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# Dual-phase MoS2/MXene/CNT ternary nanohybrids for efficient electrocatalytic hydrogen evolution

## Abstract

Two-dimensional (2D) molybdenum disulfide (MoS2) has been recognized as a potential substitution of platinum (Pt) for electrochemical hydrogen evolution reaction (HER). However, the broad adoption of MoS2 is hindered by its limited number of active sites and low inherent electrical conductivity. In this work, we employed a one-step solvothermal synthesis technique to construct a ternary hybrid structure consisting of dual-phase MoS2, titanium carbide (Ti3C2) MXene, and carbon nanotubes (CNTs), and demonstrated synergistic effects for active site exposure, surface area enlargement, and electrical conductivity improvement of the catalyst. The dual-phase MoS2 (DP-MoS2) is directly formed on the MXene with CNTs acting as crosslinks between 2D islands. The existence of edge-enriched metallic phase MoS2, the conductive backbone of MXene along with the crosslink function of CNTs clearly improves the overall HER performance of the ternary nanocomposite. Moreover, the integration of MoS2 with MXene not only increases the interlayer distance of the 2D layers but also partially suppresses the MXene oxidation and the 2D layer restacking, leading to good catalytic stability. As a result, an overpotential of 169 mV and a low Tafel slope of 51 mV/dec was successfully achieved. This work paves a way for 2D-based electrocatalyst engineering and sheds light on the development of the next-generation noble metal-free HER electrocatalysts.

## Introduction

Hydrogen shows great potential in reducing greenhouse gas emissions and improving energy efficiency due to its environmentally friendly nature and inherent high gravimetric energy density1,2,3. Hydrogen gas can be generated via electrochemical water splitting based on the hydrogen evolution reaction (HER, $$2H^ + + 2e^ - \to H_2$$)4,5. HER is a multistep reaction that starts with a Volmer step ($$H^ + + e^ - + \ast \to H_{ads}$$). The intermediate Hads is removed from the catalyst surface either by Tafel reaction ($$H_{ads} + H_{ads} \to H_2 + 2 \ast$$) or by Heyrovsky reaction ($$H^ + + H_{ads} + e^ - \to H_2 + \ast$$)6,7. The reaction kinetics is greatly affected by the number of available active sites (represented as * in the equation), the way Hads interacts with the catalyst surface (i.e., hydrogen adsorption energy ΔGads), and electron transfer rate. It is well known that Pt-group metals (PGM) are excellent catalysts for HER, but their practical applications are limited by the high cost and scarcity1,7,8. Therefore, the development of active HER catalysts made from low-cost materials is the key step in the utilization of hydrogen energy.

Recently, non-precious elements have been widely employed to construct HER catalysts which can be classified into two major groups including transition metals (such as Mo, W, and Co, etc.) and nonmetals (such as S, Se, and C, etc.). To date, efficient PGM-free HER electrocatalysts synthesized based on the above-mentioned non-precious elements have demonstrated outstanding HER catalytic activities because of their unique physical and chemical properties6,9. For instance, ideal H adsorption energy, high metallicity, and PGM-like electronic configuration along with chemical environmental compatibility have been identified as origins of superior HER activity for metal sulfide/selenides/carbides6,10,11. Among them, two-dimensional (2D) molybdenum disulfide (MoS2) is regarded as a promising alternative to Pt due to its large surface area, near-zero ΔGads, and numerous structure engineering possibilities3,12. The material properties of MoS2 are determined by its polymorph types, namely hexagonal 2H or trigonal 1 T phases. The intrinsically low electrical conductivity arising from the semiconducting nature of the 2H phase hinders the development of MoS2-based electrocatalysts. Tremendous efforts have been devoted to improving the conductivity of 2H-MoS2 via inducing phase transition from semiconducting 2H phase to metallic 1 T phase through ion intercalation, doping engineering, and strain application, etc.13,14,15,16. Among them, solution-phase-based ion intercalation achieved during MoS2 hydrothermal/solvothermal synthesis has been considered as one of the most effective approaches for phase engineering. Compared to multistep electrochemical/chemical intercalations where post-synthetic treatments are normally required, such a process enables ion intercalation along with MoS2 synthesis in a single step one-pot reaction and produces highly active, defect-rich 1 T MoS2 with high surface area, offering significant advantages such as simplicity, low cost, scalability, operational stability, and environmental friendliness due to the use of benign precursors/solvents17. Compared with a hydrothermal synthesis which is widely used for producing various MoS2 structures including nanosheets, nanodots, and nanoflowers with different 1 T phase ratios18, solvothermal synthesis involving the use of bisolvent has been rarely explored. The use of bisolvent will increase the solubility of MoS2 precursors, trigger deep 2H to 1 T phase transition and prevent from undesired oxidation reaction which is of particular importance for sensitive materials, such as MXene.

