Owing to the high gravimetric specific energy density and environmentally friendly characteristics, hydrogen energy has emerged as one of the most promising alternatives to fossil fuels1,2. Electrochemical hydrogen evolution reaction (HER) provides an attractive way for efficient H2 production from water electrolysis, in which catalysts are critical for developing renewable energy conversion technologies3. To date, platinum (Pt)-based materials are considered to be the most active HER catalysts, but the scarcity and high cost of Pt rigorously hamper their widespread applications4. Therefore, developing earth-abundant alternatives to Pt-based catalysts for achieving efficient H2 generation is highly desirable. Molybdenum carbide (Mo2C), an excellent early transition-metal carbide, has intensely awakened ever-growing interest as a promising HER electrocatalyst because its electronic structure is virtually analogous to that of Pt metal5,6. Nevertheless, Mo2C surface shows excessively strong Mo–H binding energy, which hinders the desorption of adsorbed H to generate H2, severely deteriorating the electrochemical HER activity7.

Grain boundaries (GBs), as a type of planar defect, are effective to directly tune the surface atomic and electronic structure, significantly altering the intrinsic reactivity of nanocrystalline materials8,9. Specifically, GBs create lattice distortion regions in Mo2C polycrystals by stabilizing dislocations, which could provide an optimized electronic structure for tailoring the binding energy of Mo–H, consequently accelerating the H2 production. However, conventional bulk materials are typically limited to the surface GB density, which is not available for practical catalytic reactions due to the relatively low accessibility of active sites. Compared with bulk counterparts, ultrathin two-dimensional (2D) nanostructures possess sufficient interplanar active sites and shorter reactant/product diffusion length, and have been intensively reported as promising candidates for HER10. Currently, most of the Mo2C nanostructures are synthesized from either high-temperature carburization of costly/toxic molybdenum precursors (e.g., Mo foil, MoF6, and Mo(CO)6) with carbonaceous gases (e.g., CH4, C2H6, and CO)7,11 or the selectively etching layered ternary Mo-containing phases12,13. Nevertheless, in the former method, the resultant carbide surface generally suffers from severe char contamination from the pyrolysis of carbonaceous gases, inhibiting the exposure of active sites; in the latter, the delamination yield and defect controllability of Mo2C sheets derived in aqueous fluoride-containing acidic solutions are not satisfactory. In this context, nearly all the above-mentioned methods can only introduce small changes in the structural and chemical configuration of Mo2C catalysts, resulting in poor tunability for altering the catalytic performance. Therefore, a facile approach for developing high-density and fully exposed GBs on ultrathin 2D Mo2C nanostructure is highly desired.

Herein, we propose an effective strategy to achieve ultrathin Mo2C nanosheets (NSs) with rich GBs supported on N-doped graphene (H-Mo2C/NG) via hydrothermal and water-assisted carbothermal reactions. During the carbonization process, water induces the structural evolution of Mo2C nanocrystals from nanoparticles (NPs) to NSs and controls the GB density of Mo2C NSs as well. The high-density GBs in Mo2C NSs provide an ultra-high fraction of active sites, significantly improving the inherent HER activity of H-Mo2C/NG. Theoretical calculations show that the GBs in Mo2C NSs modulate the configuration of MoC3 pyramid, which thereby regulates the Mo dz2 orbital energy level, manipulating the Mo–H bond strength of H-Mo2C/NG catalyst and influencing the HER activity. This work opens up an avenue for the development of high-efficiency catalysts through GB engineering.


Controllable construction of ultrathin Mo2C NSs with high-density GBs

Mo2C NSs supported on N-doped graphene (NG) were constructed in situ by facile hydrothermal and water-assisted carbothermal reactions (Fig. 1a). Typically, graphene oxide (GO) and (NH4)6Mo7O24·4H2O were dissolved into deionized water and then the homogeneous solution was subjected to a hydrothermal reaction to obtain a homogeneous mixture composed of amorphous MoO3 supported on reduced GO sheets (MoO3/RGO) (Supplementary Fig. 1)7. Next, the mixture was freeze-dried and then treated at 800 °C under NH3/Ar gas. Finally, only Mo2C NPs decorated on NG were obtained when the MoO3/RGO intermediate was water-free. However, when MoO3/RGO intermediate contained sufficient water concentration (18.56 wt%), Mo2C NSs with high-density GBs were constructed in situ and anchored on NG. Further details of the experiments were provided in Methods.

Fig. 1: Formation of H-Mo2C/NG.
figure 1

a Schematic diagram of the synthesis of Mo2C/NG and H-Mo2C/NG. b Various reaction states of ISNP and ISNS along the reaction pathway. Inset shows the corresponding reaction ΔH diagram. The reaction ΔH for TSNS conversion to TSNS-C (–2.48 eV) is lower than that of TSNP conversion to TSNP-C (–0.73 eV), indicating that water promotes the formation of Mo2C during carbonization process.

