Skip to main content
Nano Convergence
Download PDF

Microscopic evidence of strong interactions between chemical vapor deposited 2D MoS2 film and SiO2 growth template

Nano Convergence volume 8, Article number: 11 (2021) Cite this article

Abstract

Two-dimensional MoS2 film can grow on oxide substrates including Al2O3 and SiO2. However, it cannot grow usually on non-oxide substrates such as a bare Si wafer using chemical vapor deposition. To address this issue, we prepared as-synthesized and transferred MoS2 (AS-MoS2 and TR-MoS2) films on SiO2/Si substrates and studied the effect of the SiO2 layer on the atomic and electronic structure of the MoS2 films using spherical aberration-corrected scanning transition electron microscopy (STEM) and electron energy loss spectroscopy (EELS). The interlayer distance between MoS2 layers film showed a change at the AS-MoS2/SiO2 interface, which is attributed to the formation of S–O chemical bonding at the interface, whereas the TR-MoS2/SiO2 interface showed only van der Waals interactions. Through STEM and EELS studies, we confirmed that there exists a bonding state in addition to the van der Waals force, which is the dominant interaction between MoS2 and SiO2. The formation of S–O bonding at the AS-MoS2/SiO2 interface layer suggests that the sulfur atoms at the termination layer in the MoS2 films are bonded to the oxygen atoms of the SiO2 layer during chemical vapor deposition. Our results indicate that the S–O bonding feature promotes the growth of MoS2 thin films on oxide growth templates.

Introduction

Transition metal dichalcogenides, such as MoS2, have attracted much interest because of their remarkable electrical, mechanical, thermal, and optical properties. Therefore, they are considered novel materials and suitable for application in optoelectronic devices, water-splitting catalysts, sensors, field-effect transistors, capacitors, and energy storage devices [1,2,3,4,5,6,7,8,9,10]. Recent studies have focused on the large-scale growth of MoS2 films, which is mainly carried out on Al2O3 and SiO2/Si substrates [11,12,13,14]. Through chemical vapor deposition (CVD) and pulsed laser deposition (PLD), MoS2 films are well deposited when the Si wafer has a SiO2 layer on the top. In contrast, the growth of MoS2 fails or MoSi2 is synthesized instead of MoS2 when CVD growth is carried out on a bare Si wafer even if Si substrate has a native oxide layer on top because the thin native oxide layer can be removed or penetrated during the high temperature synthesis process [4, 15]. Moreover, there are a few studies to show the formation of MoSi2 through chemical reactions between MoS2 and Si. When the Mo film is sulfurized on a bare Si wafer, the formation of a gas phase SiS2 rather than MoS2 is presumable. This indicates that making large-scale growth of MoS2 directly on Si is hardly achievable. However, when Mo is sulfurized on SiO2 substrates, S–O bonding is preferable rather than S–Si bonding, which helps Mo-S bonding followed by growth of a MoS2 film. The different tendency of CVD MoS2 growth on bare Si and SiO2/Si substrates was found in previous studies [4, 15]. To date, it has been reported that some substrates such as SiO2/Si and sapphire enable the large-scale deposition of MoS2 films. However, microscopic evidence showing the interaction between the chemical-vapor-deposited MoS2 and the SiO2 growth template has not been observed. Microscopic studies are mainly focused on the atomic and electronic structures of MoS2, using transmission electron microscopy (TEM) and aberration-corrected scanning transmission electron microscopy (Cs-corrected STEM), which can directly observe materials on an atomic level. Crystal and atomic structures with various defects have been discovered using a combination of ab-initio calculations [4, 11,12,13,14, 16,17,18,19,20,21,22].

To investigate the atomic and electronic structure and chemical state of the MoS2/SiO2 heterostructure, an atomic-scale study using Cs-corrected STEM and EELS with a cross-sectional view should be carried out. The use of Cs-corrected STEM with a probe corrector would enable the direct observation of heterointerfaces at the atomic resolution. Moreover, the changes in the electronic and chemical states would be available in unit-cell resolution. Interfaces between dissimilar compounds provide unusual properties that are attributed to lattice mismatch, strain, chemical bonds, and the formation of secondary interfacial layers [23,24,25,26,27]. The observation of the atomic and electronic structures of MoS2/SiO2 interfaces not only provides insights on the growth mechanisms and bonding states, but also suggests the possibility of application in various devices. Understanding the nature of the interfaces can provide insights on how the MoS2 film is synthesized via CVD and how the MoS2 `film on the SiO2/Si template can be utilized in electronic devices.

