Improving the capacity and efficiency of the Hydrogen Evolution Reaction (HER) is an enduring challenge of green energy production and artificial photosynthesis1,2. Still, while HER in organisms evolved with time and increasing complexity, artificial HER aims to replicate the same with minimalism and simplicity. A cornerstone of the challenge is to mimic the function of natural hydrogenase enzymes, which catalyse HER in living systems. Indeed, it can be seen that without a catalyst like hydrogenase, HER does not proceed with the speed required for practical applications3,4. However, hydrogenases can be difficult to extract and purify, and can denature under non-natural operations5, consequently, inorganic alternatives are used for most applications. The most common example of this is platinum (Pt), which has served as the benchmark catalyst for HER due to its high catalytic efficiency6,7,8. Nevertheless, because of the scarcity and cost of Pt, a more abundant alternative is needed for cost-effective implementation.

For this, MoS2, an earth abundant lamellar solid, has shown prominent HER catalysis nearing the efficiency of platinum9,10. However, experiments using MoS2 grown on Au(111) indicated that this material is only catalytic on its edge sites9. Theoretical studies corroborated these results with the Gibbs free energy of hydrogen adsorption (ΔGH), a measure of HER efficiency, to be feasible for catalysis only at MoS2 edges11,12; the basal plane of MoS2 does not appear to participate in catalysis, meaning the bulk of material is catalytically inert. Consequently, the maximization of MoS2 edges and mimicry of the edge structure has become a significant topic13,14,15,16.

Interestingly, recent studies have begun to show enhancement of MoS2 catalytic efficiency following lithium intercalation and exfoliation17,18,19. The Tafel-slope of these sheets, a benchmark of electrochemical efficiency against applied overpotential, is nearly twice that of natural MoS2 after lithium treatment17,18,19. As the lithium-exfoliation reactions increase the availability of basal plane surfaces but not edges, the catalytic improvements are postulated to be basal plane related. Nonetheless, because the basal plane structures of lithium-exfoliated monolayers, and indeed, many two-dimensional sheets, are difficult to characterize20,21,22, the post lithiation and exfoliation structure of MoS2 remains nebulous and historically controversial, rendering the origin of this catalytic enhancement correlatively vague. To briefly recount a history of the structural understanding of MoS2 exfoliated with the assistance of lithium, it can be seen that a structural change in Li-intercalated MoS2 has been reported as far back as 1973 (ref. 23), nevertheless, interpretations of the final structure vary significantly in the literature. For example, in 1973, Somoano et al.23, observed extensive layer displacements after intercalation, suggesting the resulting product is a mixture of disordered compounds. However, in 1983, Py et al.24 reported the alkali metal exfoliated structure to be crystalline, with a first order phase transition from the natural trigonal prismatic (2H) to an octahedral (1T) phase. In 1989, a significant distortion to a 2ao × 2ao lattice was reported by Chrissafis et al.25 In 1991, an octahedral structure was observed by Jimenez et al. and Qin et al., but a small distortion was noted, making the final crystal a 2ao × ao super lattice26,27. Atomic force microscopy images obtained in 1993, by Schumacher et al., though, indicated no distortion or superlattice28. In 1998, Dungey et al. observed a 2ao × 2ao lattice with trigonal Mo clustering29, but in 1999, a 2ao × ao superlattice was seen by Heising et al., with severe distortion and formation of infinite Mo-zig-zag chains30. A chain-of-diamonds motif was suggested by Petkov et al. in 2002 (ref. 31), but most recently, in 2013, Maitra et al. reported a distortion-free octahedral phase32. Chhowalla and coworkers observed similar variations, from a perfect octahedral phase with natural 2H MoS2 domains33, distrted phases19, coexistence of various phases34, and also, a perfect octahedral phase35. Surprisingly, we note that the changed structures are almost always referred to as 1T, regardless of polymorphic structural differences. It is therefore not surprising to see recent catalytic improvement being attributed to varied structures, including octahedral17,18,32, and distorted Mo phases36,37. Part of the confusion is likely a simple consequence of incomplete transformation resulting in identification of partially transformed and transitional states due to variations between batches, however, there may be underlying issues of stability as well, making the resultant structure, and indeed, structural based predictions of its catalytic effectiveness difficult to handle38.