MXene (Mn+1XnTx, where “M” represents early transition metal, “X” is carbon and/or nitrogen, and Tx is surface functional groups in the chemical formula) is a group of materials consisting of transition metal carbides/nitrides/carbonitrides, which are produced by selectively etching of “A” element from MAX phase (“A” is group IIIA and IVA element)19,20. It has been widely investigated in supercapacitors and aqueous batteries because of its high conductivity, excellent hydrophilicity, and large interlayer distance21,22,23,24. Compared with charge-neutral graphene, MXene exhibits a negatively charged surface due to the existence of enriched surface functional groups, including -OH, -O, and -F, etc.22,25. These surface functional groups will not only enhance the dispersion of precursors but also promote the MoS2 nucleation in bisolvent, making it a superior substrate for the synthesis of MoS226. Especially, oxygen-containing functional groups have been proved with near-zero ΔGads, suggesting potentially catalytic activity for the HER27,28. Recently, 2H-MoS2 has been integrated with different types of MXene using in-situ sulfidation29 and microwave-assisted growth methods26. The hybrid structures delivered an exceptional catalytic activity and durability for HER. Nevertheless, the above-mentioned strategies normally require multiple engineering processes involving complicated experimental setups that are costly and time-consuming. Hydrothermal methods have also been employed to synthesize 2H-MoS2/MXene composites30, but the low electrical conductivity of 2H phase MoS2 is still a limiting factor for the overall catalytic performance.

Herein, we design and construct 1 T phase-enriched MoS2 and Ti3C2Tx MXene composites as HER catalysts using a one-step solvothermal method in a bisolvent media. To further improve the catalyst performance, carbon nanotubes (CNT) are introduced in the hybrid structure as crosslinks. The ternary composite not only improves the overall electrical conductivity but also prevents the undesired oxidation and restacking of 2D materials simultaneously. Moreover, we notice that dual-phase MoS2 (DP-MoS2) nanoflakes are vertically integrated with MXene with the exposure of numerous edge sites which are catalytically active for the HER. As a result, an improved HER activity is achieved compared to pure 2H MoS2 and other binary counterparts. The ternary composite exhibits an overpotential of 169 mV which is achieved at a current density of 10 mA/cm2 and a low Tafel slope of 51 mV/dec with good stability.

## Results

### Preparation of the dual-phase MTC

The dual-phase MoS2/Ti3C2 MXene/CNT (DP-MTC) samples were prepared by a one-step bisolvent solvothermal synthesis technique and the schematic illustration of the preparation procedure can be found in Fig. 1a. Briefly, few-layered MXene flakes were prepared by the in situ HF etching method31. The mixture of MXene and CNT powders were then added into DI water/DMF bisolvent along with ammonium molybdate and thiourea which served as Mo and S sources, respectively. The use of bisolvent is beneficial for promoting MoS2 nucleation by increasing the solubility of MoS2 precursors and improving the conductivity via triggering the 2H to 1 T phase transition through ion intercalation32,33,34. In addition, compared with the pure DI-based hydrothermal method, the adoption of bisolvent will preserve the high conductivity of the MXene matrix by improving the stability of MXene via reducing the undesired oxidation reaction. As shown in Supplementary Figs. 1 and 2, a large amount of TiO2 nanoparticles were found on the surface of the 2H-MoS2/Ti3C2 composite synthesized in DI water along with high oxygen content, which is often observed in the previous reports35,36. By contrast, the bisolvent-produced DP- MoS2/ Ti3C2 (Supplementary Fig. 3) showed fewer TiO2 particles and the oxygen content is much lower, demonstrating successfully suppressed oxidation of MXene.