In this work, we investigated the atomic and electronic structures of MoS2 (more than 20 layers)/SiO2 interfaces on an Si substrate. First, we observed and compared the atomic structure of the AS and TR-MoS2 films on the SiO2/Si substrates and plotted the (001) plane distance from the interface to the interior of the film. Second, we investigated the chemical bonding state at the AS and TR-MoS2/SiO2 hetero interfaces. The final aim of this study is figuring out the main reason why MoS2 is deposited only on oxide substrates such as SiO2, Al2O3 and understanding how the SiO2 layer affects the structures of MoS2 films when Mo is sulfurized through CVD [11,12,13]. We used SiO2 for a growth template mainly because other oxides such as Al2O3 and SrTiO3 do not dissolve in HF, disabling transfer process. For this purpose, we carried out a TEM-based analysis with Cs-corrected high annular dark field (HAADF) imaging, and annular bright field (ABF) STEM imaging and EELS with a combination of ab-initio calculations. To the best of our knowledge, this is the first reported paper investigating the influence of the SiO2 template on the growth of MoS2 films using Cs-corrected STEM and EELS with a cross-sectional view.

Experimental details

MoS2 film deposition

SiO2(300 nm)/Si wafers were cleaned with a standard piranha solution (3:1 mixture of H2SO4 and H2O2) using conventional cleaning procedures followed by ultrasonication in acetone, isopropyl alcohol, and deionized (DI) water. To obtain hydrophilic surfaces on the SiO2/Si wafers, O2 plasma and UV-O3 surface treatments were sequentially performed for 15 min. A 10 nm-thick Mo thin film was deposited on a SiO2/Si substrate using an E-beam evaporator. (Rocky Mountain Vacuum Tech, Englewood, CO, USA). The base pressure, E-beam voltage, and current were 10–6 Torr, 7.3 kV, and 70 mA, respectively, and the deposition rate was approximately 0.1 Å/s. Sulfurization of the Mo thin film was performed by CVD at 900 °C for 30 min. After sulfurization, the thin films were annealed for the crystallization of the MoS2 films.

TEM sample preparation

Due to the weak interaction between the MoS2 film and SiO2 layer, MoS2 films are peeled off from SiO2 when cross-section TEM specimen preparation using polishing. To minimize mechanical damage, we carried out FIB TEM sample preparation followed by nanomilling (Fischione 1040). Nanomill is similar to precision ion polishing, except that the milling area can be selected during nanomill process. Thus, nanomill is the optimal method for the preparation of the FIB TEM specimens.

Raman, XPS, TEM and STEM/EELS characterization

Raman and X-ray photoelectron spectroscopy were carried out to analyze vibration modes and surface chemical states of the MoS2 films using LABRAM HR Evolution and AXIS-Hsi. The Mo to S ratio of the MoS2 films are calculated by dividing intensity or the area of each elements by factor of Mo or S elements [4].

The TEM analysis was divided into 2 steps. First, we obtained bright-field TEM and high-resolution TEM images to confirm the quality and thickness of the TEM specimen. In this step, we analyzed the MoS2 film using JEOL JEM-2100F. In the next step, to investigate the atomic structure of the interfaces, Cs-corrected high-resolution STEM images were obtained with a Cs-probe corrected TEM instrument (JEOL JEM ARM 200F). STEM imaging with a spherical aberration corrector provided clearer images with a spatial resolution of 80 pm. Thus, Cs-corrected HR-STEM imaging enabled the identification of elements as well as the location of atomic positions with high accuracy.

Theoretical calculation

For the calculations, the MoS2-SiO2 heterostructure supercell was composed of 8 Si layers of SiO2, a monolayer of MoS2, and a 15 Å vacuum layer to prevent the interaction between layers. Both sides of the SiO2 slab were reconstructed surfaces, which have a lower surface energy compared to a pristine surface according to a previous study [29]. Before constructing the heterostructure, the unit cells of SiO2 and MoS2 were first relaxed; the lattice parameters were a = b = 4.896 Å for SiO2 and a = b = 3.161 Å for MoS2. Subsequently, along the x–y plane, SiO2 in 2 × 2 lateral periodicity and MoS2 in 3 × 3 lateral periodicity was stacked together. Considering that the monolayer MoS2 is much more prone to deformation than bulk SiO2, the x–y plane lattice parameter of 2 × 2 SiO2 was employed as that of a heterostructure supercell. This allowed the MoS2 layer to expand along the x and y directions with a lattice mismatch of approximately 3.4%. In addition, the position of the SiO2 layer was fixed during the relaxation of the heterostructure for the same reason mentioned above. All structural relaxations and free energy calculations were performed with the Vienna ab initio simulation package (VASP) [31, 32] based on density functional theory (DFT) [33, 34]. For the replacement of the core electrons, a projector augmented wave (PAW) [35, 36] scheme was implemented. The exchange–correlation energy was described through the generalized gradient approximation (GGA) using the Perdew-Burke-Emzerhof (PBE) functional [37]. The kinetic cutoff for the plane-wave basis was 400 eV. The Brillouin zone for 3 × 3 × 1 k-point sampling was constructed with a gamma-centered grid. For electronic self-consistency and force tolerance, criteria of 5–10 eV and 0.01 eV/A were applied.

