Open Access

Structural Properties and Phase Transition of Na Adsorption on Monolayer MoS2

Nanoscale Research Letters201611:330

Received: 1 June 2016

Accepted: 7 July 2016

Published: 15 July 2016


First-principles calculations are performed to investigate the structural stability of Na adsorption on 1H and 1T phases of monolayer MoS2. Our results demonstrate that it is likely to make the stability of distorted 1T phase of MoS2 over the 1H phase through adsorption of Na atoms. The type of distortion depends on the concentration of adsorbed Na atoms and changes from zigzag-like to diamond-like with the increasing of adsorbed Na atom concentrations. Our calculations show that the phase transition from 1H-MoS2 to 1T-MoS2 can be obtained by Na adsorption. We also calculate the electrochemical properties of Na adsorption on MoS2 monolayer. These results indicate that MoS2 is one of potential negative electrodes for Na-ion batteries.


First-principlesMoS2 Structural stabilityPhase transition


In recent years, the study of transition-metal dichalcogenides (TMDs) has been a topic of current interest due to their layered structure [1, 2]. TMDs exhibit a broad range of properties, which are advantageous for a wide range of applications as high-performance functional nanomaterials [3]. Among them, molybdenum disulfide (MoS2) has attracted considerable attention because of its important role in ultrasensitive photodetectors, flexible electronic device, lithium ion battery, field effect transistors, and sodium-ion batteries [47]. These applications show high figure of merit in microelectronics, thermoelectrics, and optoelectronics.

Bulk MoS2 crystal is an indirect-gap semiconductor, which is built up of atomic layers stacking by weak van der Waals force. It is possible to exfoliate MoS2 monolayer from the bulk, owing to the weak van der Waals interaction between these layers [8, 9]. The typical monolayers of TMDs come in two varieties, called H and T phase with trigonal or octahedral prismatic coordination, respectively [10]. Consequently, MoS2 monolayers come in two phases, called 1H-MoS2 and 1T-MoS2 [11]. The 1H-MoS2 phase has the space group of P6/mmc and is semiconducting with a direct band gap [12]. The 1T-MoS2 phase is metallic and metastable relative to the 1H-MoS2 phase [13]. However, stable 1T-MoS2 phase can be realized by doping of MoS2 with Re atoms [14] and be stabilized by adsorption of Li atoms [15].

Previous studies demonstrated the phase transition between 1H-MoS2 and 1T-MoS2 in the early lithiation process [1620]. The charge transfer induced by the adatoms leads to turn 1T-MoS2 phase into a stable MoS2 phase. The phase transition is the main issue for application in Li-ion batteries [20, 21] and Na-ion batteries [22, 23]. A large amount of experimental and theoretical works on the application of MoS2 in Li-ion batteries has emerged in the past years [1621]. Kan et al. [16] studied possible pathways of structural phase transition between 1H-MoS2 and 1T-MoS2 by increasing lithium adsorption concentration constantly. Esfahani et al. [18] calculated the H-T transition by adsorption of Li atoms on both sides of the MoS2 monolayer. Mortazavi et al. [22] investigated phase transition between 2H-MoS2 and 1T-MoS2 upon Na intercalation. Li-ion batteries are prime energy storage systems at present in amounts of devices used in our daily lives such as smartphones and laptops. Na-ion batteries are excellent alternatives to Li-ion batteries because of their lower cost and the greater availability. However, to our knowledge, there are few theoretical calculations on Na adsorption on monolayer MoS2.

In this work, we perform a comprehensive first-principles study of the electronic structure, adsorption energies, phase transitions, and electrochemical properties for Na-adsorption compounds. All reasonable structure phases of MoS2 monolayer are introduced. Our results suggest that it is easily to turn to be octahedral phases by Na-adsorption for 1T-MoS2, such as ZT-MoS2 with zigzag Mo-Mo chains and DT-MoS2 in rhombus-shape with Mo-Mo chains. Furthermore, Na adsorption on the MoS2 surface can lead to a structural phase transformation from 1H-MoS2 to an octahedral coordinated MoS2. Average operating voltages by Na adsorption are calculated. This will be helpful to understand the basic processes involved in monolayer MoS2 applied in Na-ion batteries.