### Morphology, phase and structure characterization

To confirm the structure and composition of the products, a series of characterizations were conducted. The SEM images of the as-synthesized materials are shown in Fig. 2. The morphologies of the dual-phase MoS2 (DP-MoS2) nanosheets and MXene layers are shown in Fig. 2a, b, respectively. Compared to the pure DP-MoS2 flakes which exhibit a well-defined nanoflower-like structure with the tendency to form aggregated bundles, DP-MoS2 flakes tend to grow in the interlayers as well as the surface of Ti3C2 MXene, as shown in Fig. 2c. Such a sandwiched binary DP-MoS2/Ti3C2 structure will not only prevent the 2D layers from restacking but also protect the environmentally sensitive MXene from oxidation. The morphology of the ternary DP-MTC100 can be found in Fig. 2d, where the three components are clearly observed. The TEM image of DP-MTC100 (see Fig. 2e, more images can be found in Supplementary Fig. 4a) displays a ternary composite consisting of 1D/2D hybrid structures. Although the density of CNTs is low, they served as a crosslink between the 2D islands and led to the formation of a well-connected conductive network, promoting electron transfer efficiency within the whole system. The EDS elemental mapping can be found in the bottom panel of Fig. 2 (Fig. 2h–l) where the uniform distribution of Mo, S, Ti, and C elements are revealed. The interlayer distance of DP-MoS2 in the as-synthesized ternary composite was extracted from the HRTEM image (Fig. 2f) and the value is ~0.98 nm which is clearly larger than the pure 2H-MoS2 obtained from in situ sulfurization method (~0.64 nm)33,34,37. Besides that, the Ti3C2 MXene layers also exhibit an expanded interlayer spacing of ~1.53 nm (Supplementary Fig. 4b) compared to the typical reported value of 1 nm38. The increased interlayer space can be ascribed to the NH4+ ions intercalation and the integrated stacking nature of the 2D layers, which will be discussed in detail later. Moreover, we notice that a large portion of DP-MoS2 flakes is in favor of exposing edge sites (Fig. 2g) in the DP-MTC100 composite, leading to the involvement of numerous catalytic active sites for the future HER test.

Figure 3a shows the XRD patterns of various as-prepared samples. The diffraction pattern of Ti3C2 MXene shows obvious peaks at 9, 18.4, 27.7, and 60.5 degrees, corresponding to (002), (006), (008), and (110) crystal planes31,39. The interlayer distance is extracted to be 0.98 nm and is close to the typical reported value of 1 nm38. The absence of the Al peak at~38 degree suggests the successful etching of the Al layer from the MAX precursor31. Two peaks located at 35.9 and 41.7 degrees come from TiC, which is the impurity in the MAX phase precursors40,41. The DP-MoS2 obtained via bisolvent synthesis exhibits major diffraction peaks at 9, 33.2, and 58.6 degrees, which are corresponding to the (002), (100), and (110) planes, respectively33,42. Compared with the 2H-MoS2 obtained in aqueous solvent (see Supplementary Fig. 5), the (002) peak has downshifted from ~14 degree to 9 degree, suggesting an expanded interlayer spacing. To analyze in detail, the interlayer spacing has been extracted using Bragg’s diffraction equation, and the value is calculated to be 0.98 nm for DP-MoS2, which is 0.34 nm larger than the reported value of 2H-MoS2 (0.64 nm)34. In our bisolvent synthesis process, both ammonium molybdate and DMF can act as the abundant source of NH4+33. Interestingly, the 0.34 nm difference is very close to the size of NH4+ ion (0.35 nm), indicating the expanded interlayer spacing of DP-MoS2 could be attributed to the interaction of NH4+ ions, as indicated in Fig. 1b, c. A similar peak shift has been observed for DP-MoS2/CNT composite as well. In the case of the DP-MoS2/Ti3C2 composite, two peaks located at 6.6 and 8.9 degrees can be clearly identified, corresponding to the (002) planes of Ti3C2 and MoS2 with enlarged interlayer distances of 1.5 nm and 0.99 nm, respectively. This result suggests that the interlayer spacing of both MoS2 and Ti3C2 MXene were expanded simultaneously by forming the MoS2/ Ti3C2 composite with the assistance of ion intercalation and integrated 2D layer stackings. Similar interlayer distance expansion is observed in DP-MTC100, which corresponds well with previous TEM observations in Fig. 2f and Supplementary Fig. 4b. However, compared with the DP-MoS2/Ti3C2, no further (002) peak shift is observed in DP-MTC100, indicating that the addition of CNT does not impact the interlayer distance of MoS2 and Ti3C2 MXene.