Results and discussion

The growth of the MoS2 film and imaging of the MoS2/SiO2 interface

The growth and transfer process of the MoS2 film is shown in Fig. 1(a). The experimental details are explained in the Sect. 2.1. The growth of the AS-MoS2 film was demonstrated using Raman spectroscopy, as shown in Additional file 1: Figure S1. The Raman spectrum showed two characteristic Raman vibration modes, E12g and A1g, which indicated that the MoS2 film grew laterally on the Si/SiO2 substrate.

Fig. 1
figure 1

a Schematic illustration of the MoS2 film deposition and transfer. STEM images of MoS2 film on SiO2/Si. b Low-magnification HAADF STEM, c Cs-corrected ABF STEM, and d Cs-corrected HAADF STEM images of AS-MoS2 film. e Low-magnification HAADF STEM, f Cs-corrected ABF STEM, and g Cs- corrected HAADF STEM images of TR-MoS2 film

Full size image

Due to the weak interaction between the TMD film and the substrate, which hinders the observation of the structure of the interfaces when the TEM sample is prepared using mechanical polishing, we prepared a TEM specimen using a focused ion beam (FIB) followed by nanomill using a Fischione 1040 nanomill. Additional file 1: Figure S2 depicts the result using the prepared AS and TR-MoS2 films, which are in line with the Raman spectrum. Figure 1(b) and (c) is the HAADF STEM image and shows that the MoS2 film was laterally aligned on the amorphous silicon oxide layer. Since the SiO2 growth template is not atomically smooth, the AS-MoS2/SiO2 interface seems to be rough. Figure 1(c) is a contrast-inverted ABF STEM image. As ABF STEM imaging is efficient in detecting light elements, especially sulfur, the atomic configuration in Fig. 1(d) shows clearer image contrast than that in Fig. 1(c). The TR-MoS2 film also showed comparatively well laterally aligned MoS2 sheets at the surface and in the interior of the layer as shown in Fig. 1(e–g). In addition, the TR-MoS2 film showed no significant difference in the overall lattice structure and interlayer distance.

Interlayer distance of the AS and TR-MoS2 films depending on number of layers

To quantify the effect of the amorphous SiO2 layer on the atomic structure of the MoS2 film, we plotted the changes in the out-of-plane distance at 16 different positions and calculated the average interlayer distance with error bars. Each measured distance of the AS and TR-MoS2 films is depicted in Additional file 1: Figure S3. As shown in Fig. 2(a) and (b), at the AS-MoS2/SiO2 interface, the interlayer distance was up to 3.7% shorter than that of the AS-MoS2 film, whereas there was no significant change in the interlayer distance in the TR-MoS2 film, as shown in Fig. 2(c) and (d). The huge error bar is not originated from the roughness of the of the SiO2 substrate, but irregular S–O bond at the MoS2/SiO2 interface, making the shape of the MoS2 surface wavy. Despite of this roughness, the difference in tendency of interlayer distance of AS and TR-MoS2 films is non-negligible. This suggests that when MoS2 films are grown on SiO2 via the sulfurization of the Mo film, SiO2 not only plays a significant role as a growth template but also influences the atomic structure of the AS-MoS2 film at the MoS2/SiO2 interface. Considering that only van der Waals interactions occur between the MoS2 layers in the bulk, the change in interlayer distance is attributed to the chemical bonding between AS-MoS2 and SiO2.

