Charge Engineering of Mo2C@Defect-Rich N-Doped Carbon Nanosheets for Efficient Electrocatalytic H2 Evolution

Highlights The Mo2C modified carbon nanosheets produce a graphene wave structure to form localized charges and further enhance the N-doping effect. The optimal sample shows a Tafel slope as low as 60.6 mV dec−1 and high durability up to 10 h in acidic media. Electronic supplementary material The online version of this article (10.1007/s40820-019-0279-8) contains supplementary material, which is available to authorized users.


Introduction
With the intensification of global energy consumption and severe environmental deterioration, sustainable and environmentally friendly approaches have aroused increasing interest [1]. Among ongoing attempts to produce clean fuels, the electrolysis of water to produce H 2 is attractive [2][3][4][5][6]. The key to this problem is to seek an effective electrocatalyst to minimize the overpotential for hydrogen evolution reaction (HER). To replace Pt-based noble metals, abundant earth catalysts have received great attention [7][8][9][10][11]. Because of their similar electronic structure and catalytic behaviors to Pt [12], Mo-based compounds [13,14], especially molybdenum carbide [15], have drawn tremendous fascination. On the other hand, the electronic structure significantly affects the interaction between the catalyst surface and reactants [4,[16][17][18][19][20]. Charge engineering is an important strategy to regulate the surface/interface behaviors involved in catalysis. For example, Sasaki et al. [21] found that carbide ligand changed the d-electron configuration of Mo 2 C to moderate Mo-H binding energy, leading to enhanced-HER activity.
Recently, researchers have paid great attention to nitrogen-doped defective carbon materials for electrocatalysis [22][23][24][25][26]. The defects not only play an important role in the adsorption/desorption during reaction, but also change the electrical conductivity of the catalysts to regulate the electronic structure [27]. However, related work on the application of MO 2 C to pyridinic N-doped carbon is limited. Furthermore, for gas-involving electrocatalysis, the hierarchical morphology is also important to optimize the gas/ mass transport [16].
Considering the above-mentioned observations, Mo 2 C@ defect-rich N-doped carbon nanosheets (MoNCs) were developed. The theoretical results imply that the introduction of Mo 2 C produces a graphene wave structure, which to a degree behaves like N doping to form localized charges.
As expected, the catalyst shows high-electrocatalytic HER activity with a Tafel slope as low as 60.6 mV dec −1 and stability up to 10 h in acidic media, making it one of the best Mo 2 C electrocatalysts. The multifold design, including charge engineering and nanoarchitecture construction, contributes to the HER performance.

Synthesis
Graphitic carbon nitride (g-C 3 N 4 ) was prepared by simple calcination. A certain quantity of melamine was placed in an alumina crucible (100 mL) with a cover and then heated at 550 °C for 4 h in a muffle furnace (2.3 °C min −1 ). Subsequently, the obtained light-yellow solid product was milled into a powder state and sealed for later use. Next, ammonium heptamolybdate, sucrose, and g-C 3 N 4 were mixed together (1:2:2, mass ratio). The homogeneous mixture was placed in an alumina crucible and then transferred to the center of the tube furnace. After pumping and purging the system three times with N 2 flow, it was heated to 800 °C (3 °C min −1 ) and maintained at 800 °C for 6 h under flowing N 2 . The obtained black sample, called MoNCs (Mo 2 C@N-doped carbon sheets; the mass ratio of g-C 3 N 4 and ammonium heptamolybdate is 2), was then ground to a fine powder without further treatment. For comparison, MoNCs-0, MoNCs-1, and MoNCs-5 (the mass ratio of g-C 3 N 4 and ammonium heptamolybdate is 0, 1, 5), as counterparts, were also prepared in the same way.

Computational Details
In this work, nanosheets with Mo 2 C nanoparticles have been modeled as single-layer graphene in a 6 × 6 × 1 supercell, and Mo 2 C in a 5 × 5 × 2 supercell. The cell and atomic coordinates are fully relaxed based on the density functional theory implemented in the Vienna Ab-initio Simulation Package (VASP) v5.3.5 [29][30][31] with grimme-D2 correction [32], where the PBE functional [33] and PAW pseudopotential [34,35] have been used. The criteria of convergence of energy and force have been taken as 1 × 10 −6 eV and 0.01 eV Å −1 , respectively, the energy cutoff is set to 450 eV, and a 3 × 3×1 k-mesh is used to sample the Brillouin zone [36,37]. The parameters are comparable to those in Refs. [36,37]. In the core-level shift (CLS) calculation, the final state approximation has been adopted.