Our calculations are carried out by using the Vienna Ab-initio Simulation Package (VASP) package [24], which is based on density functional theory (DFT) and plane-wave pseudopotential method. The electron exchange-correlation energy is described in the Perdew-Burke-Ernzerhof (PBE) form for the generalized gradient approximation (GGA) [25]. The cut-off energy is set to be 600 eV for the plane-wave expansion of the wave functions. The Brillouin zone integration is represented by the Monkhorst-Pack k-point scheme with 9 × 9 × 1 and 5 × 5 × 1 grid meshes for the (1 × 1) unit cell and (4 × 4) supercell, respectively. The criterion of convergence of energy is chosen as 10−5 eV between two ionic steps, and the maximum force allowed on each atom is 0.01 eV/Å. The vacuum space along the z direction is taken to be more than 15 Å for the both 1H-MoS2 and 1T-MoS2.

The geometry structures are shown in Fig. 1. A (4 × 4) supercell of MoS2 monolayer consisting of 48 atoms, which contains 16 Mo and 32 S, is made up of the primitive cell of MoS2. 1H-MoS2 has single S-Mo-S layer, where the Mo site in a trigonal prism coordination as shown in Fig. 1a. 1T-MoS2 has asymmetric sulphur atoms sites, where the Mo site in octahedral coordination as shown in Fig. 1b.
Fig. 1

a Top and side views of 1H-MoS2. b Top and side views of 1T-MoS2

Results and Discussion

Structural Properties

To obtain a clear insight into the 1H to 1T phase transition, we first calculate electronic structures of both the trigonal prismatic phase (1H-MoS2) and octahedral prismatic phase (1T-MoS2) by using (1 × 1) unit cell. Our results show that the optimized lattice parameters a 0 = 3.166 Å for both the pristine 1H-MoS2 and the pristine 1T-MoS2 as shown in Table 1.
Table 1

Structural parameters of 1H-MoS2 and 1T-MoS2 and band gap




a (Å)

Present work




3.16 [30]; 3.18 [11]

3.18 [10]

d S-S (Å)

Present work




3.089 [30]

Gap (eV)

Present work




1.71 [30]; 1.67 [11]


Electronic structure provides a clear insight into the difference of band structure between 1H-MoS2 and 1T-MoS2. The two phases show completely different electronic structures. Figure 2 shows the band structures of 1H-MoS2 and 1T-MoS2 without spin-orbit coupling. 1H-MoS2 is a direct semiconductor with both conduction band minimum (CBM) and valence band maximum (VBM) located at the K point. The band gap obtained from GGA-PBE calculations is 1.71 eV. However, the electronic structure calculation of the 1T structure shows that this polytype is indeed metallic in Fig. 2b. We also calculate the energy difference between 1H-MoS2 and undistorted 1T-MoS2 unit cell, which shows that the optimized 1H-MoS2 is more stable than the 1T-MoS2 by 0.84 eV. In normal conditions, although both polytypes of monolayer MoS2 have the same element constitution, 1H-MoS2 is more stable than 1T-MoS2. Besides, the equilibrium lattice constant of 1H-MoS2 is close to that of 1T-MoS2 according to Table 1.
Fig. 2