Fig. 2
figure 2

Changes in the interlayer distance at the MoS2/SiO2 interface. a Position at which the interlayer distance values were measured in the AS-MoS2 films. b Plot of the interlayer distance of AS-MoS2. The black solid line represents the average value of the interlayer distance with error. c Position at which the interlayer distance values were measured in the TR-MoS2 films. d Plot of the interlayer distance of TR-MoS2. The black solid line represents the average value of the distance with error

Full size image

Next, we carried out ab-initio calculations to suggest an atomic model based on STEM images. We compared the equivalent distance between SiO2 (single crystal)-MoS2 and MoS2-MoS2 with the assumption that the MoS2/SiO2 interface is S–O-terminated. As shown in Fig. 3(a), the shortest distance between SiO2-MoS2 was calculated to be 3.16 Å, which was slightly longer than the MoS2-MoS2 distance, 3.04 Å. Figure 3(b) illustrates the formation energy as a function of the distance between SiO2 and MoS2. Figure 3(b) shows that 3.16 Å provides the most stable formation energy in our calculation. Since the calculation assumed that SiO2 was a single crystal and considered only the van der Waals interaction, the result of the calculation deviated from that of the experiment. This discrepancy suggests that there is a strong chemical interaction other than the van der Waals force between the AS MoS2 film and the SiO2 template. This is in contrast with the previous DFT study, which argued that the structure of MoS2 is not affected by SiO2 [28, 29].

Fig. 3
figure 3

a Atomistic model of the MoS2 layer on the single-crystal SiO2. b Formation energy as a function of SiO2-MoS2 distance

Full size image

Chemical bonding at the MoS2/SiO2 interface

MoS2 films were analyzed using X-ray photoelectron spectroscopy (XPS) to determine the chemical composition and atomic ratios of the films on the SiO2/Si substrate. The core level spectra of Mo 3d and S 2p were recorded for the AS- and TR-MoS2 films (Additional file 1: Figure S4a–d). Figure 4 shows that the AS- and TR-MoS2 films were both deposited in a stoichiometric composition (Mo:S = 1:2) without any significant chemical shift. In addition, the XPS characteristics of the AS-MoS2 film were not significantly different from those of the transferred sample. However, since the detection depth of XPS was only a few nanometers and XPS detected the overall area of the MoS2 films, the XPS profiles of the MoS2 films could not clarify the electronic structure of the MoS2/SiO2 interfaces, which are defined in the sub-nanometer range.

Fig. 4
figure 4

a Region of AS-MoS2/SiO2 in which EELS spectra were obtained. b S L-edge of the AS-MoS2 film. c Comparison between the S L-edges of the AS-MoS2 film (blue line) and MoS2/SiO2 interface (red line). d O K-edge of the AS-MoS2 film. e Comparison between the O K-edges of the AS-MoS2 film (yellow line) and MoS2/SiO2 interface (red line). f Region of TR-MoS2/SiO2 in which EELS spectra were obtained. g S L-edge of the TR-MoS2 film h Comparison between the S L-edges of the TR-MoS2 film (blue line) and MoS2/SiO2 interface (red line). i O K-edge of the TR-MoS2 film. j Comparison between the O K-edges of the TR-MoS2 film (yellow line) and MoS2/SiO2 interface (red line)

Full size image

To identify the chemical bonding state at the MoS2/SiO2 interface, we obtained and analyzed the EELS SL and O K-edge spectra. Unlike XPS, EELS can provide chemical information in a local area with a spatial resolution in the sub-nanometer range, thus facilitating the analysis of the MoS2/SiO2 heterointerfaces. The TEM sample was thin enough for the noise in the EELS spectra to be minimized, and each spectrum was acquired at a distance of 0.6 nm. Figure 4(a) and (e) show the STEM HAADF image of both samples from which the EELS spectra were acquired; both films were found to be well attached to the substrate through the TEM sample preparation. Next, we compared the S L- and O K-edge spectra in the two above-mentioned samples to identify the bonding state of AS-MoS2 on the SiO2/Si substrate. Figure 4(b) shows the changes in the S L-edge at 10 different positions, and Fig. 4(c) shows the difference in the S L-edge spectra at the MoS2/SiO2 interface (red solid line) and the MoS2 film (blue solid line). The two spectra showed differences not only in the intensity, but also in the overall edge structure. In addition, considering that the MoS2/SiO2 interface was S–O-terminated, the difference of the S L-edge at the interface.Please provide complete details for the References The appearance of the peak at 168 eV indicates that the sulfur atoms were partially bonded to the oxygen atoms. The deviation from the previous study is due to the defects at the AS-MoS2/SiO2 interface. In other words, at the MoS2/SiO2 interface, the sulfur atom of the MoS2 film had four nearest-neighbor oxygen atoms from the amorphous SiO2 growth template. Figure 4(d) shows the O K-edge at 10 different positions. The O K-edge also showed a peak shift at the AS-MoS2/SiO2 interface compared to that of the interior of SiO2. Figure 4(c) shows that along with the S–O bond, several defects were also formed at the AS-MoS2/SiO2 interface over the range of 1.2–1.5 nm. In addition, the negative peak shifts of the SL and O K-edges at the AS-MoS2/SiO2 interface were due to an increase in the negative charge around the sulfur and oxygen ions.

