalcogenide nanosheet-based nanosensors for rapid, sensitive, and multiplexed detection of DNA. Adv. Mater. 27, 935–939 (2015).
Perkins, F. K. et al. Chemical vapor sensing with monolayer MoS2 . Nano Lett. 13, 668–673 (2013).
Late, D. J. et al. Sensing behavior of atomically thin-layered MoS2 transistors. ACS Nano 7, 4879–4891 (2013).
Voiry, D. et al. Conducting MoS2 nanosheets as catalysts for hydrogen evolution reaction. Nano Lett. 13, 6222–6227 (2013).
Chang, Y.-H. et al. Highly efficient electrocatalytic hydrogen production by MoSx grown on graphene-protected 3D Ni foams. Adv. Mater. 25, 756–760 (2013).
Smith, A. J. et al. Molybdenum sulfide supported on crumpled graphene balls for electrocatalytic hydrogen production. Adv. Energy Mater. 4, 1400398 (2014).
Karunadasa, H. I. et al. A molecular MoS2 edge site mimic for catalytic hydrogen generation. Science 335, 698–702 (2012).
Jaramillo, T. F. et al. Identification of active edge sites for electrochemical H2 evolution from MoS2 nanocatalysts. Science 317, 100–102 (2007).
Chen, Y., Tan, C., Zhang, H. & Wang, L. Two-dimensional graphene analogues for biomedical applications. Chem. Soc. Rev. 44, 2681–2701 (2015).
Sun, G. et al. Hybrid fibers made of molybdenum disulfide, reduced graphene oxide, and multi-walled carbon nanotubes for solid-state, flexible, asymmetric supercapacitors. Angew. Chem. Int. Ed. 54, 4651–4656 (2015).
Acerce, M., Voiry, D. & Chhowalla, M. Metallic 1T phase MoS2 nanosheets as supercapacitor electrode materials. Nat. Nanotechnol. 10, 313–318 (2015).
Wu, W. et al. Piezoelectricity of single-atomic-layer MoS2 for energy conversion and piezotronics. Nature 514, 470–474 (2014).
Huang, X., Zeng, Z. & Zhang, H. Metal dichalcogenide nanosheets: preparation, properties and applications. Chem. Soc. Rev. 42, 1934–1946 (2013).
Wang, H., Yuan, H., Sae Hong, S., Li, Y. & Cui, Y. Physical and chemical tuning of two-dimensional transition metal dichalcogenides. Chem. Soc. Rev. 44, 2664–2680 (2015).
Sakashita, Y. Effects of surface orientation and crystallinity of alumina supports on the microstructures of molybdenum oxides and sulfides. Surf. Sci. 489, 45–58 (2001).
Najmaei, S. et al. Vapour phase growth and grain boundary structure of molybdenum disulphide atomic layers. Nat. Mater. 12, 754–759 (2013).
Lee, Y. H. et al. Synthesis of large-area MoS2 atomic layers with chemical vapor deposition. Adv. Mater. 24, 2320–2325 (2012).
Lin, Z. et al. Controllable growth of large-size crystalline MoS2 and resist-free transfer assisted with a Cu thin film. Sci. Rep. 5, 18596 (2015).
Kong, D. et al. Synthesis of MoS2 and MoSe2 films with vertically aligned layers. Nano Lett. 13, 1341–1347 (2013).
Jung, Y. et al. Metal seed layer thickness-induced transition from vertical to horizontal growth of MoS2 and WS2 . Nano Lett. 14, 6842–6849 (2014).
Hansen, L. P., Johnson, E., Brorson, M. & Helveg, S. Growth mechanism for single- and multi-layer MoS2 nanocrystals. J. Phys. Chem. C 118, 22768–22773 (2014).
Liu, K. K. et al. Growth of large-area and highly crystalline MoS2 thin layers on insulating substrates. Nano Lett. 12, 1538–1544 (2012).
Ramachandramoorthy, R., Bernal, R. & Espinosa, H. D. Pushing the envelope of in situ transmission electron microscopy. ACS Nano 9, 4675–4685 (2015).
Fei, L. et al. Direct observation of carbon nanostructure growth at liquid-solid interfaces. Chem. Commun. 50, 826–828 (2014).
Nielsen, M. H., Aloni, S. & De Yoreo, J. J. In situ TEM imaging of CaCO3 nucleation reveals coexistence of direct and indirect pathways. Science 345, 1158–1162 (2014).