To address these long-standing issues and shed light on the catalytic origin of the transformed crystals, here we take a combined experimental/theoretical approach using controlled processing conditions to achieve stable phases and density functional theory calculations to investigate the stability of these polymorphs. With the solution processing advantages of these materials39,40,41, we report the catalytic efficiency of HER in homogenous reactions, with experimental H2 yield of these phases, and corroborate them with calculated ΔGH. The analysis was then extended from MoS2 to WS2 to show similarly distorted crystal phases and basal plane catalytic activation.


Exfoliation and phase transformation of MoS2

A typical lithium-exfoliation reaction consisted of immersing MoS2 powder in n-butyl lithium (1 M) for 72 h at room temperature31,33,42. The intercalated compound was then transferred to water and sonicated to yield exfoliated monolayers. After purification using centrifugation and dialysis, concentrations and purity of each batch were measured using Flame Atomic Absorption Spectrophotometry. Samples were then visualized using abberation-corrected scanning transmission electron microscopy.

As seen in Fig. 1, a typical sheet exfoliated using this method indeed yields a mixed phase (shown without false colouring in Supplementary Fig. 1). First, a trigonal prismatic (2H) phase that corresponds with an untransformed basal plane can be seen with symmetrical Mo–Mo spacing of 2.98±0.05 Å. Second, an octahedral phase with displaced sulfur atoms and symmetrical Mo arrangements (2.95±0.06 Å) is seen, albeit in small quantities. Last, large swatches of a visually distinct, tertiary phase is also present, with Mo atoms asymmetrically clustered to form one-dimensional lines of alternating light-and dark stripes. In this phase, Mo–Mo distances of 3.55±0.16 Å and 2.92±0.16 Å were measured. On the basis of the above, we thus conclude that within one individual sheet, a microcosm of various phases are present, with each representing differing interpretations in previous work. Nevertheless, as the stability of each phase should be an intrinsic consequence of the energetics of distinct atomic arrangements, we sought to understand the relative stabilities of each phase. Because it was previously reported that materials revert back to the natural 2H phase42, we reasoned that the 2H is the overall energetic minimum, with the other polymorphs occupying differing metastable points in relation to the 2H.

Figure 1: Polymorphism and incomplete transformations.
figure 1

Polymorphisms within the basal plane exhibit coexistence of three different phases, 2H (trigonal prismatic, false coloured as red), 1T (octahedral, false coloured as blue) and 1T′ (clustered Mo, false coloured as green). Scale bar, 5 nm.

To better define this, we employed Density Functional Theory (DFT) to independently predict the structures of possible polymorphs (see Supplementary Information for computational details). As can be seen in Table 1, a total of four polymorphs were predicted based on structural optimization of unit cells. The first two, consisting of 1 × 1 unit cells, were the 2H trigonal prismatic phase and the 1T octahedral phase. In addition, a distorted phase with zig-zag chains consisting of a 2 × 1 supercell and a phase with Mo–Mo atoms clustered into trimerized pockets in a 2 × 2 supercell were predicted. We dub the two later phases, 1T′ and 1T′′, respectively.

Table 1 Structural polymorphs of MoS2 and summary of parameters as predicted by Density Functional Theory.

Next, the stabilities of each DFT polymorph were calculated. It can be seen that the symmetrical 1T representation has the least stable ground-state (+0.82 eV versus 2H). Indeed, in a 2 × 2 or 4 × 4 supercell, we find the 1T phase eventually relaxes into 1T′′, which is second in stability, at +0.63 eV, conforming with the dynamical phonon instability previously predicted in the 1T phase38. Nevertheless, the 1T′ phase was significantly more stable than 1T and 1T′′ (+0.55 eV versus 2H), with a barrier against 2H reversion of 0.73 eV f.u.−1 (formula unit, Supplementary Fig. 2, Supplementary Table 1). By the DFT calculations, the transformed portions within a sample, if allowed to reach metaequilibria, should therefore preferentially form 1T′ instead of the other polymorphs.