The EELS edge spectra of the TR-MoS2/SiO2/Si heterostructure were also observed. Figure 4(g) and (i) present the S L- and O K-edges at 10 different positions. In contrast to those for the AS-MoS2 sample, the sulfur and oxygen edge spectra exhibited no significant difference, as shown in Fig. 3(h) and (j). Since the TR-MoS2 film was detached and transferred onto the SiO2/Si substrate, only van der Waals interactions existed between the MoS2 and SiO2 template.

Based on the EELS spectra of the AS-MoS2 sample, we prepared an electron transition diagram (Fig. 5). The EELS core loss spectra showed the transition of electrons from the core state to the unoccupied state [30]. As shown in Fig. 5(a) and (b), the peak positions near 540 eV and 560 eV in the O K-edge spectra are attributed to the transition of electrons from O 1 s to O 2p mixed with Si 3sp and Si d states [30]. Figure 5(a) shows negative peak shifts at the interface and the formation of an energy loss peak at 542 eV, which were due to an increase in the negative charge at the interface and the formation of the S–O bond, respectively. However, there is no peak shift in O K edge at the TR-MoS2/SiO2 interface, as shown in Fig. 5(b). This indicates that when sulfur atoms are chemically bonded with oxygen in SiO2, excess negative charges accumulate at the interface, causing a negative peak shift of the S L- and O K-edges.

Fig. 5
figure 5

Electron transition diagram of the SiO2 layer a at the AS-MoS2/SiO2 and b TR-MoS2/SiO2 interface

Full size image

Combining all experimental results, the summary of our study is illustrated in Fig. 6. At the AS-MoS2/SiO2 interface, the interlayer distance decreases due to the formation of S–O bonding, whereas there is no significant change in the interlayer distance at the TR-MoS2/SiO2 interface, 12 which can explain the role of oxide templates such as SiO2 and Al2O3 on the large-scale growth of the MoS2 film. In addition, our key findings play a role in enhancing the carrier mobility of the MoS2 film, which can lead to the improved performance of devices [38,39,40,41,42,43].

Fig. 6
figure 6

Schematic illustration of the phenomena at the AS and TR-MoS2/SiO2 interface. At the AS-MoS2/SiO2 interface, the interlayer distance decreases due to the formation of S–O bonding, whereas there is no significant change in the interlayer distance at the TR-MoS2/SiO2 interface

Full size image

Conclusions

We prepared MoS2 films on SiO2/Si substrates and studied the effect of the amorphous SiO2 layer on the atomic and electronic structure of the MoS2 films. The interlayer distance of the AS-MoS2 film exhibited a change at the AS-MoS2/SiO2 interface, which was attributed to the formation of S–O chemical bonding at the interface. Through theoretical calculations, we confirmed the existence of a bonding state in addition to the van der Waals force, which was the dominant interaction between MoS2 and SiO2. The formation of S–O bonding at the AS-MoS2/SiO2 interface layer suggested that during CVD, the Mo thin film was not only sulfurized, but the sulfur atoms at the termination layer were also bonded to the oxygen atoms of the SiO2 layer, preventing the formation of Si-S bonding and MoSi2 (Fig. 6). Our key findings in the study are consistent regardless of the deposition techniques. In other words, the formation of S–O bonding occurs and interlayer distance between the AS-MoS2 film and the substrate is affected by the SiO2 growth template even if MoS2 is deposited by MOCVD or other deposition techniques.This study not only provides a guideline on the relationship between the interfacial structure and electrical properties of MoS2 thin film-based heterostructures and explains the role of oxides on the growth of MoS2 films, but also shows that this kind of interfacial interaction is prominent when it comes to single layer MoS2 which is generally used for a wide variety of devices.

Availability of data and materials

Not applicable.