The Raman spectra of selected samples are shown in Fig. 3b. In the pure Ti3C2 MXene Raman spectrum, several peaks that appeared at the lower Raman shift region (below 1000 cm−1) can be attributed to the C-Ti vibrations, and the peaks located at 1341 cm−1 and 1583 cm−1 reflect the carbon-based D band and G band vibrations, respectively43,44. The as-synthesized DP-MoS2 sample shows the characteristic E2g and A1g vibration peaks at 378 cm−1 and 405 cm−1, respectively, corresponding to the 2H phase characteristics45. The relative intensity of A1g to E2g peaks provides insightful information related to the MoS2 planes. The out-of-plane A1g vibration mode in MoS2 is preferentially excited for edge-terminated structure due to the polarization dependence46. The A1g/E2g ratio is extracted to be as large as 2, indicating an edge-enriched MoS2 structure (see Supplementary Fig. 6)45. In addition to the 2H peaks, three 1T-MoS2 related peaks (150, 219, and 336 cm−1) are observed which can be ascribed to J1, J2, and J3 vibration modes, respectively47. The coexistence of 1 T and 2H related peaks in the Raman spectrum proves the successful preparation of dual-phase MoS2 using the bisolvent synthesis approach. The broad peak located at 820 cm−1 can be attributed to the slightly oxidized MoS2 product48. In the case CNTs, the peak located at ~1356 cm−1, 1584 cm−1, and 2695 cm−1 can be attributed to the vibration modes of D, G, and G’ bands, respectively49.

The DP-MTC100 sample exhibits both MoS2 related peaks along with CNT-related vibration modes, indicating the successful formation of the ternary composite. It is worth noting that the Ti3C2-related Raman peaks are diminished due to the high surface coverage of MoS2 and the intrinsically weak signal nature of Ti3C2. The unchanged A1g/E2g ratio suggests the edge-enriched MoS2 morphology maintained in the MTC ternary composite, corresponding to the TEM result shown in Fig. 2g. Clear 1T-phase based Raman modes are observed in the MTC hybrid structure (see Supplementary Fig. 6) as well suggesting the coexistence of 2H and 1 T phases in the composite. The formation of the 1 T phase is triggered by the ion intercalation. Specifically, the intercalated NH4 + can stimulate the charge imbalance between Mo3+ and Mo4+ and cause the S plane sliding and therefore the MoS2 crystal structure distortion along with expanded interlayer spacing, resulting in the phase transformation from 2H to 1 T eventually, as shown in Fig. 1c, d. The existence of the 1 T phase is further proved by the HRTEM image of DP-MTC100, as shown in Supplementary Fig. 4c, where the 1 T phase atomic coordination can be clearly identified.