To investigate these results experimentally, we prepared samples to induce equilibria by extending the lithium intercalation period. As seen in Fig. 2a, a preferential transformation to 1T′ is possible on the entirety of the basal plane. This therefore suggests that the various polymorphs observed previously are likely consequences of incomplete reactions, such as partial intercalation, with parts of the basal plane yet to undergo sufficient conversion to the 1T′. Indeed, we have observed that when intercalation times are extended from 72 to 240 h, a complete transformation to the 1T′ can be achieved (Supplementary Fig. 3).

Figure 2: Basal plane transformations.
figure 2

(a) MoS2 basal plane showing preferential transformation to 1T′ with increased lithiation, in accordance with the calculated relative stability of the metastable phases. (b) On electron beam illumination, the basal plane exhibits a restoration to a symmetrical Mo arrangement indicative of 2H reversion. (c) Sequential frames taken 60 s apart, showing phase evolution under the electron beam. Electron dose rate was 2,800 e Å−2 s−1, with each frame requiring 40 s to capture. (d) An electron dosed region with sulfur atoms resolved, demonstrating 1T′ to 2H phase reversion after illumination.

Given the DFT prediction of 1T′ as a metastable phase, we examined the ability to covert 1T′ back to 2H under electron beam-illumination. As shown in Fig. 2c, sequential frames taken at 60 s intervals (acquired at 40 s/frame at an electron dose rate of 2,800 electron Å−2 s−1) show gradual relaxation of Mo atoms from 1T′ lines to symmetrical 2H spacing. A detailed investigation of the structures again showed the 1T′ phase with Mo spacings of 3.55 Å and 2.92 Å, and the relaxed structure displayed trigonal prismatically coordinated sulfur atoms with Mo–Mo spacing of 2.95 Å, in agreement with the 2H structure (Fig. 2d). These results corroborate the 1T′ as the energetically preferred metastable phase that will relax back to 2H when energetic input, for example, heat, exceeds that of the metastable barrier energy. It further suggests that the partial or incomplete phase transformations observed previously may be due to energetic conditions reverting the material to 2H during the characterization process. Supplementary Fig. 4 shows the final product of 1T′ heated under inert atmosphere is a 2H lattice. These observations support previous electrical characterizations of the material33,42 with 1T′ having greatly reduced resistivity compared to 2H (calculated bandgap of 0.01 and 1.7 eV, respectively, shown in Table 1).

To corroborate the above, High-angle annular Dark-field (HAADF) images were simulated using coordinates from DFT. As seen in Fig. 3, good agreement was seen between experiment and simulations. We note in samples that are predominantly 1T′ (Fig. 2a), lines modulated in two-dimensions can be seen at intersections of 1T′. This may be interpreted as the 1T′′, however, its occurrence is very localized and defective (<5%), and consequently, not of practical significance.

Figure 3: Different possible phases for MoS2.
figure 3

(a) Simulated and experimental images of different possible phases for MoS2. FFT mask filters have been employed for clarity. (b) line scan comparisons between 2H and 1T using the simulated and experimental images, showing modulation of sulfur contrast.

Dye-sensitized HER

Following these structural insights, HER catalysis of these MoS2 polymorphs was examined. For this, we measured H2 formation using MoS2 in a homogenous photocatalysis reaction. In a typical reaction, a solution of MoS2 was sensitized with Eosin Y (EY), and Triethanolamine (TEOA) was added as a sacrificial electron donor43,44. The reaction mixture was then purged of atmospheric gasses, and irradiated with a xenon lamp tuned to 1 sun. The flow entering and exiting the reaction flask was then monitored on a gas chromatograph to quantify H2 formation inside the flask.