Abbreviations

AS-MoS2 :

As-synthesized MoS2

TR-MoS2 :

Transferred MoS2

STEM:

Scanning transition electron microscopy

EELS:

Electron energy loss spectroscopy

CVD:

Chemical vapor deposition

PLD:

Pulsed laser deposition

TEM:

Transmission electron microscopy

Cs-corrected STEM:

Aberration-corrected scanning transmission electron microscopy

HAADF:

High annular dark field

ABF:

Annular bright field

DI:

Deionized

VASP:

Vienna Ab initio Simulation package

DFT:

Density functional theory

GGA:

Generalized gradient approximation

References

  1. X. Liu, L. Chen, Q. Liu, J. He, K. Li, W. Yu, J.P. Ao, K.W. Ang, J. Alloys Compd. 698, 141 (2017)

    CAS  Google Scholar 

  2. K.S. Novoselov, D. Jiang, F. Schedin, T.J. Booth, V.V. Khotkevich, S.V. Morozov, A.K. Geim, Proc. Natl. Acad. Sci. U. S. A. 102, 10451 (2005)

    CAS  Google Scholar 

  3. B. Radisavljevic, A. Radenovic, J. Brivio, V. Giacometti, A. Kis, Nat. Nanotechnol. 6, 147 (2011)

    CAS  Google Scholar 

  4. K.C. Kwon, S. Choi, K. Hong, C.W. Moon, Y.S. Shim, D.H. Kim, T. Kim, W. Sohn, J.M. Jeon, C.H. Lee, K.T. Nam, S. Han, S.Y. Kim, H.W. Jang, Energy Environ. Sci. 9, 2240 (2016)

    CAS  Google Scholar 

  5. M.R. Laskar, L. Ma, S. Kannappan, P. Sung Park, S. Krishnamoorthy, D.N. Nath, W. Lu, Y. Wu, S. Rajan, Appl. Phys. Lett. 102, 252108 (2013)

    Google Scholar 

  6. J.N. Coleman, M. Lotya, A. O’Neill, S.D. Bergin, P.J. King, U. Khan, K. Young, A. Gaucher, S. De, R.J. Smith, I.V. Shvets, S.K. Arora, G. Stanton, H.Y. Kim, K. Lee, G.T. Kim, G.S. Duesberg, T. Hallam, J.J. Boland, J.J. Wang, J.F. Donegan, J.C. Grunlan, G. Moriarty, A. Shmeliov, R.J. Nicholls, J.M. Perkins, E.M. Grieveson, K. Theuwissen, D.W. McComb, P.D. Nellist, V. Nicolosi, Science 331, 568 (2011)

    CAS  Google Scholar 

  7. M.W.S.W.Y. Lee, T.M. Besmann, J. Mater. Res. 9, 1474 (1994)

    CAS  Google Scholar 

  8. Y.H. Lee, X.Q. Zhang, W. Zhang, M.T. Chang, C. Te Lin, K. Di Chang, Y.C. Yu, J.T.W. Wang, C.S. Chang, L.J. Li, T.W. Lin, Adv. Mater. 24, 2320 (2012)

    CAS  Google Scholar 

  9. G. Clark, S. Wu, P. Rivera, J. Finney, P. Nguyen, D.H. Cobden, and X. Xu, APL Mater. 2, 101101 (2014)

    Google Scholar 

  10. M. Ye, D. Winslow, D. Zhang, R. Pandey, Y.K. Yap, Photonics 2, 288 (2015)

    CAS  Google Scholar 

  11. N. Lu, C. Zhang, C.H. Lee, J.P. Oviedo, M.A.T. Nguyen, X. Peng, R.M. Wallace, T.E. Mallouk, J.A. Robinson, J. Wang, K. Cho, M.J. Kim, J. Phys. Chem. C 120, 8364 (2016)

    CAS  Google Scholar 

  12. G. Deokar, N.S. Rajput, P. Vancsó, F. Ravaux, M. Jouiad, D. Vignaud, F. Cecchet, J.F. Colomer, Nanoscale 9, 277 (2017)

    CAS  Google Scholar 

  13. T.P. Nguyen, W. Sohn, J.H. Oh, H.W. Jang, S.Y. Kim, J. Phys. Chem. C 120, 10078 (2016)

    CAS  Google Scholar 

  14. X. Su, H. Cui, W. Ju, Y. Yong, X. Li, Mod. Phys. Lett. B 31, 1 (2017)

    Google Scholar 

  15. P.A. Bertrand, Langmuir 5, 1387 (1989)

    CAS  Google Scholar 

  16. S. Hussain, J. Singh, D. Vikraman, A.K. Singh, M.Z. Iqbal, M.F. Khan, P. Kumar, D.C. Choi, W. Song, K.S. An, J. Eom, W.G. Lee, J. Jung, Sci. Rep. 6, 1 (2016)