To investigate the chemical composition of the as-synthesized DP-MTC100, XPS analysis was performed. The complete survey spectrum is shown in Fig. 4a where the characteristic peaks of C, O, Mo, S, and Ti can be clearly observed. To analyze the details for each element, peak deconvolution was carried out. As shown in Fig. 4b, four major peaks located at 284.1 eV, 284.85 eV, 285.85 eV and 287.3 eV for C1s spectra can be ascribed to the C-Mo/C-Ti, C-C, C-O, and C=O bonds, respectively, which are the typical bonding structures in MXene and CNT26,50,51. The peaks at 530.9 eV and 531.6 eV in the O1s spectrum (Fig. 4c) originate from the C-Ti-(OH) and C-Ti-O, respectively, corresponding to the –(OH) and -O functional group attached on the Ti3C2 surface26,51. The peak located at 530.1 eV can be assigned to the Ti-O bond which can be ascribed to the oxidation of the Ti3C2 MXene surface during the XPS measurement. In addition, although MXene oxidation is suppressed during the bisolvent synthesis compared to the aqueous-based method (see Supplementary Figs. 1, 2, and 3), a certain degree of undesired oxidation still took place during the solvothermal process. Moreover, two peaks at 532.3 eV and 532.8 eV can be attributed to the presence of Al2O3 related to the incomplete Al layer etching from the MAX phase and the adhesive water associated with the high hydrophilicity of the MXene surface, respectively51. In Fig. 4d, the peaks for Mo4+(d3/2) and Mo4+(d5/2) are located at 231.8 eV and 228. 6 eV, respectively, with an S2+ peak at 225.8 eV. It is noteworthy that a doublet (at 229.6 eV and 233.1 eV) for Mo5+ were observed, which is beneficial for the MoS2 stability52. Besides that, Mo6+ shows a peak at 235.7 eV, suggesting partial oxidation of Mo, corresponding to the Raman observation in Fig. 3b. As for S 2p spectra, two doublets that emerged at 163.5/162.1 eV and 162.7/161.4 eV can be attributed to 2H-MoS2 and 1T-MoS2, respectively, reflecting the successful synthesis of mixed 1 T and 2H phase MoS2, which is in good agreement with the previous TEM and Raman analysis in Supplementary Fig. 4c and Supplementary Fig. 6, respectively. Our calculation based on S 2p peak deconvolution suggested that the content of 1 T phase MoS2 is around 66%, indicating a 1T-phase enriched structure in the dual-phase MoS2. Figure 4f displays the Ti 2p spectra. The doublet located at 464.3 eV and 458.9 eV can be assigned to the Ti-O bond and resonate well with the observation in Fig. 4c. The two peaks at 465.1 eV and 459.4 eV represent the Ti-F bond, which is introduced during the Al layer etching process using HCl/LiF. The Ti-C bond-related peaks are observed at 461.2 eV and 456.6 eV, respectively, which are consistent with previous reports for MXene structures26,50.

### The HER performance and electrochemical characterizations

The electrochemical HER activity exploration of as-synthesized MoS2-based electrocatalysts was conducted in 0.5 M H2SO4 using a standard three-electrode configuration with the built-in IR compensation function. Figure 5a, b display the LSV curves and corresponding Tafel plots of as-prepared samples. The pristine CNT and Ti3C2 MXene show nearly inert HER activity with a horizontal LSV curve pattern, indicating a limited HER activity of CNT and Ti3C2. The DP-MoS2 exhibits a much lower overpotential of 238 mV at a current density of 10 mA/cm2 (η10) and a low Tafel slope of 85 mV/dec due to the higher intrinsic catalytic capability of DP-MoS2 compared to the aqueous-synthesized 2H-MoS2 (Supplementary Fig. 7a, b). The enhanced HER performance can be ascribed to the significantly reduced charge transfer resistance (Rct) associated with the high conductivity of the metallic 1 T phase (Supplementary Fig. 7c). In the case of binary composites, the DP-MoS2/CNT enabled a better HER performance compared with DP-MoS2/Ti3C2, evidenced by a lower overpotential and a smaller Tafel slope (202 mV, 72 mV/dec and 230 mV, 102 mV/dec for CNT and Ti3C2 composites, respectively), which can be attributed to the smaller Rct of DP-MoS2/CNT (see Fig. 5c) because of the higher conductivity of CNT with respect to Ti3C221,53 and the crosslink function of CNTs bridging different 2D MoS2 islands (see Fig. 2e) for a universal conductive network formation. Among all the structures, MTC100 exhibits the lowest η10 of 169 mV and the smallest Tafel slope of 51 mV/dec, which can be associated with the smallest Rct (see Fig. 5c) originated from the highest overall electrical conductivity via constructing a 1T-phase enriched MoS2-based 1D/2D hybrid network. It is worth mentioning that the MTC100 shows excellent performance reproducibility. The overpotentials were found to be 169 ± 5 mV for four different catalyst inks fabricated using the same batch of MTC100 sample that has been stored for around 1 year.