The reaction proceeded via photoexcitation of EY and subsequent intersystem crossing to yield a triplet excited state (EY3*). Acceptance of an electron via reductive quenching from the sacrificial electron donation (TEOA) then yields a radical EY32,43,45,46,47. The highly reductive EY can then reduce a proton to form H0, return the electron to an oxidized TEOA, or transfer the electron to another catalyst such as the MoS2. As seen in Fig. 4a, in the absence of MoS2, direct reduction of protons by radicalized EY occurs by collisional reductive quenching with TEOA (Supplementary Fig. 5), and generates a peak H2 flux of 150 nmol min−1. Over the course of 100 min, a yield of 7.5 μmols was observed, giving a typical activity of 4.5 μmol h−1 (Fig. 4b). Sequential addition of 1T′ (for example, ‘fully transformed MoS2’) gradually raised the peak flux, until saturation was reached with 40 p.p.m. of MoS2, yielding a peak flux of 620 nmol min−1. With the latter reaction, 40 p.p.m. of MoS2 raised overall yield to 30 μmol in the first 100 min, giving a typical activity of 18 μmol h−1, which is four times higher than the autocatalytic EY dye under the same conditions43. In both cases, addition of small amounts of HCl regenerates a stopped reaction, suggesting reaction termination is due to proton depletion (Supplementary Fig. 6).

Figure 4: Hydrogen evolution.
figure 4

With dye sensitization (eosin Y, EY), MoS2 can be used to conduct homogenous hydrogen evolution reactions in solution. (a) Real time H2 flux at incremental MoS2 concentrations. Diminished reactions are indicative of proton exhaustion, and can be restarted with acid addition. (b) Corresponding cumulative H2 yield (For a and b note key bottom left). (c) Incremental concentration of MoS2 and correlative overlay of cumulative H2 yield (black) with fluorescence quenching of dye (red) in solution. (d) fluorescence decay of eosin Y, (e) reaction saturated with eosin Y and MoS2 showing similar decay, indicative of static-quenching and ground-state complex, and (f) collisional quenching between TEOA and eosin Y resulting in second order decay and attenuated lifetime. Error bars denote s.d.

Given the boosted HER performance, it reasons that in the presence of fully transformed MoS2 a preferential charge transfer occurred between the radical EY and the MoS2. Indeed, with the reductive potential of EY at −0.8 V versus normal hydrogen electrode (NHE), and MoS2’s conduction band situated at 0.2 V versus NHE, such a transfer is feasible48,49. To support this, the charge transfer was examined using fluorescence quenching correlations between EY and the Li-exfoliated MoS2 (Fig. 4c). It can be seen that the fluorescence quenching interactions between EY and MoS2 are predictive of the eventual H2 yield, with both curves rising to saturation in the presence of 40 p.p.m. of MoS2. The fluorescence quenching following a saturation reaction fitting, vis-à-vis a continual diminishing of fluorescence with increasing quencher concentration (for example, collisional quenching) indicates the formation of a ground-state complex between EY and lithium-exfoliated MoS2, facilitating effectual charge transfer. To further elucidate these interactions, we monitored the excited state interactions via fluorescence decay. As seen in Fig. 4d, the fluorescence lifetime of a singlet excited EY, in the absence of secondary interactions, is 1 ns. However, interactions with reductive quenchers, such as TEOA, via collisional quenching results in fluorescence lifetime shortening that fits a two exponential decay (Fig. 4e)50. Interactions between EY and MoS2 did not follow this behavior. Instead, the lifetime of EY was maintained at 1 ns (Fig. 4f), while the fluorescence intensity was attenuated by 75% at saturation. This indicates adsorption of EY onto MoS2 to form a non-fluorescent ground-state complex that facilitates charge transfer within the complex with an excited state lifetime following the behavior of the 25% minority free dyes50.

As the above were performed with the fully transformed 1T′, effect of partial 1T′ transformation was then investigated. Here, two additional MoS2 batches with diminishing 1T′ transformation were used in identical reactions. As shown in Fig. 5a, the MoS2 batches with diminished 1T′ transformation yielded significantly less H2. Indeed, it can be seen that H2 yield scaled proportionately with 1T′ signatures, which dominates the basal plane of the exfoliated sheets (Supplementary Fig. 7, Supplementary Table 2). Given that 1T′ has shown empirical evidence of improved electrical conductivity, it is therefore possible that the improved catalysis seen with the ‘fully transformed MoS2’ is a consequence of better electron conduction from the EY charge transfer site to the catalytic sites of MoS2. However, it is also possible that the 1T′ transformation fundamentally alters the catalytic mechanism of the MoS2 sheets, possibly giving additional active sites for catalysis.