a Band structures of 1H-MoS2. b Band structures of 1T-MoS2

Adsorption Energies and Stability Analysis

In order to investigate the stability of the two structural phases with Na adsorption, the most stable configuration of an isolated Na atom adsorbed on (4 × 4) cell for the both structure phases is determined at first. Three different types of adsorption sites are introduced to determine the most stable position [26], including “t” site (top site directly above a Mo atom), t’ site (top site directly above an S atom), and “h” site (hollow site above the center of hexagons), respectively. Na atoms adsorbed at other positions can eventually relax into one of the three listed adsorption sites [27]. Considering the monolayer hexagonal lattice structure of MoS2 monolayer, it is reasonable to expect the relaxation of foreign atoms on one of these adsorption sites. There is little change for the adsorption geometry of 1H-MoS2 after relaxation. However, the optimized 1T-MoS2 supercell will transform into the distorted 1T phase duo to its instability, such as ZT-MoS2 with zigzag Mo-Mo chains. Further, to investigate the relative stabilities of the systems, we defined the adsorption energy as follows:
$$ {E}_a=\left({E_X}_{-\mathrm{M}\mathrm{o}\mathrm{S}2}+{E}_{\mathrm{Na}}\right)-{E}_{\mathrm{total}}^x $$
where X = 1H, distorted 1T, \( {E}_{X-\mathrm{M}\mathrm{o}\mathrm{S}2} \) represents the total energy of 1H-MoS2 and distorted 1T-MoS2 system, \( {E}_{\mathrm{total}}^x \) represents the total energy of the adsorption system, and \( {E}_{\mathrm{Na}} \) represents the total energy of bulk sodium. The electron configurations of adatom adsorption energies (\( {E}_a \)) and structural properties for single adatom-adsorbed MoS2 obtained from our calculations are listed in Table 2. Our calculated results show that the adsorption energy is different for different sites. In all adsorption sites, the site with the largest adsorption energy (minimum total energy) is referred to as the favored one. Comparing the possible sites of h, t, and t’, we found that Na atom prefer to reside on t site for the both structures.
Table 2

Adsorption energy, distance between Na and S atoms, the bond length of Mo-Mo



E a (eV)

d Na-S (Å)

d Mo-Mo (Å)














Distorted 1T-MoS2













Phase Transition of 2D MoS2 Monolayer Induced by Na Insertion

In the previous analysis, we have determined the most stable adsorption site for Na atoms on the surface of MoS2 monolayer, which is top of Mo atom sites. Totally, there are 32 most stable sites for Na atoms on both sides of (4 × 4) MoS2 supercell [28]. In order to investigate systematically Na adsorption on the surface of MoS2 monolayer, we introduce Na atoms on both sides of MoS2 monolayer forming the compound 1H-Na x MoS2 and 1T-Na x MoS2 to induce phase transition, which is a solvent-based exfoliation of MoS2 monolayer and a typical procedure for both the charge/discharge processes in battery.

The geometries of 1H-Na x MoS2 are optimized with adsorption concentration increasing, as shown in Fig. 3. Our results show the variation of energies and structure for 1H-Na x MoS2 with the increasing of Na concentrations. As shown in Fig. 3, Mo-Mo chains appear in 1H-Na x MoS2 when 2~6 Na atoms are added to the system. Triangular Mo-Mo clustering appears in 1H-Na x MoS2 with the increasing of adsorption concentrations.
Fig. 3

The optimized structures of the most stable 1H-Na x MoS2, triangular Mo-Mo clustering as highlighted in red

The optimized geometries of 1T-Na x MoS2 with the increasing of adsorption concentrations are shown in Fig. 4a. The substrate structure of 1T-MoS2 directly transits to the ZT-MoS2 after relaxation due to the instability. Some Mo-Mo chains appear in 1T-Na x MoS2 following certain rules. These Mo atoms gradually form a diamond-like chain up to eight Na atoms that are introduced in the system. The system is likely to maintain the diamond chain structure. The geometry configurations of ZT-MoS2 and DT-MoS2 without adsorption are clearly shown in Fig. 4b, c, respectively. The free-standing 1T-MoS2 exhibits metallic property and is metastable. Both ZT-MoS2 and DT-MoS2 belong to distorted octahedral coordinated MoS2.
Fig. 4

a The optimized structures of the most stable 1T-Na x MoS2, diamond-like Mo-Mo clustering as highlighted in red. Distorted octahedral coordinated MoS2: b ZT-MoS2: zigzag-like Mo-Mo chains, c DT-MoS2 diamond-like Mo-Mo chains