Electrochemical Measurements
The HER measurements were performed in a typical threeelectrode cell in 0.5 M H 2 SO 4 using a CHI 660e electrochemical station (Shanghai Chenhua Co., China) at room temperature. A glassy carbon electrode (GCE) 8 mm in diameter, a saturated calomel electrode (SCE), and a graphite rod electrode were used as the working electrode, reference electrode, and counter electrode, respectively. All of the potentials were converted to the potential versus the reversible hydrogen electrode (RHE) according to E (RHE) = E (SCE) + 0.241 + 0.059 pH. The working electrode was fabricated as follows: A catalyst ink was prepared by dispersing 6 mg of catalyst into a mixed solution including 40 μL Nafion solution and 1 mL of 3:1 v/v water/isopropanol via sonication for at least 1 h to form a homogeneous ink. Then, 20 μL of well-dispersed catalyst ink was drop-casted on the glassy carbon electrode, producing a ~ 0.23 mg cm −2 loading for all samples, and the modified GC electrode was then dried at 50 °C in a drying oven for the following test. Before data collection, all working electrodes were pretreated by cyclic voltammetric scanning in 0.5 M H 2 SO 4 solution to activate the electrodes. The electrochemical impedance spectroscopy (EIS) measurements were tested in 0.5 M H 2 SO 4 solution with open-circuit voltage at a frequency from 10 mHz to 100 kHz at an amplitude of 5 mV.