Figure 5: Energetics of Hydrogen Evolution.
figure 5

(a) Cumulative H2 yield with MoS2 undergoing differing degrees of 1T′ transformation. (b) DFT calculated Gibbs free energy of hydrogen adsorption (ΔGH) as a function of H coverage. (c) DFT calculated stability of the MoS2 structures per Mo atoms as a function of H coverage. As the H coverage exceeds 0.4, the stability of the 1T′ phase (red dashes) surpasses that of the 2H (black dots). (d) Free-energy diagram of hydrogen evolution reaction at 1/2 and 1/4 H coverage, with 1T′ MoS2 basal plane, 2H MoS2 edge on graphene and 2H MoS2 on Au(111) as reference. (e) Structural representation of 1T′ at 1/2 H coverage.

To investigate, we calculated, via DFT, the free energy of hydrogen adsorption (ΔGH), for the basal plane of each polymorph. From previous reports, it is known that |ΔGH|≈0 describes an optimal adsorption condition for catalysis10. Significant deviation in the exothermic direction (ΔGH<0) can indicate irreversible adsorption, consequently, an efficient catalyst such as the 2H MoS2 edge site, tends towards being slightly endothermic (ΔGH>0). From our calculations, ΔGH for the 2H basal plane is >+1.6 eV regardless of the H coverage and the absorption site. As a result, the adsorption of H on the 2H basal plane is strongly unfavorable. This is consistent with the 2H surface being catalytically inert9. However, when the basal plane is converted to 1T′, the hydrogen binding energy becomes negative (adsorption occurs). As seen in Fig. 5b, the free energy of adsorption here for 1T′ MoS2 is reasonably close to the optimum value of 0 eV (ref. 12), emerging at ΔGH=0.13 eV at 1/16 coverage and growing to 0.25 eV as H coverage increased to 1/2. This indicates that the 1T′ transformed surface is amenable for catalysis, and indeed, the HER improvements with 1T′ fraction is due to catalytic activation of the MoS2 basal plane. Most interestingly, we also observe adsorption of hydrogen to stabilize the 1T′. Indeed, Fig. 5c shows that when H coverage exceeds 0.4, 1T′ becomes more stable than 2H. As significant benchmark work with 2H MoS2 was performed with Au (111) supports9, we compare 1T′ with 2H Mo-edge sites, when supported on gold. It can be seen here that |ΔGH| on the 1T′ basal plane is comparable to the 2H Mo-edge supported on Au (111) and graphene at 0.25 coverage and slightly outperforms Mo-edges on Au (111) at 0.5 coverage (Fig. 5d,e)51. Above all, the shear increase in surface area availability after exfoliation to monolayers (100–1,000-fold greater than bulk solids)52 renders the basal plane improvements even more significant.

As WS2 can undergo analogous phase transformations, its catalytic efficiency was similarly analyzed. We show in Supplementary Fig. 8, the H2 flux with WS2 was a third lower than MoS2. For peak H2 flux, WS2’s 400 nmol min−1 showed approximately threefold improvement over controls, but weaker than the 750 nmol min−1 observed for MoS2. Similarly, H2 yield with WS2 was 18 μmol at t=100 min, which is 33% lower than MoS2. As fluorescence lifetime measurements revealed an analogous molecular charge transfer pathway, the reduced HER efficiency was thus indicative of WS2 being a less efficient catalyst. From Fig. 5b, it can be seen that the ΔGH of 1T′ transformed WS2 was 0.15 to 0.2 eV higher than MoS2. Nevertheless, this value represents a 10-fold reduction over ΔGH of 2H WS2, indicating catalytic activation of the basal plane comparable to MoS2.