To illustrate the growth behavior of Mo2C nanocrystals with the assistance of water, density functional theory (DFT) calculations were performed. As shown in Fig. 1b, two theoretical model systems consisting of initial MoO3 without H2O (ISNP) and with H2O (ISNS) are constructed, and the structural evolution mechanisms of Mo2C products are discussed from a reaction enthalpy (ΔH) viewpoint. During the carbonization process, ISNP and ISNS first absorb heat and dissociate into transition states of TSNP and TSNS, respectively, and they then react with C atoms in RGO to form Mo2C. Generally, RGO has two types of C atoms, namely, the highly reactive carbon at the edge and the relatively inertness carbon of the six-membered C-ring far away from the edge14. Because H-bonded graphene has a structure analogous to benzene (Ph), the chemical properties of the compounds can be thought to be similar15. For simplicity, the C atoms extracted from the edge of the graphene lattice, as well as the free Ph radicals, react with TSNP and TSNS to produce TSNP-C, TSNP-Ph, TSNS-C, and TSNS-Ph, respectively. Of course, these model structures are much simpler than those in the actual experiment, yet, they are sufficient to study the interaction between two substances. Theoretical calculations show that ΔH values for TSNP and TSNS reacting with C atoms are both negative, which indicates that the C atoms from RGO can carbonize MoO3 to form Mo2C. In anhydrous atmosphere, C atoms are chemically intercalated into common MoO3 motifs, reducing MoO3 into Mo2C NPs decorated on defective NG. In addition, the reaction ΔH of TSNP to produce TSNP-Ph is 0.45 eV, suggesting that TSNP fails chemically bind with the six-membered C-ring. But the reaction ΔH for TSNS to produce TSNS-Ph is –1.45 eV, which indicates that TSNS tends to combine with six-membered C-ring on RGO basal plane, thus inducing the lateral arrangement of Mo2C lattice along 2D direction16. In general, common MoO3 without H2O can only react with carbon on RGO edge, producing Mo2C NPs. While MoO3 with H2O not only reacts with the edge C atoms but also readily combines with six-membered C-ring along the RGO basal plane; in this situation, epitaxial growth is carried out to enlarge the Mo2C domain, achieving a coalesced NSs with several micrometers in lateral size. Especially, in the presence of H2O, due to the guest–host interaction between H2O and MoO317, a unique Mo–O configuration is obtained and anchored on RGO, which serves as the nucleation site for Mo2C growth. As the activated carbon species encounter the Mo–O configuration, the dense seeds begin to individually nucleate at multiple regions. Consequently, these simultaneously grown nanocrystals merge together seamlessly and eventually form multi-faceted Mo2C NSs, which thereby hinders the growth of Mo2C grains in the radial orientation, leaving behind numerous GBs. In this situation, the RGO intermediate not only provides C source for Mo2C growth, but also acts as a robust supports for Mo2C nanodomains to nucleate and finally splice into NSs; in turn, the formed Mo2C NSs are covalently connected with underneath NG sheets through Mo–C bonds, which ensures the high inherent stability of Mo2C hybrids.

Morphologies and structures of the Mo2C hybrids were characterized with atomic force microscopy (AFM), transmission electron microscopy (TEM), and high-angle annular dark-field scanning TEM (HAADF-STEM) measurements. For Mo2C/NG, Fig. 2a, b and Supplementary Fig. 2 show that high-density and discrete Mo2C NPs (diameter <5 nm) are uniformly loaded on NG layers. In contrast, in H-Mo2C/NG, GB-rich Mo2C NSs with a uniform thickness of ~1.0 nm, corresponding to 2 ~ 3 layers of unit cells, are well-distributed on NG (Fig. 2c, d and Supplementary Figs. 3, 4), affording a very high proportion of exposed active sites. Procession electron diffraction (PED) measurements under TEM were employed to collect orientation maps and extract GB density. As shown in Fig. 2e and Supplementary Fig. 5, the crystallographic orientations of each grain in the polycrystalline microstructure are random, and especially abundant intersections between domain walls can be observed. The GB density of Mo2C NSs in Mo2C hybrids is summarized in Supplementary Fig. 6, where the statistical region of each sample is ~ 20,000 nm2. Obviously, H-Mo2C/NG possesses the highest GB density of 138 ± 3 μm−1, clearly demonstrating that the water content in MoO3/RGO effectively manipulates the GB density of Mo2C NSs, consistent with TEM results (Supplementary Figs. 79 and Supplementary Note 1). It is worth mentioning that the supply of NH3 (Supplementary Fig. 10 and Supplementary Note 2) and the sufficient oxygen-containing functional groups on GO surface (Supplementary Figs. 1114 and Supplementary Note 3) are necessary for the formation of GB-rich Mo2C NSs. Furthermore, tens of HAADF-STEM images clearly reveal that Mo2C NSs composed of individual grains with nanometer size (Fig. 2f and Supplementary Fig. 15), which forms chemically connected interfaces with numerous GBs and triple junctions, indicating full exposure of high-density active sites in electrocatalysis.

Fig. 2: Structural characterization of Mo2C hybrids.
figure 2

a, c AFM images of a Mo2C/NG and c H-Mo2C/NG and their corresponding height profiles. b, d TEM images of b Mo2C/NG and d H-Mo2C/NG. Mo2C NPs are highlighted by yellow dotted circles. e Inverse pole figure (IPF) images from PED analysis of H-Mo2C/NG. f Representative HADDF-STEM image of H-Mo2C/NG, the dashed lines point out the irregular GBs.