    Google Scholar 

  17. W. Zhou, X. Zou, S. Najmaei, Z. Liu, Y. Shi, J. Kong, J. Lou, P.M. Ajayan, B.I. Yakobson, J.C. Idrobo, Nano Lett. 13, 2615 (2013)

    CAS  Google Scholar 

  18. R.J. Wu, M.L. Odlyzko, K.A. Mkhoyan, Ultramicroscopy 147, 8 (2014)

    CAS  Google Scholar 

  19. L. Jin, C.L. Jia, I. Lindfors-Vrejoiu, X. Zhong, H. Du, R.E. Dunin-Borkowski, Adv. Mater. Interfaces 3, 1 (2016)

    CAS  Google Scholar 

  20. Y. Ishikawa, K. Wada, D.D. Cannon, J. Liu, H.C. Luan, L.C. Kimerling, Appl. Phys. Lett. 82, 2044 (2003)

    CAS  Google Scholar 

  21. K.S. Siow, L. Britcher, S. Kumar, H.J. Griesser, Sains Malaysiana 47, 1913 (2018)

    CAS  Google Scholar 

  22. D.Y. Cho, S. Tappertzhofen, R. Waser, I. Valov, Nanoscale 5, 1781 (2013)

    CAS  Google Scholar 

  23. G. Kresse, J. Furthmüller, Comput. Mater. Sci. 6, 15 (1996)

    CAS  Google Scholar 

  24. J.F.G. Kresse, Phys. Rev. B 54, 170 (1996)

    Google Scholar 

  25. P. Hohenberg, W. Kohn, Phys. Rev. 136, B864 (1964)

    Google Scholar 

  26. W. Kohn, L.J. Sham, Phys. Rev. 140, 1133 (1965)

    Google Scholar 

  27. H. Li, Q. Zhang, C.C.R. Yap, B.K. Tay, T.H.T. Edwin, A. Olivier, D. Baillargeat, Adv. Funct. Mater. 22, 1385 (2012)

    CAS  Google Scholar 

  28. Y. Yu, C. Li, Y. Liu, L. Su, Y. Zhang, L. Cao, Sci. Rep. 3, 1 (2013)

    Google Scholar 

  29. S. Najmaei, Z. Liu, W. Zhou, X. Zou, G. Shi, S. Lei, B.I. Yakobson, J.C. Idrobo, P.M. Ajayan, J. Lou, Nat. Mater. 12, 754 (2013)

    CAS  Google Scholar 

  30. J.H. Sung, H. Heo, S. Si, Y.H. Kim, H.R. Noh, K. Song, J. Kim, C.S. Lee, S.Y. Seo, D.H. Kim, H.K. Kim, H.W. Yeom, T.H. Kim, S.Y. Choi, J.S. Kim, M.H. Jo, Nat. Nanotechnol. 12, 1064 (2017)

    CAS  Google Scholar 

  31. L.K. Tan, B. Liu, J.H. Teng, S. Guo, H.Y. Low, K.P. Loh, Nanoscale 6, 10584 (2014)

    CAS  Google Scholar 

  32. C.S. Tan, Y.J. Lu, C.C. Chen, P.H. Liu, S. Gwo, G.Y. Guo, L.J. Chen, J. Phys. Chem. C 120, 23055 (2016)

    CAS  Google Scholar 

  33. R.H. and Y.I.X. Gao, Y.H. Ikuhara, C.A. Fisher, H. Moriwake, A. Kuwabara, H. Oki, K. Kohama, R. Yoshida, Adv. Mater. Interfaces 1, 1400143 (2014)

  34. P.K. Petrov, B. Zou, Y. Wang, J.M. Perkins, D.W. McComb, N.M.N. Alford, Adv. Mater. Interfaces 1, 1 (2014)

    Google Scholar 

  35. P.E. Blöchl, Phys. Rev. B 50, 17953 (1994)

    Google Scholar 

  36. G. Kresse, D. Joubert, Phys. Rev. B Condens. Matter Mater. Phys. 59, 178 (1999)

    Google Scholar 

  37. J.P. Perdew, K. Burke, M. Ernzerhof, Phys. Rev. Lett. 77, 3865 (1996)

    CAS  Google Scholar 

  38. Z. Yu, Z.Y. Ong, S. Li, J.B. Xu, G. Zhang, Y.W. Zhang, Y. Shi, X. Wang, Adv. Funct. Mater. 27, 160493 (2017)

    Google Scholar 

  39. J.M. Suh, Y.-S. Shim, K.C. Kwon, J.-M. Jeon, T.H. Lee, M. Shokouhimehr, H.W. Jang, Electron. Mater. Lett. 15, 368–376 (2019)