We investigated the structure of MoS2 exfoliated with lithiation intercalation and directly correlated the varying physical structures to the catalytic origin for HER. Particularly, we demonstrated via abberation-corrected scanning transmission electron microscopy that modulated lithiation can lead to complete 1T′ transformation in the basal plane, and corroborated the experimental findings with DFT calculated phase stabilities. It was shown that the Mo atoms of MoS2 became asymmetrically spaced with increased lithiation, thus forming the 1T′ phase. In DFT, the 1T′ was shown to be energetically favorable compared to other possible polymorphs. Nevertheless, external perturbations within the environment, including electron imaging parameters, can induce a reversion to 2H.

With regard to catalysis, we have shown that the 1T′ transformation rendered the normally inert basal plane amenable towards hydrogen adsorption and H2 evolution. Indeed, ΔGH on the basal plane of 1T′ MoS2 showed catalytic activation and was lowered from +1.6 eV in the 2H to +0.18 eV. Moreover, when H coverage became >0.4, DFT showed 1T′ phase stability surpasses that of 2H. To put this in perspective, the ΔGH of 0.18 eV is comparable to 2H MoS2 edges on Au(111), one of the most active HER catalysts yet characterized. This makes the 1T′ MoS2 a state-of-the-art catalyst. In addition, as exfoliation to monolayers increases the surface area by as much as 1,000-fold52,53, the basal plane activation provides non-trivial increases in catalytic efficiency compared with the edge only catalysis of the 2H (refs 9, 15). We demonstrate this by H2 evolution studies in basic solution (pH 11), via self-assembled photocatalytic charge transfer complexes for HER. Here it can be seen that MoS2 catalysts can boost H2 yield of the HER catalytic dye, EY, by fourfold. Moreover, MoS2 itself does not fatigue over the course of the reaction. A clearer understanding of these materials, and the underlying relationship between structure, properties and performance, provides a pathway towards quantitative engineering of MX2 to enable the emerging ‘green energy’ economy.


Lithium intercalation and exfoliation

For MoS2, lithium intercalation was accomplished by immersing 1 g of MoS2 powder in 10 ml of 1 M n-butyl lithium. The mixture was stirred vigorously in an inert atmosphere glovebox for 3 to 10 days. After, the compound was washed over three layers of Whatman filter paper (#51, ashless) with 200 ml of hexane and then collected in a bottle. Three hundred millilitres of H2O was then added, and the mixture was sonicated for 3 m to extricate the intercalated MoS2 powder from the filter paper. The filter paper was then removed from the bottle, and the solution was sonicated for an additional 1.5 h. Unexfoliated portions were removed with centrifugation at 100 g for 3 min. The supernatant was then collected, and purified by centrifugation and washing with H2O (3 × 10,000 g for 1.5 h, followed by resuspension in water after each centrifugation cycle). The solution was then transferred in to a dialysis bag (Fisher Scientific, MW 5,000), and dialysed against running water for 3 days. The solution was then again centrifuged at 500 g for 15 m to remove aggregates, and the resultant samples were used as is. For WS2, Li intercalation was performed at 100 °C in a Parr bomb. Exfoliation and purification of WS2 was the same as MoS2. Atomic force microscopy images of exfoliates sheets are shown in Supplementary Fig. 9.

STEM microscopy and analysis

A FEI Titan G2 80–200 S/TEM with a Cs probe corrector operated at 200 kV was used in this study. High-angle annular dark-field (HAADF) S/TEM images were acquired with an electron probe size of 0.8 Å, convergence angle of 18.1 mrad, and current of 100 pA with an annular detector with a collection range of 60–160 mrad. The high resolution HAADF images were typically taken at 1,800 k magnification, yielding a pixel size of about 0.23 Å or a frame size of 48 × 48 nm for 2,048 × 2,048 pixels per frame. Such conditions gave rise to an equivalent electron dose rate of 2,800 electrons Å−2 s−1. Acquisition of the HAADF image (frame of 2,048 × 2,048 pixels) took 40 s at a dwell time of 10 μs/pixel. In sub-figures of Figs 1, 2 and 3, the filtered images were obtained by Fast Fourier transformation (FFT) of the HAADF images into reciprocal space, forming FFT patterns. Reciprocal spots from the patterns (typically {100} type reflections) were selected, masked with a 60 pixels filter, and then transformed into real space with inverse FFT. Gatan Digital Micrograph was used for the image processing. Additional details on TEM imaging and simulation are shown in Supplementary Methods