Atomic structure of GBs on Mo2C NSs in H-Mo2C/NG

We employed HAADF-STEM characterization to examine the atomic structure of GBs. The inspection of dozens of boundary locations systematically found that the nanocrystalline grains in Mo2C NSs are seamlessly stitched with irregular GBs (Fig. 3 and Supplementary Fig. 16). Figures 3a, a1–a3 obviously display that two Mo2C nanograins form a corrugated GB with an angle of 15°, as well as stacking faults (SFs) and off-centered Mo columns. Furthermore, a conspicuous strain concentration is discovered in the vicinity of the GB (Fig. 3b). Compressive strain (–0.136 ± 0.036) and tensile strain (0.801 ± 0.484 and 0.107 ± 0.086) coexist (Supplementary Fig. 17), ensuring that the average strain of Mo2C NSs almost offsets. In addition, Fig. 3c demonstrates sharp GBs in the same specimen, offering an alternative view. The atomic structure of Mo2C NS is directly determined by characterizing the nanostructure along two zone axes, where two Z-contrast images closely resemble the structural projection of hexagonal close-packed (hcp) Mo2C, and their fast Fourier transform (FFT) patterns can be well indexed by hcp cells along their [1\(\overline{2}\)1\(\overline{3}\)]h and [01\(\overline{1}\)1]h directions, respectively (Fig. 3c1, c2). Where misorientation angle (38°), step dislocations, and terraced step edges are observed (Fig. 3c3, c4). Particularly, the misorientation angle distribution of observed adjacent grains reveals that the misorientation angle of GBs mostly ranges from 18° to 39° (Supplementary Fig. 18). High-angle GBs are the dominant type of planar defects in all of the Mo2C NSs examined, distinguishing from conventional Mo2C nanocrystals grown on graphene without water involved, where low-angle GBs predominate18. Compared with low-angle GBs, high-angle irregular GBs have a greater degree of atomic disorder, which generates a suitable electronic structure19, so as to optimize the H adsorption behavior. Impressively, Mo2C NSs also occur a topotactic transition from a conventional phase of hcp to a metastable phase of face-centred cubic (fcc), which highlights the controlled synthesis of Mo2C NSs with unconventional crystal phases through water-assisted carbonization process. Figure 3d, e and Supplementary Fig. 19 show representative HAADF-STEM images of fcc/hcp GB superstructures. Along the fcc/hcp heterophase edges, both hcp phase with “ABAB” stacking and fcc phase with “ABCABC” stacking, with the coexistence of twin boundaries (TBs) and SFs are observed along the close-packed [110]f/[11\(\overline{2}\)0]h direction. This fcc/hcp heterophase GBs regulate the atomic arrangement of Mo2C lattice, which modifies the electronic structure of Mo2C hybrid, thus enhancing the efficiency of hydrogen production20. In fact, the fcc and hcp phases of Mo2C nanocrystals are strongly controlled by carbon activity21. Meanwhile, the reaction ΔH calculation clearly reveal that in anhydrous system, only the C atoms from graphene edges participate the formation of hcp Mo2C; while in aqueous system, carbon sources from edge and basal plane of the graphene lattice are both active and readily react with the unique Mo–O configuration to produce Mo2C NSs with a mixed fcc and hcp phases (Fig. 1b). On the basis of the aforementioned characterizations, the crystalline structure of Mo2C NSs can be schematically illustrated in Fig. 3f, where the hcp/hcp and fcc/hcp GBs appear alternately. As a result, atomic structure analyzes clarify the atomic configuration at GBs in Mo2C NSs and reveal the obvious lattice distortion, accompanied by abundant atomic step edges, dislocations, TBs, and SFs, which can effectively alter the surface electronic structure.

Fig. 3: Local atomic structure of GBs on Mo2C NSs in H-Mo2C/NG.
figure 3

a A tilted GB in Mo2C NS. Inset of the FFT pattern indicates a 15° misorientation between grains. a1 Enlarged HAADF-STEM image of region 1 in a. Yellow and tangerine circles represent the Mo atoms on the left and right sides of GB, respectively. a2, a3 Enlarged HAADF-STEM images of regions 2 and 3 in a. The orange and white arrows represent SFs and displacements, respectively. b Lattice shear distortion determined from panel a, analyzed using the lattice distortion analysis (LADIA) programme. Inset is the quantitative distribution of shear strain for atoms in black-boxed region. The arrow indicates the direction of strain. The strains near GBs range from –5% to 5%. The atoms are colored according to strain scale, that is, colors for positive values represent tensile strain and those for negative values represent compressive strain. c The hcp/hcp lattices along the [1\(\overline{2}\)1\(\overline{3}\)]h/[01\(\overline{1}\)1]h direction, the white dashed lines point out the irregular GBs. c1, c2 FFT patterns taken from regions 1 and 2 in c, and the corresponding projected supercell models of hcp Mo2C. The cyan balls represent Mo atoms. c3, c4 Enlarged HAADF-STEM images of regions 3 and 4 in c displaying tilt GBs, step dislocations, and stepped surfaces. Step dislocations, caused by the insertion of additional planes into the otherwise self-contained lattice, highlighted with the cyan dotted box. The atomic displacement arose from this distortion at GBs is usually much greater than the relaxation displacement occurring on the crystal surface as well as the displacement caused by the coherent strain through epitaxial thin-film growth18. d The fcc/hcp lattices along the [110]f/[11\(\overline{2}\)0]h direction. The fcc/hcp GBs are marked with white solid lines. e Enlarged HAADF-STEM image of the square region in d. Yellow, tangerine, and cyan dots, respectively, represent planes A, B, and C. Typical defects, including SFs and TBs are marked with orange and yellow lines, respectively. f Schematic illustration of hcp/hcp and fcc/hcp GBs in Mo2C NSs, the red dashed lines point out the irregular GBs.