Liao, H.-G., Cui, L., Whitelam, S. & Zheng, H. Real-time imaging of Pt3Fe nanorod growth in solution. Science 336, 1011–1014 (2012).
Boston, R., Schnepp, Z., Nemoto, Y., Sakka, Y. & Hall, S. R. In situ TEM observation of a microcrucible mechanism of nanowire growth. Science 344, 623–626 (2014).
Brito, J. L., Ilija, M. & Hernández, P. Thermal and reductive decomposition of ammonium thiomolybdates. Thermochim. Acta 256, 325–338 (1995).
Verble, J. L., Wietling, T. J. & Reed, P. R. Rigid-layer lattice vibrations and van der Waals bonding in hexagonal MoS2 . Solid State Commun. 11, 941–944 (1972).
Stockmann, R. M., Zandbergen, H. W., van Langeveld, A. D. & Moulijn, J. A. Investigation of MoS2 on γ-Al2O3 by HREM with atomic resolution. J. Mol. Catal. A Chem. 102, 147–161 (1995).
de Jong, K. P. et al. High-resolution electron tomography study of an industrial Ni-Mo/gamma-Al2O3 hydrotreating catalyst. J. Phys. Chem. B 110, 10209–10212 (2006).
Chhowalla, M. et al. The chemistry of two-dimensional layered transition metal dichalcogenide nanosheets. Nat. Chem. 5, 263–275 (2013).
De Yoreo, J. J. et al. Crystallization by particle attachment in synthetic, biogenic, and geologic environments. Science 349, aaa6760 (2015).
Li, D. et al. Direction-specific interactions control crystal growth by oriented attachment. Science 336, 1014–1018 (2012).
Yin, Y. & Alivisatos, A. P. Colloidal nanocrystal synthesis and the organic-inorganic interface. Nature 437, 664–670 (2005).
Shi, Y. et al. van der Waals epitaxy of MoS2 layers using graphene as growth templates. Nano Lett. 12, 2784–2791 (2012).
Wang, H. et al. Electrochemical tuning of vertically aligned MoS2 nanofilms and its application in improving hydrogen evolution reaction. Proc. Natl Acad. Sci. USA 110, 19701–19706 (2013).
Lee, C. et al. Anomalous lattice vibrations of single- and few-layer MoS2 . ACS Nano 4, 2695–2700 (2010).
Kresse, G. & Furthmüller, J. Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set. Comput. Mater. Sci. 6, 15–50 (1996).
Kresse, G. & Furthmüller, J. Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set. Phys. Rev. B 54, 11169–11186 (1996).
Blöchl, P. E. Projector augmented-wave method. Phys. Rev. B 50, 17953–17979 (1994).
Kresse, G. & Joubert, D. From ultrasoft pseudopotentials to the projector augmented-wave method. Phys. Rev. B 59, 1758–1775 (1999).
Perdew, J. P., Burke, K. & Ernzerhof, M. Generalized gradient approximation made simple. Phys. Rev. Lett. 77, 3865–3868 (1996).
Reuter, K. & Scheffler, M. Composition, structure and stability of RuO2(110) as a function of oxygen pressure. Phys. Rev. B 65, 035406 (2001).
This work was supported by the Research Grant Council of Hong Kong (project Nos: PolyU 252001/14E, GRF 5016/12P), The Hong Kong Polytechnic University (project Nos: G-UC71, G-UC72) and the National Natural Science Foundation of China (project Nos. 51428202, 61302045, 11574126 and 51562026). S.L. acknowledges the financial supports from National Natural Science Foundation of China (project No. 21461014). Y.W. acknowledges the support from the ‘863’ Project of China (project No. 2013AA031903) and Chutian Scholarship of Hubei Province of China.
The authors declare no competing financial interests.
Supplementary Figures 1-9, Supplementary Notes 1-3 and Supplementary References (PDF 1867 kb)
Typical growth dynamics of MoS2 layer formation maintaining at 400 oC. The snapshot frames were captured as Figure 2 A-D. The video was edited to play at 4X speed. (WMV 12423 kb)
Typical growth dynamics on the coalescence of a small MoS2 nanoparticles by larger one upon heating to 840 oC. This video was edited to play at 8X speed. (WMV 61088 kb)
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Fei, L., Lei, S., Zhang, WB. et al. Direct TEM observations of growth mechanisms of two-dimensional MoS2 flakes. Nat Commun 7, 12206 (2016). https://doi.org/10.1038/ncomms12206
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