It is similar to the definition of adsorption energy that the formation energy in different concentrations of Na absorption is calculated using the expression:
$$ {E}_{f(x)}={E}_{\left(X-\mathrm{N}\mathrm{a}x\mathrm{M}\mathrm{o}\mathrm{S}2\right)}-{E}_{\left(X-\mathrm{M}\mathrm{o}\mathrm{S}2\right)}-n{E}_{\left(\mathrm{N}\mathrm{a}\right)} $$
where X = 1H, 1T, \( {E}_{\left(X-\mathrm{N}\mathrm{a}x\mathrm{M}\mathrm{o}\mathrm{S}2\right)} \) is the total energy of the X-Na x MoS2 compound, \( {E}_{\left(\mathrm{M}\mathrm{o}\mathrm{S}2\right)} \) is the total energy of the same MoS2 polytype, and \( {E}_{\left(\mathrm{N}\mathrm{a}\right)} \) is the total energy of bulk sodium. A negative binding energy indicates an exothermic chemical interaction between Na and MoS2. Relative formation energy per Na atom of 1T-Na x MoS2 with respect to 1H-Na x MoS2 varies as increasing the Na-adsorption concentration constantly in Fig. 5. The 1H-Na x MoS2 still keeps stability in the low adsorption concentration. However, the 1T-Na x MoS2 becomes more stable than 1H-Na x MoS2 when the adsorption concentration of Na atoms exceeds about 35 %. As the adsorption concentration of Na increases, the 1T-Na x MoS2 will become stable further.
Fig. 5

Relative formation energy per Na atom of 1T-Na x MoS2 with respect to 1H-Na x MoS2 as a function of Na concentration

Transition Barrier from 1H Phase to 1T Phase

The procedure of transition can be viewed as a shift of one S atom layer in the 1H-MoS2 structure to the position h in Fig. 1a. Therefore, the barrier energy of 1H-MoS2 structure to 1T-MoS2 structure transition is able to be calculated by shearing one S layer from the 1H structure toward the 1T structure when fixing the Mo atoms, while the other atoms are allowed to relax. Nudged Elastic Band (NEB) method is adopted to calculate the barrier energy from 1H to 1T structure transition as shown in Fig. 6a. Our results show that the barrier of phase transition from 1H to 1T structure is approximately 1.61 eV in the absence of external adatoms. The phase transition involves one of the S atoms moving from one pyramidal position to the other pyramidal position. The relative energy of Na-intercalated 1T-MoS2 is 0.52 eV. Meanwhile, the barrier from 1H-MoS2 to 1T-MoS2 reduces to 0.91 eV when Na atoms are adsorbed completely on one side of MoS2 monolayer. The barrier energy reduces considerably from 1H to 1T structure transition by the Na atom adsorption on MoS2 monolayer. These results suggest that the Na atoms are not only effective to make the 1T-MoS2 energetically favorable but also play an important role in the process of phase transition. According to our theoretical calculation and experimental works, we summarize the pathways for structural phase transition among different structures in Fig. 6b. The detailed process is the following: (1) When Na atoms are adsorbed to 1H-MoS2, the 1H-MoS2 remains stable until the Na concentration reaches 35 %. When more Na atoms are adsorbed on both sides of MoS2 monolayer, the distorted 1T-MoS2 will become more stable. Besides, the structure finally transform to the distorted 1T-MoS2 phase with diamond-like chains. (2) When all of the Na atoms are extracted from the system, the structure will become ZT-MoS2. (3) The ZT-MoS2 will transform back to 1H-MoS2 phase by heating or aging.
Fig. 6

a Evolution of the energy per S atom for 1H to 1T structure transition as a function of the reaction coordinate, for pure and Na-covered MoS2. b The pathways of structural phase transition of Na adsorption on monolayer MoS2