Crystal and surface electronic structure of Mo2C hybrids were investigated by X-ray diffraction (XRD) and X-ray photoelectron spectroscopy (XPS) measurements. The diffraction patterns of H-Mo2C/NG and Mo2C/NG in Fig. 4a match with the hcp Mo2C (PDF#35-0787), which confirms the identity of Mo2C. Compared to Mo2C/NG, the diffraction peak intensity of H-Mo2C/NG is significantly enhanced with a narrower full width at half maxima, indicating that the introduction of water enables the epitaxial growth of Mo2C grains to harvest large-sized NSs22. No diffraction peaks of fcc Mo2C are detected in Mo2C hybrids (Supplementary Fig. 20), which could be attributed to the strong destruction of the periodic structure for the fcc lattice because of the alternating arrangement of fcc and hcp Mo2C lattices22. Moreover, the Mo 3d spectra of H-Mo2C/NG and Mo2C/NG are deconvoluted into four pairs of peaks (Fig. 4b), indicating that four oxidation states for molybdenum species (+2, +3, +4, and +6) exist in Mo2C hybrids. Compared to Mo2C/NG, a negative shift of 0.17 eV is observed on Mo2+ in H-Mo2C/NG, indicating the electron accumulation of Mo atoms near GBs in Mo2C NSs, which is beneficial to weaken the binding strength of Mo–H and thus enhance the HER activity6. Meanwhile, the Mo–C resonance in C K-edge X-ray absorption near-edge structure (XANES) spectra for H-Mo2C/NG shifts to a higher photon energy zone compared to that of Mo2C/NG (Fig. 4c), which could be attributed to the enhanced orbital hybridization between the C and Mo elements, that caused by lattice distortion near GBs, facilitating electron transfer23. In addition, to further understand the role of water during carbonization process, a series of Mo2C hybrids synthesized with various water contents were also subjected to XPS measurement. As water content increases, the peak intensity of Mo–C (Supplementary Fig. 21) and Mo–N (Supplementary Fig. 22) species increases slightly, indicating that water promotes the formation of nitrogen-doped Mo2C. As revealed by the theoretical calculation that the reaction ΔH of TSNS to produce TSNS-N (–1.05 eV) is lower than that of TSNP to produce TSNP-N (–0.31 eV) (Supplementary Fig. 23), indicating that unique Mo–O configuration induced by water prefers to bind with N atoms forming Mo–N species.

Fig. 4: Spectroscopy characterization of Mo2C hybrids.
figure 4

a XRD patterns of H-Mo2C/NG and Mo2C/NG. The peaks near 2θ = 26° and 43° are assigned to the (002) and (100) reflections of graphene, respectively, and the weak peaks at 37° and 53° are considered to be the (\(\overline{2}\)11) and (\(\overline{2}\)22) planes of MoO2 (PDF#32-0671), respectively. b The high-resolution Mo 3d XPS spectra of H-Mo2C/NG and Mo2C/NG. Mo4+ and Mo6+ can be attributed to MoO2 and MoO3 caused by the oxidation of molybdenum species in ambient atmosphere, respectively. The Mo2+ and Mo3+ are assigned to carbides and nitrides, respectively, which are known to serve as active sites for HER6. c C K-edge XANES spectra of H-Mo2C/NG and Mo2C/NG. The characteristic resonances of C = C π* and C–C σ* originating from NG support. d Mo K-edge XANES spectra of H-Mo2C/NG, H-Mo2C/NG-7.14, Mo2C/NG, and the reference samples. H-Mo2C/NG-7.14 and Mo2C/NG have a higher half-edge energy than that of bulk Mo2C reference, which arises from the charge-transfer from Mo to C atoms on the NG-supported Mo2C8. e Mo K-edge Fourier transform EXAFS spectra of H-Mo2C/NG, H-Mo2C/NG-7.14, Mo2C/NG, and the reference samples. f EPR spectra of H-Mo2C/NG and Mo2C/NG. H-Mo2C/NG shows the EPR signals at g2 = 1.930 (Mo–N species36), g1 = 1.870 and g4 = 2 .056 (Mo5+ species37), followed by g5 = 2.111 and g6 = 2.156 (the resonance on conduction electrons38).