The CV was carried out to determine the double-layer capacitance (Cdl) and to calculate the electrochemical surface area (ECSA), as shown in Supplementary Fig. 8. The measured Cdl for Ti3C2 MXene, DP-MoS2, DP-MoS2/Ti3C2, DP-MoS2/CNT and MTC100 is 36, 6, 34, 27 and 44 mF/cm2, and the corresponding ECSA are calculated to be 882, 144, 838, 676, and 1099 cm2, respectively (see Supplementary Table 1). The BET specific surface area was also tested by N2 adsorption/desorption isotherm, as shown in Supplementary Fig. 9a. The result shows that MTC100 contains the largest surface area of 32 m2/g, which is larger compared to the other binary composites (DP-MoS2, DP-MoS2/Ti3C2, and DP-MoS2/CNT exhibit the BET area of 21, 18, and 28 m2/g, respectively). As can be seen in Supplementary Fig. 9b, the pore size lies in the range of 10~50 nm, suggesting a mesopore-enriched structure of the DP-MoS2 hybrids54. The enriched porosity feature can be attributed to the gas evolution during the solvothermal synthesis of the flower-shaped MoS2-based hybrid structure and the integrated stacking nature of the 2D MoS2/MXene layered hybrids17,32,55,56,57. The turnover frequency (TOF) is another vital parameter to evaluate the activity of an HER electrocatalyst which characterizes the intrinsic activity of an electrocatalyst at a single active site. By combining the TOF with overpotential, it can provide a more comprehensive and in-depth view of the kinetics and a robust basis of catalytic benchmarking58. The TOF values of the above-mentioned samples were calculated based on the CV measurement in a pH-neutral phosphate buffer solution and were plotted in Fig. 5d in the range of 0.2~0.23 V. It is worth mentioning that the TOF of DP-MoS2/CNT is lower than that of DP-MoS2/Ti3C2 despite the smaller Rct as shown in Fig. 5c, which is due to CNTs exhibit inherently low catalytic activity (see Fig. 5a) and limited contribution to the interlayer spacing expansion and surface area enlargement (see Fig. 3a, Supplementary Fig. 8, and Supplementary Fig. 9). Among all the samples, DP-MTC100 exhibits a superior TOF corresponding to the observed higher catalytic activity compared to the other DP-MoS2-based binary composites. The origin of the outstanding HER performance for the ternary composite lies in threefold: (i) the enlarged surface area due to the 2D/2D MoS2/Ti3C2 integration and ion intercalation which promotes the contact between electrolyte and catalyst, leading to an increased hydrogen ion adsorption; (ii) the vertically grown MoS2 flakes on the Ti3C2 template ensures the maximum exposure of MoS2 edge planes which is beneficial to increase the total number of active sites; (iii) the synergistically enhanced conductivity due to the existence of 1T-phase enriched metallic MoS2, the conductive backbone of Ti3C2 along with the crosslink function of CNTs, minimizing the charge transfer resistance at the electrode/electrolyte interface.

To investigate the cycling stability, the CV measurements between −0.2 and 0.3 V were performed and the polarization curves before and after cycling are shown in Fig. 5e. A negligible shift of the polarization curve after 1000 CV cycles was observed, suggesting a long lifetime of DP-MTC100 in the acidic media. The superior ternary catalyst stability is benefited from the integration of MoS2 with Ti3C2 which not only partially suppressed the Ti3C2 oxidation but also prevent the 2D layer restacking. In addition, it is known that the 1 T phase MoS2 is metastable and easily converted to the stable 2H phase, leading to the performance degradation of 1 T metallic MoS2-based devices13,59. In our case, the NH4+ intercalation can serve as the electron donor to stabilize the 1 T phase and therefore reduce the tendency of phase conversion60. The ultralong time stability of DP-MTC100 is again confirmed by the time-dependent stability measurement as shown in Fig. 5f. The current density was measured at an overpotential of 169 mV and was stabilized at near 10 mA/cm2 for 72 h. The stability retention was extracted to be 95% at the 30 h and 77% at the 72 h, respectively. Nevertheless, activity loss can still be observed since the slow phase conversion of 1 T to 2H and the mild oxidation of the structure still take place to a certain degree inevitably in a long run.