Results and Discussion
We combined Mo 2 C and N-doped graphene and theoretically simulated its atomic structure with first-principles calculation. Due to the limitation of computations, we used a slab of Mo 2 C covered with one layer of graphene to simulate part of the interface region of Mo 2 C and graphene. The vacuum was added in the direction perpendicular to the graphene plane, and periodicity was kept in the other two directions. According to the literature [37,38], the β-Mo 2 C is a metastable structure at high temperature, where the Mo atoms are packed in a hexagonal close-packed structure, and the C atoms randomly occupy half of the octahedral interstitial sites (Fig. 1). As noted, the Mo 2 C@N-doped graphene has two types of structures: The Mo-terminated surface adhered to the graphene, and the C-terminated surface adhered to the graphene. We found that in Mo-terminated Mo 2 C@N-doped graphene, the graphene was approximately 2.22 Å above the Mo 2 C (Fig. 1b). Interestingly, the phenomenon of a graphene wave was observed, which should be attributed to the mismatch of the graphene and Mo 2 C unit cell. We have reason to believe that the graphene wave could introduce more localized charge density on some C sites, as indicated by the yellow circles (Fig. 1f), leading to the redistribution of electrons on the graphene and formation of a gradient of charge density to increase active sites. For C-terminated Mo 2 C@N-doped graphene, the graphene is found to be selfreorganized in the bulk defect region and approximately 3.96 Å above Mo 2 C (Fig. 1d).
Here, a Mo 2 C slab covered with one layer of graphene was used to simulate the real case, in which Mo 2 C nanoparticles are enclosed in nanosheets. Given that the nanoparticles have various shapes and sizes, the structural change and charge localization on the graphene should be more significant, as the nanoparticles have curved and highly indexed surfaces. On the other hand, with the increase in the number of nanosheets, the effect weakens. However, for a nanoparticle with two or three layers of nanosheets, the predicted phenomena should occur and contribute to the catalysis. Moreover, to clarify the influence of Mo 2 C on N-doped carbon sheets (NCS) further, we computed the N1s CLS within For Mo-terminated Mo 2 C@N-doped graphene, the CLS moves forward to a higher energy (Figs. 1e, f and S1). The N1s core level deepens, which means that N achieved more electrons localized on the N atom. This will strengthen the N-doping effect and further promote the HER activity. Apart from these, we also calculated three more types of N doping in the Mo 2 C region within Mo 2 C@N-doped graphene, as shown in Fig. S1b-d. All three types of structures yield rather smaller binding energies for N1s core electrons. The synthesis route of MoNCs is shown in Fig. 2a. The carbonization of sucrose and the decomposition of ammonium heptamolybdate and g-C 3 N 4 were integrated, rendering the simultaneous formation of uniformly dispersed Mo 2 C and N-doped carbon nanosheets. The synthesis avoids sophisticated or hazardous processes and expensive precursors. Figure 2b clearly displays the diffraction peaks at 34.4°, 38.0°, and 39.4°, attributed to the (100), (002), and (101) plane of hexagonal β-Mo 2 C (PDF# 35-0787), respectively [40]. No additional peaks were observed except for the (002) diffraction peak of graphite at ~ 26° [41]. Then, the N 2 adsorption-desorption measurement (Fig. 2c) was carried out to investigate the specific surface area and pore structure. The typical type-IV isotherm curve is noted according to the Brunauer-Deming-Deming-Teller classification [42], verifying the presence of mesopores [43]. The BET surface area (S BET ) is evaluated as 216.4 m 2 g −1 . The pore size distribution curve indicates the presence of micropores and mesopores, which are probably caused by the released molecules (H 2 O, CO 2 , C 2 N 2 + , C 3 N 2 + , C 3 N 3 + , etc.) during the carbonization of sucrose [44,45] and the decomposition of g-C 3 N 4 [46]. There is no doubt that the hierarchically porous structure will supply adequate diffusion passageways to strengthen the mass transfer [47].   In Fig. 3a, b, the typical TEM and HRTEM images reveal that MoNCs mainly consisted of a large amount of 1-3-nm Mo 2 C (inset in Fig. 3b) particles wrapped in thin carbon nanosheets. The lattice spacing is ~ 0.23 nm, corresponding to the distance between the (101) crystal planes of β-Mo 2 C. The thin carbon nanosheets (3-5 graphene layers) with lattice spacing of ~ 0.34 nm not only inhibit the agglomeration of Mo 2 C, but also guarantee the fast electron transfer and effective exposure of active phases. Massive defects were also noted (white arrows). The elemental mapping (Fig. 3c-f) result indicates that the Mo, N, and C atoms were homogeneously distributed. The Raman spectrum (Fig. 3g) also displays the typical D-band and G-band at 1341 and 1583 cm −1 , respectively. The D1, D3, D4, and G peaks were fitted [48]. The high value (2.16) of I D1 /I G implies abundant defects, which are believed to enhance the electrocatalytic activity [49]. The Mo 2 C content in MoNCs determined by TGA is ~ 50.0 wt.% (Fig.  S2). X-ray photoelectron spectroscopy (XPS) was used to further characterize the composition and chemical state of each element. As seen in Fig. S3, the survey XPS spectrum of the MoNCs shows obvious signals of elemental Mo, C, and N, which is consistent with the elemental mapping result above. The Mo 3d XPS spectrum (Fig. 3h) was deconvoluted into six peaks, corresponding to Mo 2+ (228.6 and 232.4 eV), Mo 4+ (229.3 and 232.8 eV), and Mo 6+ (233.2 and 235.9 eV) species [50]. Mo 2+ comes from Mo 2 C, which serves as the active sites for HER [51,52]. In Fig. S4, the main peak at 284.6 eV in the deconvoluted C1s spectrum implies that graphite carbon is the majority species [53]. The N1s XPS spectrum was deconvoluted into two peaks at 401.3 and 398.6 eV (Fig. 3i), corresponding to the quaternary N (20%) and pyridinic N (80%), respectively. The high pyridinic N content will be  Log (|j(mA cm −2 )|) favorable for HER [54]. Moreover, the element contents in the MoNCs were calculated and summarized in Table S2. The electrocatalytic HER performance was investigated. For comparison, control samples synthesized with different mass ratios of starting materials were also tested. In Fig. 4a, the MoNCs show a low onset overpotential of 83 mV and the lowest overpotential of 157 mV @ 10 mA cm −2 , exhibiting the best HER activity among the four control samples. In addition, the influence of loading mass on the HER activity was also studied (Fig. S5). The linear sweep voltammetry (LSV) curves of the MoNCs are also provided when the loading mass increased from 0.115 to 0.460 mg cm −2 , indicating the enhanced-HER performance with more loadings. To demonstrate the HER mechanism, the linear sections of the Tafel plots were fitted to the Tafel equation (η = a + b log (j), where a is the intercept, b is the Tafel slope, and j is the current density), as shown in Fig. 4b. The MoNCs achieve the smallest Tafel slope of 60.6 mV dec −1 among the four samples (Table S3), suggesting that HER can likely proceed through the Volmer-Heyrovsky mechanism [55]. Remarkably, the exchange current density (j 0 ) for MoNCs, calculated by extrapolating the Tafel plot to an overpotential of 0 mV (Fig. S6), was also the highest (2.65 × 10 −2 mA cm −2 ). Compared to the previously reported Mo 2 C-based non-preciousmetal catalysts, the excellent HER performance makes our sample one of the most promising electrocatalysts (Fig. 4c, Table S3). MoNCs show almost no current loss after 1000 CV cycles (Fig. 4e). Furthermore, the current density exhibits a negligible degeneration at a static overpotential The effective electrochemical surface area (ECSA) was evaluated by the electrochemical double-layer capacitance (EDLC, C dl ) (Figs. 4d, 5). The C dl measured at 0.10 V for MoNCs was the highest (14.31 mF cm −2 ), indicating more active sites. The EIS was also tested (Fig. S7). The Nyquist plot of the MoNCs displays a small semicircle among them, suggesting lower impedance to accelerate the charge transfer during HER. Furthermore, the turnover frequency (TOF) of MoNCs was estimated [56] (see more details from supporting information). In Fig. S8, the MoNCs achieved a TOF of 0.07 and 1.12 s −1 at overpotential of 150 and 250 mV, respectively. The values were much higher than those of other catalysts, indicating more active sites.

Conclusion
In summary, we illustrate charge engineering of Mo 2 C@ defect-rich N-doped carbon nanosheets for electrocatalytic H 2 evolution. The calculation result indicates that the introduction of Mo 2 C induces a graphene wave structure, which behaves like N doping to form localized charges for the first time. The thin carbon nanosheets, combined with plentiful defects, facilitate the fast electron transfer and effective exposure of active phases. As a result, the sample displays a Tafel slope as low as 60.6 mV dec −1 and high durability up to 10 h in acidic media, featuring excellent HER catalytic activity and stability. Our work emphasizes the importance of charge engineering in electrocatalysis.