To precisely probe the local coordination structure of GBs in Mo2C nanosheets, XANES and extended X-ray absorption fine structure (EXAFS) at Mo K-edge were conducted. Compared to H-Mo2C/NG-7.14 and Mo2C/NG, the pre-edge of H-Mo2C/NG obviously shifts to lower energy (Fig. 4d), indicating the increased average electron density around Mo atoms, consistent with XPS results. The details of Mo local environment can be described through the k2-weighted Fourier-transformed EXAFS (FT-EXAFS) in R-space. Mo2C hybrids display a prominent peak at 1.30 Å originated from the Mo–C/N vector; with the increase of water content, the peak intensity of Mo–C/N path gradually decreases, indicating a low coordination number (CN) for Mo atoms in Mo2C (Fig. 4e)24. In addition, comparing with Mo foil and bulk Mo2C, Mo2C hybrids exhibit relatively weak Mo–Mo vectors at 2.30 and 2.90 Å; these Mo–Mo paths in H-Mo2C/NG (2.38 and 2.95 Å) are slightly stretched compared to H-Mo2C/NG-7.14 (2.29 and 2.87 Å) and Mo2C/NG (2.29 and 2.87 Å). These results indicate that numerous Mo atoms in H-Mo2C/NG are misplaced and deviated from the normal crystalline position, which could be attributed to the high-angle GBs with large lattice strain in Mo2C NSs25. Furthermore, quantitative EXAFS fitting was performed using DFT optimized hcp Mo2C structure to extract the structural parameters, and the fitting results are displayed in Supplementary Fig. 24. Briefly, compared to H-Mo2C/NG-7.14 and Mo2C/NG, H-Mo2C/NG has two different Mo–C/N paths and low CN (Supplementary Table 1), highlighting the structural distortion and carbon defects, which further confirms the construction of GBs in Mo2C NSs. Moreover, the surface defects in Mo2C NSs are further resolved with the electron paramagnetic resonance (EPR) spectroscopy. As illustrated in Fig. 4f, the EPR signal at g3 = 2.002 for H-Mo2C/NG is attributed to the unpaired electrons trapped on carbon defects at Mo2C GBs;26 where a slightly lower signal is observed for Mo2C/NG, demonstrating relatively high concentration of coordination unsaturated Mo atoms in Mo2C NSs, consistent with EXAFS results. The above results demonstrate that the water-assisted carbothermal reaction strategy successfully constructs ultrathin Mo2C NSs with high-density GBs anchored on NG support, which provides sufficient active sites and the possibility of modulating the interface atomic and electronic configurations.

Electrocatalytic HER performance

The catalytic performance of Mo2C hybrids was investigated by a three-electrode system in 0.5 M H2SO4 and 1.0 M KOH solutions (see more details in Methods). As revealed in Fig. 5a, H-Mo2C/NG shows the highest HER performance among all catalysts in acidic media, and only requires an overpotential of 10 mV to achieve the geometric current density of –10 mA cm–2 (η10), significantly superior to the Mo2C/NG (η10 = 138 mV) and even Pt/C catalyst (η10 = 19 mV). Furthermore, the Tafel slope of H-Mo2C/NG is 38 mV dec–1 (Fig. 5b), which far surpasses that of Mo2C/NG (137 mV dec–1) and is even comparable to that of state-of-the-art Pt/C catalyst (34 mV dec–1), suggesting that H-Mo2C/NG possesses more fast kinetics with the Heyrovsky reaction as the rate-determining step18. The exchange current density (j0) of H-Mo2C/NG is calculated to be 5.47 mA cm−2, which is much higher than that of Mo2C/NG (0.80 mA cm−2) (Supplementary Table 2), further underscoring favorable HER kinetics. Meanwhile, H-Mo2C/NG also demonstrates promising HER activity in alkaline media. H-Mo2C/NG merely requires overpotentials of 63 and 163 mV to reach –10 and –100 mA cm–2, respectively, which are comparable to commercial Pt/C catalyst (η10: 57 mV and η100: 173 mV) and significantly better than those of Mo2C/NG (η10: 107 mV and η100: 388 mV) (Fig. 5c). Compared to Mo2C/NG catalyst, H-Mo2C/NG also affords a lower Tafel slope of 48 mV dec–1 (Fig. 5d) and higher j0 value (0.75 mA cm–2), which reveals the same favorable HER kinetics as in acidic media for H-Mo2C/NG. To further study the effect of GBs on HER activity, we performed electrocatalytic hydrogen evolution tests on a series of Mo2C hybrids. Obviously, as the water content increases, the η10 and Tafel slopes on Mo2C hybrids firstly decrease and then increase (Supplementary Figs. 25-28), where H-Mo2C/NG with the highest GB density achieves the best HER performance. These results suggest that the GBs in Mo2C NSs can effectively enhance the intrinsic HER activity of the Mo2C hybrids. Additionally, to gain insight into the superior catalytic activity of H-Mo2C/NG, the turnover frequency (TOF) was calculated (Supplementary Fig. 29 and Supplementary Note 4). As displayed in Fig. 5e, H-Mo2C/NG affords the TOF values of 21.33 and 3.81 H2 s–1 at η = 100 mV in acidic and alkaline electrolytes, respectively, which are quite larger than those of Mo2C/NG (0.57 and 1.08 H2 s–1), as well as other control samples (Supplementary Fig. 30), confirming the high HER activity of H-Mo2C/NG. To further identify the intrinsic activity of H-Mo2C/NG, geometric current density (j) was normalized by electrochemical active surface area (ECSA; jECSA), which was determined by deriving the electrochemical double-layer capacitance (Cdl). The Cdl of H-Mo2C/NG (23.8 mF cm–2) is slightly higher than that of Mo2C/NG (19.7 mF cm–2), suggesting the close ECSA values (Fig. 5f and Supplementary Note 5). Yet, H-Mo2C/NG delivers the jECSA values of 109.53 and 10.57 μA cm–2 at η = 50 mV in 0.5 M H2SO4 and 1.0 M KOH (Supplementary Figs. 31, 32), which are evidently higher than those of Mo2C/NG (3.70 and 6.23 μA cm–2) and Pt/C (80.16 and 9.86 μA cm–2), respectively, revealing better intrinsic HER activity of H-Mo2C/NG with massive GBs, even outperforming benchmark Pt/C catalyst. In comparison with non-precious metal HER electrocatalysts reported recently (Supplementary Tables 3, 4), H-Mo2C/NG exhibits almost the lowest overpotential and Tafel slope, illustrating the super HER activity in pH-universal electrolyte. Besides, H-Mo2C/NG has a small charge-transfer resistance (Rct) (2.5 and 2.1 Ω) in 0.5 M H2SO4 and 1.0 M KOH, respectively, which is much lower than those of Mo2C/NG (5.5 and 12.5 Ω) and other control samples (Supplementary Fig. 33). This result indicates that H-Mo2C/NG possesses much fast electron transfer kinetics during HER process, which is attributed to the unique structure of Mo2C NSs with chemically connected GBs, shortening the electron transfer pathway between active sites27.