### HER performance evaluation of MTC hybrids with different CNT ratios

To optimize the HER activity, we synthesized four different ternary DP-MTC samples with different weights of CNTs (50, 70, 100, and 200 mg). As shown in Fig. 6, the MTC100 outperforms the other ternary hybrids, evidenced by the smallest overpotential (169 mV) and a small Tafel slope (51 mV/dec). It is noteworthy that MTC200 displays an even smaller Tafel slope (49 mV/dec) and the lowest Rct value among the ternary composites (see Fig. 6b, c), which can be ascribed to the higher ratio of CNTs that further enhanced the network conductivity and therefore charge transfer efficiency during the reaction. However, the TOF of MTC200 is one of the smallest among different CNT composites along with a large overpotential (216 mV), as shown in Fig. 6a, d. It is well known that the number of active sites and the electrical conductivity are two vital factors for determining the HER activity of the electrocatalyst. In our case, the conductivity of the ternary composites improved significantly by adding more CNTs. However, the intrinsically low catalytic activity of CNT (see Fig. 5a) and its limited contribution to the surface area enlargement impacts the HER activity adversely. In addition, the relatively high CNT ratio will decrease the content of DP-MoS2, leading to a decreased total number of active sites and therefore the catalytic activity correspondingly. Overall, the MTC100 provides a well-balanced relationship between the electrical conductivity and the number of active sites and therefore delivered the best catalytic performance for HER.

## Discussion

In summary, we successfully synthesized a ternary, dual-phase MoS2/Ti3C2/CNT structure by a one-step solvothermal technique, and investigated its HER activity. Such a ternary hybrid composite exhibited superior structure advantages compared to the other binary counterparts in terms of enlarged surface area, increased number of active sites, and a well-constructed 1D/2D hybrid conductive network. The 2D domains of metallic phase-enriched MoS2 and the Ti3C2 conductive backbone were bridged by the 1D CNTs and therefore synergistically boosted the overall network conductivity. The composition-performance relationship interrogation revealed that the amount of CNTs in the composite is a determining factor for HER performance. The long-term catalytic stability was also achieved by the integration of MoS2 with Ti3C2 in bisolvent media which effectively prevented the 2D layer restacking and partially suppressed the Ti3C2 oxidation. Our work demonstrated an effective strategy for low-dimensional material structure-property engineering with the aim of optimizing the device performance and shedding light on the development of the next-generation PGM-free HER electrocatalysts.

## Methods

### Materials

Anhydrous ethanol, lithium fluoride (LiF), hydrochloric acid (HCl), ammonium molybdate, thiourea and N, N-dimethylformamide (DMF) were purchased from Fisher Scientific, USA. Ti3AlC2 was purchased from Beijing Forsman Scientific Co. Ltd., China. Multiwalled carbon nanotubes (CNT) were purchased from XFNANO, China. All chemicals were used as received without any further purification.

### Preparation of Ti3C2 MXene

The Ti3C2 was prepared by the in situ HF etching method31. Specifically, 2 g LiF powder was slowly added into 40 ml HCl (9 M) solution and stirred for 30 min until the LiF was fully dissolved. 2 g Ti3AlC2 was slowly added into the LiF/HCl mixture which was placed in an ice bath subsequently. The solution was kept at 40 ˚C for 48 h with continuous stirring. After the reaction, the black powder was collected by centrifugation and washed with DI water until the supernatant reached a pH value of 6. The powder was dried under vacuum at 60 ˚C for 12 h.

### Synthesis of the dual-phase MoS2/Ti3C2/CNT (DP-MTC) ternary composite

1 g of as-prepared Ti3C2 powder and 0.1 g CNT were added into 60 mL DI/DMF (volume ratio 1:1) bisolvent, followed by ultrasonication to form a homogenous suspension. 1.928 g ammonium molybdate and 3.645 g of thiourea were slowly added into the suspension and stirred until the precursors were well mixed. The suspension was then transferred into a 100 mL Teflon-lined autoclave and kept at 195 ˚C for 22 h. After naturally cooling down to room temperature, the product was collected by centrifugation and washed with DI/ethanol, followed by vacuum drying at 60 ˚C for overnight. The as-prepared sample was denoted as DP-MTC100 where the number indicated the weight of CNT (100 mg). Different binary composites (MoS2/Ti3C2, MoS2/CNT) and MTC hybrid structures with different MXene to CNT ratios were also synthesized as control samples. To evaluate the influence of bisolvent impact in the synthesis, the MoS2 powder and MoS2/Ti3C2 composite (denoted as 2H-MoS2 and 2H-MoS2/Ti3C2, respectively) was also synthesized with the same precursor concentration in DI water as a reference sample.