Computational details

All density functional calculations were carried out using the Vienna ab initio simulation package54 with plane wave basis set and projector augmented-wave pseudopotentials55. All energies were calculated with Perdew–Burke–Ernzerhof exchange-correlation potentials56. For selected structures, we applied the hybrid HSE06 functional57 to calculate the electronic band gap. The MoX2 (X=Mo,W) monolayers were modeled using surface supercells separated in the periodic direction by a 20 Å-thick vacuum slab. We applied a plane wave energy cutoff of 600 eV and Γ-centered 24 × 24 × 1, 12 × 24 × 1, 12 × 12 × 1, and 6 × 6 × 1 k-points grids for Brillouin zone sampling of the 1 × 1 unit cell (2H and 1T), and the 2 × 1 (1T′), 2 × 2 (1T′’), and 4 × 4 (H/XS2) supercells, respectively. The criteria of convergence for energy and force were set as 10−4 eV and 3 × 10−3 eV/Å. The hydrogen adsorption energies were calculated using the 4 × 4 surface supercell containing 16 Mo atoms and 32 S atoms. A dipole correction was applied to cancel the electrostatic interaction between the periodic slabs. The DFT binding energies were calculated as , where E(surf+nH), E(surf), and E(H2) are the total energies for the MoS2 surface with n hydrogen atoms adsorbed, the clean MoS2 surface, and the molecular hydrogen in the gas phase, respectively. The most stable H binding site in the basal plane of MoS2 is on the top of the S atoms. We define H coverage as the ratio of the number of H and Mo atoms in the basal plane. For 1T′ MoS2, we obtained binding energies of −0.16 eV, −0.13 eV, and −0.11 eV, and −0.035 eV at the 1/16H, 1/8H, 1/4H, and 1/2H coverage. For the 4 × 4 supercell, this corresponds to n=1, 2, 4, and 8, respectively. The adsorption free energy was calculated by adding a thermal correction to the binding energy ΔGHEHEZPETΔSH, where ΔEZPE and TΔSH are, respectively, the differences in the zero point energy and entropy contribution between the H adsorbed state and H2 in the gas phase. We took ΔSH=−½ S(H2), where ½ S(H2) is the entropy of ½ H2 in the gas phase at standard conditions (T=298.15 K, Pressure=1 atm). We used the assumption that the vibrational entropy in the adsorbed state is small58. For H/1T′ MoS2, EZPE=0.228 eV (vibrational frequencies 2,530.1 cm−1, 637.6 cm−1, 519.8 cm−1) and EZPE=0.271 eV for H2. With these values, the Gibbs free energy was calculated as ΔGHEH+0.29 eV. Additional details are available in Supplementary Methods.


Stock mixtures of 30% v/v TEOA and 10 mg ml−1 Eosin Y were freshly prepared for each reaction. MoS2 (and WS2) were prepared at twice the desired final concentration (for example, 80 p.p.m.). To prepare the reaction mixture, 35 ml of the 30% v/v TEOA was mixed with 35 ml of the MoS2 or WS2, reaching the final concentration of 15% v/v TEOA and the predetermined MoS2/WS2 concentration (for example, 40 p.p.m.). The mixture was then transferred to a 250 ml two-neck flask, to which 1 ml of the 10 mg ml−1 Eosin Y was added. The flask was then covered in aluminum foil, stirred and purged with continuous Ar flow (20 c.c.m.) for 20 min. After Ar purge, the aluminum foil covering was removed, and the mixture was illuminated at 1 sun. With the Ar flow kept at 20 c.c.m., gas samples were continuously monitored at 90 s intervals using an Inficon 3,000 micro GC gas analyzer until reaction termination.

Additional information

How to cite this article: Chou, S. S. et al. Understanding catalysis in a multiphasic two-dimensional transition metal dichalcogenide. Nat. Commun. 6:8311 doi: 10.1038/ncomms9311 (2015).