Fig. 5: HER performance.
figure 5

a, c The polarization curves and b, d the relevant Tafel plots of H-Mo2C/NG, Mo2C/NG, and Pt/C in a, b 0.5 M H2SO4 and c, d 1.0 M KOH, respectively. e TOF values of H-Mo2C/NG and Mo2C/NG in 0.5 M H2SO4 and 1.0 M KOH. f The plots of the current density versus the scan rate for H-Mo2C/NG and Mo2C/NG in 1.0 M KOH. Inset is cyclic voltammetry (CV) cycles of H-Mo2C/NG. g Galvanostatic measurement of H-Mo2C/NG in 0.5 M H2SO4 and 1.0 M KOH at j = –100, –200, and –300 mA cm–2, respectively.

For real applications, the stability and durability of H-Mo2C/NG were further analyzed. As illustrated in Supplementary Fig. 34, after 10,000 or even 50,000 cycles in 0.5 M H2SO4 and 1.0 M KOH, the shifts of polarization curves for H-Mo2C/NG are negligible compared with the initial curves. Meanwhile, we performed aggressive long-term stability examine on H-Mo2C/NG by continuous galvanostatic measurement (Fig. 5g). After 100,000 s of operation at j = −100, −200, and −300 mA cm−2, the potentials of H-Mo2C/NG only increase by 8, 14, and 38 mV in 0.5 M H2SO4, and 11, 13, and 36 mV in 1.0 M KOH, respectively. In contrast, the potentials of Pt/C catalyst at j = −200 mA cm−2 increase by 136 and 110 mV in 0.5 M H2SO4 and 1.0 M KOH, respectively. In addition, TEM characterization shows that Mo2C nanocrystals in H-Mo2C/NG still maintain an ultrathin nanosheet structure with highly exposed high-density GBs after electrochemical cycling (Supplementary Fig. 35). XRD characterization displays that Mo2C is well crystallized, and no other phase is experimentally detected (Supplementary Fig. 36). The chemical valence state of Mo species remains almost unchanged, further indicating the robustness of H-Mo2C/NG in the electrocatalytic HER process (Supplementary Fig. 37). It should be noted that most synthesized 2D Mo2C catalysts cannot withstand a high current density and operate for a long-lasting lifetime in a wide pH range because of the weak interfacial adhesion with adjacent nanocrystals or substrates11,13. In this work, the excellent physicochemical stability of H-Mo2C/NG can be attributed to the chemical connection of Mo2C GBs and strong interaction of Mo2C NSs with NG sheets through Mo–C bonds. Moreover, the general synthetic strategy of GB-rich NSs can also be extended to other transition metal carbide systems (Supplementary Fig. 38), such as vanadium (Supplementary Fig. 39), niobium (Supplementary Fig. 40), tantalum (Supplementary Fig. 41), and tungsten (Supplementary Fig. 42), and yield excellent HER performances in pH-universal electrolyte (Supplementary Fig. 43), demonstrating the generality of this method, which provides an alternative way to develop high-efficiency catalysts through GB engineering.