    CAS  Google Scholar 

  40. B. Wang, C. Muratore, A. A. Voevodin, M. A. Haque, Nano Converg. 1, 22 (2014)

    Google Scholar 

  41. D. M. Andoshe, J. -M. Jeon, S. Y. Kim, H. W. Jang, Electron. Mater. Lett. 11, 323–335 (2015)

    CAS  Google Scholar 

  42. H. W. Shin, J. Y. Son, Electron. Mater. Lett. 14, 59–63 (2018)

    CAS  Google Scholar 

  43. F.-J. Zhang, C. Kong, X. Li, X. -Y. Sun, W. -J Xie, W. -C. Oh, J. Korean. Ceram. Soc. 56(3), 284–290 (2019)

    CAS  Google Scholar 

Download references

Acknowledgements

Not applicable.

Funding

This work was financially supported by National Research Foundation of Korea (NRF) funded by the Ministry of Science and ICT (2018M3D1A1058793, 2019M3E6A1103818, 2020M2D8A206983011, 2021R1A2B5B03001851). The Inter-University Semiconductor Research Center and Institute of Engineering Research at Seoul National University provided research facilities for this work.

Author information

Authors and Affiliations

  1. Department of Materials Science and Engineering, Research Institute of Advanced Materials, Seoul National University, Seoul, 08826, Republic of Korea

    Woonbae Sohn, Ki Chang Kwon, Jun Min Suh, Tae Hyung Lee & Ho Won Jang

  2. Energy Storage Materials Centre, Korea Institute of Ceramic Engineering and Technology, Jinju, 52851, Republic of Korea

    Woonbae Sohn & Kwang Chul Roh

  3. Advanced Institute of Convergence Technology, Seoul National University, Suwon, 16229, Republic of Korea

    Ho Won Jang

Authors
  1. Woonbae Sohn
    View author publications

    You can also search for this author in PubMed Google Scholar

  2. Ki Chang Kwon
    View author publications

    You can also search for this author in PubMed Google Scholar

  3. Jun Min Suh
    View author publications

    You can also search for this author in PubMed Google Scholar

  4. Tae Hyung Lee
    View author publications

    You can also search for this author in PubMed Google Scholar

  5. Kwang Chul Roh
    View author publications

    You can also search for this author in PubMed Google Scholar

  6. Ho Won Jang
    View author publications

    You can also search for this author in PubMed Google Scholar

Contributions

WBS carried out the STEM/EELS analysis and wrote of the full manuscript according to the journal’s instruction. KCK and JMS prepared materials and substrates for the procedures. THL carefully performed TEM specimen preparation. KCR and HWJ carefully revised the manuscript. All author perused and agreed to the final manuscript.

Corresponding authors

Correspondence to Kwang Chul Roh or Ho Won Jang.

Ethics declarations

Competing interests

The authors declare they have no competing interests.

Additional information

Publisher's Note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Supplementary Information

Additional file 1

: Figure S1. Raman spectra of the MoS2 thin film on the SiO2/Si substrate. Lateral growth of multilayer MoS2 film has been successful. The two characteristic Raman vibration modes E12g and A1g are labelled. Figure S2. TEM images of MoS2 film on SiO2/Si. (a) Low magnification, (b), (c) HRTEM images of AS-MoS2 film. (d) Low magnification, (e), (f) HRTEM images of TR-MoS2 film. Figure S3. (a) Position in which interlayer distance values are measured in AS-MoS2 films and (b) position in which interlayer distance values are measured in TR-MoS2 films. Figure S4. XPS spectra of MoS2 films. XPS core level spectra of (a) Mo 3d, (b) S 2p of AS-MoS2 film and (c) Mo 3d, (d) S 2p of TR-MoS2 films.

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creativecommons.org/licenses/by/4.0/.

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Cite this article

Sohn, W., Kwon, K.C., Suh, J.M. et al. Microscopic evidence of strong interactions between chemical vapor deposited 2D MoS2 film and SiO2 growth template. Nano Convergence 8, 11 (2021). https://doi.org/10.1186/s40580-021-00262-x

Download citation

  • Received:

  • Accepted:

  • Published:

  • DOI: https://doi.org/10.1186/s40580-021-00262-x

Keywords

  • MoS2
  • Large-scale growth
  • Chemical bonding
  • Electron energy loss spectroscopy