### Characterization

X-ray diffraction (XRD) was performed using a Rigaku Ultima IV with Cu Ka radiation (wavelength = 1.541 nm). Raman spectra were collected using Renishaw InVia with an excitation laser wavelength of 514 nm. The morphologies of all products were investigated by field-emission scanning electron microscope (FE-SEM, Carl Zeiss AURIGA CrossBeam with Oxford energy dispersive x-ray spectra (EDS) system). The transmission electron microscopy (TEM) was conducted using the JEM ARM 200 F system. X-ray photoelectron spectroscopy (XPS) was performed using a monochromatic Al Kα source (hv = 1486.6 eV) (ESCALAB 250, Thermo Scientific). The Brunauer-Emmett-Teller (BET) measurements were conducted on a Micromeritics Tri-Star II system by nitrogen (N2) adsorption-desorption isotherm at 77 K.

### Electrochemical measurements

The ink for the HER test was prepared by dissolving 10 mg of as-prepared powder in a mixture of 500 µL of ethanol, 500 µL of DI water, and 15 µL of Nafion D-521 solution. The electrochemical characterization was performed using CHI760E electrochemical workstation (CH Instrument) in a standard three-electrode system which consists of a silver/silver chloride (Ag/AgCl in 1 M KCl), a platinum (Pt) wire, and an ink-coated glassy carbon rotating ring disc electrode as reference, counter and working electrodes, respectively. The loading amount of the sample is 0.285 mg/cm2 and the samples were cycled 20 times before any data recording. Nitrogen gas saturated 0.5 M H2SO4 was employed as electrolyte. All the measured potentials were converted to the potential vs. ERHE based on the equation: ERHE = EAg/AgCl + 0.059 pH + 0.222. The linear sweep voltammetry (LSV) was carried out at a scan rate of 5 mV/s and the built-in IR compensation was executed prior to LSV tests. The electrochemical impedance spectroscopy (EIS, Biologic VMP3) was conducted from 0.1 Hz to 1 MHz with an amplitude of 5 mV at an overpotential of 250 mV vs. RHE. The electrochemical surface area was tested by cyclic voltammetry (CV) in the potential range of 0.05–0.15 V vs. RHE with different scan rates (20, 40, 50, 60, 80, and 100 mV/s). The double-layer capacitance (Cdl) was assessed from the slope of the linear regression between the current density differences (∆J/2 = (Janode-Jcathode)/2 at an overpotential of 0.1 V vs. RHE) versus the scan rates. The accessible surface area of as-synthesized samples could be approximated from the electrochemical active surface area (ECSA). The ECSA was determined by ECSA = Cdl/Cs, where Cs stands for the specific capacitance of standard electrode materials on a unit surface area. Here, based on the literature reported Cs values for carbon electrode materials, 0.04 mF/cm2 was used for ECSA calculations61. CV was performed between −0.3 V and 0.2 V vs. RHE to check the cycle stability.

## Data availability

All data generated or analysed during this study are included in this published article (and its supplementary information files).

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## Acknowledgements

This work was partially supported by New York State Energy Research and Development Authority (NYSERDA) under Award 138126, the New York State Center of Excellence in Materials Informatics (CMI) under Award C160186, and the National Science Foundation (NSF) under Award ECCS-1944095. The authors acknowledge support from the Vice President for Research and Economic Development (VPRED) at the University at Buffalo.

## Author information

Authors

### Contributions

S.C.W. Y.F., M.M.L., and H.Y.Y. conducted the material synthesis and characterization. S.W.P. and Y.H.L. performed the TEM characterization. H.M.L. and F.Y. guided the project and wrote the paper. All authors reviewed the paper.

### Corresponding authors

Correspondence to Huamin Li or Fei Yao.

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### Competing interests

The authors declare no competing interests.

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Wei, S., Fu, Y., Liu, M. et al. Dual-phase MoS2/MXene/CNT ternary nanohybrids for efficient electrocatalytic hydrogen evolution. npj 2D Mater Appl 6, 25 (2022). https://doi.org/10.1038/s41699-022-00300-0

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• DOI: https://doi.org/10.1038/s41699-022-00300-0