DFT calculations

To understand the correlation between the electronic structure and catalytic performance in GB-rich Mo2C plane, DFT calculations were conducted. According to the HAADF-STEM images of Mo2C NSs (Fig. 3 and Supplementary Figs. 16, 19), the computational models of fcc/hcp, fcc/fcc, and hcp/hcp GBs were constructed, respectively. The DFT calculation shows that the fcc/hcp Mo2C slab surface exists various kinds of trigonal pyramid-like structures (Supplementary Fig. 44), in which Mo atom locates at top and pyramidally coordinates with three C atoms at bottom, forming a typical trigonal pyramid (MoC3) configuration (Fig. 6a). Depending on the height of the pyramid-shaped MoC3 skeleton on the fcc/hcp Mo2C superlattice surface, the corresponding configuration of MoC3 can be schematically classified into three types: (i) approximative triangular plane (S1), (ii) intermediate height (S2), and (iii) high height (S3). The hcp Mo2C surface consists of S1 and S3 structures, in which the S3 structure typically represents common bulk Mo2C configuration and is predominant; on the fcc Mo2C surface, MoC3 pyramids only present S3 structure. Notably, the fcc region of the fcc/hcp GB is contracted interface with a smaller Mo–Mo distance corresponding to the S3 structure. While the hcp region of the fcc/hcp GB exhibits an elongated interface with a larger Mo–Mo distance, where MoC3 pyramids at GB have a medium height and belong to S2 structure.

Fig. 6: Relationship between HER activity and the dz2 orbital energy level.
figure 6

a Structural models and relevant electronic states of Mo d orbital for MoC3 configurations. S1: MoC3 triangular plane, S2: intermediate height, S3: high height. PDOS of Mo d orbital for b S2 and c S3 structures. d Schematic diagram of hybridization of H 1 s orbital and Mo dz2 orbital. e Correlation of the Mo dz2 orbital energy level and Hads, inset is the corresponding fitting equation.

Furthermore, to find the rule for the GB effect on HER electrocatalysis, the crystal field analyzes of MoC3 pyramids for S2 and S3 structures were performed with the projected density of state (PDOS) calculation, as illustrated in Fig. 6b and c, respectively. Evidently, with the increase of the height (from bottom C3 plane to atop Mo atom), the energy level of the Mo dz2 orbital also increases correspondingly. Consequently, these three low-lying orbitals further undergo symmetry breaking, rising the Mo dz2 orbital state into distinct energy levels28 (Fig. 6a). In the electrocatalytic HER process, the adsorption of H atoms on the Mo atoms forms σ bonds, which originate from the orbital hybridization between the H 1 s orbitals and the Mo dz2 orbitals (Fig. 6d). According to the Sabatier principle, the ideal electrocatalyst should bind H intermediate neither too strongly nor too weakly29. Therefore, the optimized adsorption free energy and fast HER kinetics can be achieved by manipulating the bond strength between the H 1 s orbital and Mo dz2 orbital4.

The bond strength is defined as:

$$E\propto \frac{f({{{{{\rm{S}}}}}},{E}_{{{\rm{d}}}_{{z}^{2}}})}{{E}_{{{\rm{s}}}}-{E}_{{{\rm{d}}}_{{z}^{2}}}}$$

Where Es and \({E}_{{{\rm{d}}}_{{z}^{2}}}\) are the energy levels of H 1 s orbital and Mo dz2 orbital, respectively. S is orbit overlap population of H 1 s orbital and Mo dz2 orbital. Within these contexts, we calculated the H adsorption free energy (Hads) of surface Mo atoms on the model of fcc/hcp GB, and studied its relationship with the Mo dz2 orbital energy level (Fig. 6e). Where the numerical fitting over the calculated Hads and the Mo dz2 orbital energy level follows the similar function as the Eq. (1) of bond strength, that is, the adsorption energy varies with the Mo dz2 orbital energy level. As a result, the intrinsic HER activity exhibits a strong dependence on the Mo dz2 orbital energy level, which rationalizes the role of dz2 orbital energy level as one of the most important activity descriptors for HER in Mo2C systems. Compared with the state-of-the-art descriptors such as band-energy theory and work function that describe the properties of the whole surface30, the dz2 orbital energy level is more relevant to the active site of the catalysts. Therefore, the descriptor dz2 orbital energy level could be used as a figure of merit for designing transition metal catalyst with well-defined active sites for electrocatalytic HER reaction. Additionally, the Hads on the Mo atoms near the fcc/fcc and hcp/hcp homophase Mo2C GBs also display close-to-zero values, such as –0.044, 0.035, and 0.038 eV (Supplementary Figs. 45 and 46), which also contribute to the excellent HER activity. As a result, the DFT results confirm that GBs in ultrathin Mo2C NSs can significantly alter the electronic structures of H-Mo2C/NG electrocatalyst, and the intrinsic HER activity strongly depends on the Mo dz2 orbital energy level controlled by the MoC3 pyramid configuration.


In summary, ultrathin Mo2C NSs with rich GBs supported on NG have been developed by facile hydrothermal and water-assisted carbothermal reactions with GO as carbon source. During carbonization process, water induces structural evolution of Mo2C nanocrystals from NPs to NSs and controls the GB density of Mo2C NSs as well. In H-Mo2C/NG, the dense polycrystalline Mo2C NSs with massive irregular GBs are chemically connected to NG through Mo–C bonds, which afford ultra-high fraction of active sites for electrolysis, exhibiting high reproducibility in terms of structure and performance. The inherent HER activity of H-Mo2C/NG electrocatalyst strongly depends on the dz2 orbital energy level of Mo atoms, which is controlled by the MoC3 pyramid configuration. This work provides a horizon for rationally designing GB interfaces of transition metal electrocatalysts to achieve excellent HER activities, and establishes a descriptor of the dz2 orbital energy level for the design of high-performance catalysts.