Electrochemical Properties of Na x MoS2

In order to inspect the suitability of Na x MoS2 compound as an electrode material for Na-ions, we calculate the average adsorption voltage. The electrode potential between Na x1MoS2 and Na x2MoS 2 (x 2 > x 1) is calculated as [29]:
$$ \overline{V}=-\frac{G_{x_2}-{G}_{x_1}-\left({x}_2-{x}_1\right){G}_{Na}}{\left({x}_2-{x}_1\right)e} $$
where \( {G}_{x_2} \) and \( {G}_{x_1} \) are the total energies of Na x MoS2 systems and \( {G}_{\mathrm{Na}} \) is the energy per atom of Na in its bulk state. The electrode potential for 1H-Na x MoS2 and 1T-Na x MoS2 as the change of concentration is shown in Fig. 7, respectively. Our results show that the voltage profile for 1H-Na x MoS2 varies with a decreasing trend in a range of 0~1 V as shown in Fig. 7a, with an average value of 0.72 V. The electrode potential for 1T-Na x MoS2 varies in a range of 0~3.5 V as shown in Fig. 7b. However, 1T-Na x MoS2 systems are unstable for concentrations x < 0.35, as shown in Fig. 5. Therefore, the large magnitudes of the potential of 1T-Na x MoS2 compounds for low concentrations are unlikely to use practically. Our results show that the average potential of 1T-Na x MoS2 is obtained approximately as 1.28 V. Compared with Li-intercalated MoS2, the average potential of Na x MoS2 is much lower because of the weaker binding of Na atoms. Since ideally a good anode should have a low electrode potential, our calculated voltage profile suggests that layered MoS2 is suitable as an anode for an NIB. When this Na-intercalated MoS2 anode is combined with high-capacity cathode materials such as Na3MnPO4CO3, the Na-ion battery cell can yield a desirable open circuit voltage in the range of 2.5~3.5 V.
Fig. 7

Electrode potential of Na-intercalated a 1H-MoS2 and b 1T-MoS2


In conclusion, we investigated the adsorption energies, phase transition for the adsorption of Na onto MoS2 monolayer, and electrochemical properties of Na x MoS2 by using the first-principles DFT method. The traditional trigonal prismatic 1H-MoS2 phase is stable under normal conditions. However, a comprehensive study of the relative phase stability of MoS2 tells us that the other structural phase transition can be stable by adsorption. Our results show that some triangular Mo-Mo clustering appears in 1H-Na x MoS2 with the increasing of Na-adsorption concentration. On the other hand, some diamond-like Mo-Mo chains appear in 1H-Na x MoS2 when the Na-adsorption concentration is beyond 25 %. What is more, the adsorption of Na on MoS2 induces a phase transformation at x = 0.35 from the 1H to 1T phase. Our calculated results show that the adsorption of Na onto MoS2 monolayer results in a lower energy barrier from 1H to 1T-MoS2. Finally, Na x MoS2 compound is likely to become a battery anode material with a low average electrode potential of 0.72~1.28 V.



This work was supported by the National Basic Research Program of China (973 Program) under Grant No. 2014CB643900, the Open Fund of IPOC (BUPT), the Open Program of State Key Laboratory of Functional Materials for Informatics, the National Natural Science Foundation of China (No. 61404153), and the Shanghai Pujiang Program (Grant No.14PJ1410600). P.F. Guan acknowledges the computational support from the Beijing Computational Science Research Center (CSRC).

Authors’ Contributions

HH carried out the calculations and HH and PFL wrote the manuscript. LYW, CFZ, YXS, and SMW helped in the discussions and analysis of the results. PFL and PFG proposed the initial work, supervised the analysis, and revised the manuscript. All authors read and approved the final manuscript.

Competing Interests

The authors declare that they have no competing interests.

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

Authors’ Affiliations

State Key Laboratory of Information Photonics and Optical Communications, Ministry of Education, Beijing University of Posts and Telecommunications, Beijing, China
Beijing Computational Science Research Center, Beijing, China
State Key Laboratory of Functional Materials for Informatics, Shanghai Institute of Microsystem and Information Technology, Chinese Academy of Sciences, Shanghai, China
Photonics Laboratory, Department of Microtechnology and Nanoscience, Chalmers University of Technology, Gothenburg, Sweden


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