All chemicals were purchased from commercial sources (Sigma Aldrich, Energy Chemical) without further purification. GO was synthesized from graphite flakes by the improved Hummers method31.

Synthesis of H-Mo2C/NG

First, the GO suspension was prepared by adding 0.16 g GO into 80 mL deionized water and sonicating for 10 h. Typically, 0.4470 g (NH4)6Mo7O24·4H2O were added into the GO suspension and sonicated for another 4 h. Subsequently, above mixture was transferred to a Teflon-lined autoclave and heated at 190 °C for 12 h to harvest MoO3/RGO intermediate. Next, the MoO3/RGO intermediate was freeze-dried to obtain sponge columns with various water contents, including 0, 0.41, 7.14, 13.52, 18.56, 30.98, and 43.28 wt%. The MoO3/RGO with various water contents were put into a tubular quartz furnace for heat treatment. After pumping and purging the system with Ar for 30 min, the temperature was ramped at 10 °C min−1 up to 800 °C with the feeding of Ar (150 sccm) and NH3 (100 sccm). The reaction was allowed to proceed for 3 h and the final product was fast cooled to room temperature by quickly removing the sample from the hot zone of the furnace under the protection of flowing Ar. The final catalysts were named H-Mo2C/NG-X, where X was the water content retained in MoO3/RGO intermediate, for example, H-Mo2C/NG-7.14 (the water content was 7.14 wt%). In our report, H-Mo2C/NG-18.56 and H-Mo2C/NG-0 were denoted as H-Mo2C/NG and Mo2C/NG unless otherwise specified, respectively.

Material characterization

Morphological structure characterizations of Mo2C hybrids were performed on SEM (JEOL-JSM-7001F) and TEM (FEI Talos F200X, FEI Titan ChemisSTEM, FEI Titan Themis). HAADF-STEM images were carried out by a Cs-corrected FEI Titan G2 60-300 equipped with a Super-X EDS detector. The LADIA package was used to analysis the strain states of Mo2C nanocrystals during the loading and unloading of tensile stress32. The surface electronic structure was checked by XPS spectra (XPX, PHI-5702). The C and N K-edge NEXAFS spectra were measured at the photoemission end-station at beamline BL10B in the National Synchrotron Radiation Laboratory (NSRL) in Hefei, China. X-ray absorption spectra (XANES and EXAFS) of Mo K-edge were measured on VESPERS beamline at the Canadian Light Source, by scanning a double crystal Si (111) monochromator and collecting emitted X-ray fluorescence.

Electrochemical measurements

Electrochemical measurements were conducted on a typical three-electrode system (CH Instruments 760E). All potentials were referenced to a reversible hydrogen electrode (RHE) and without iR compensation. The binder solution was prepared by mixing of 5 wt% Nafion solution (40 μL) with 1 mL of 4:1 v/v deionized water/ethanol. The catalyst ink was then prepared by dispersion of 2 mg Mo2C hybrids (H-Mo2C/NG, Mo2C/NG, and control samples) into binder solution followed by ultrasonication for 2 h. In Mo2C hybrids, molybdenum atoms are the active species, and molybdenum loading (~ 8 wt%, Supplementary Table 5) is basically the same. To maintain the same metal load, 8 mg Pt/C catalyst (20 wt% Pt on graphitized carbon, Johnson Matthey) ink was prepared in the same way. The ink (10 μL) was then dripped onto a carbon fiber paper (CFP, 5 mm × 5 mm) as the working electrode. The electrode was allowed to dry at room temperature for at least 24 h before measurement. After drying, a catalyst (Mo2C hybrids and Pt/C) mass loading of 0.038 mg cm–2 was obtained. A graphite rod as the counter electrode and saturated calomel electrode (SCE) as the reference electrode. All potentials were referenced to RHE: ERHE = ESCE + (0.242 + 0.059 pH) V. In 0.5 M H2SO4 and 1.0 M KOH solutions, the polarization curves were obtained at the electrode potential of 0 to 0.45 V using a scan rate of 50 mV s−1. The electrochemical EIS was performed from 10–2 to 106 Hz with an AC voltage of –5 mV. Galvanostatic charge discharge curves of H-Mo2C/NG were recorded at j = –100, –200, and –300 mA cm–2. Prior to all measurements, the electrochemical system was purged with H2 bubbles for 30 min, and then conducted all electrochemical measurements at room temperature (25 °C) under ambient atmosphere.

DFT calculations

The first-principles calculations based on the DFT were performed within generalized gradient approximation (GGA). Core electron states were represented by the projector augmented-wave method as implemented in the Vienna ab initio simulation package (VASP)33,34. The Perdew–Burke–Ernzerhof exchange-correlation functional and a plane wave representation for the wave function with a cut-off energy of 450 eV were used35, more details can be found in Supporting Information (Supplementary Note 6). The atomic coordinates of the H adsorption on the fcc/hcp GB model to generate Fig. 6e are listed in VASP CONTCAR format (Supplementary Data 1).