Nano Convergence

Nano Convergence Cover Image
Review
Open Access

Recent advances in unveiling active sites in molybdenum sulfide-based electrocatalysts for the hydrogen evolution reaction

Nano Convergence20174:19

https://doi.org/10.1186/s40580-017-0112-3

©  Korea Nano Technology Research Society 2017

Received: 10 June 2017

Accepted: 7 July 2017

Published: 25 July 2017

Abstract

Hydrogen has received significant attention as a promising future energy carrier due to its high energy density and environmentally friendly nature. In particular, the electrocatalytic generation of hydrogen fuel is highly desirable to replace current fossil fuel-dependent hydrogen production methods. However, to achieve widespread implementation of electrocatalytic hydrogen production technology, the development of highly active and durable electrocatalysts based on Earth-abundant elements is of prime importance. In this context, nanostructured molybdenum sulfides (MoS x ) have received a great deal of attention as promising alternatives to precious metal-based catalysts. In this focus review, we summarize recent efforts towards identification of the active sites in MoS x -based electrocatalysts for the hydrogen evolution reaction (HER). We also discuss recent synthetic strategies for the engineering of catalyst structures to achieve high active site densities. Finally, we suggest ongoing and future research challenges in the design of advanced MoS x -based HER electrocatalysts.

Keywords

Hydrogen evolution reaction Molybdenum sulfide Electrocatalyst Active site Synthetic strategy Structure engineering Phase engineering

1 Introduction

Hydrogen is a sustainable and renewable energy carrier that has demonstrated potential as an alternative to fossil fuel energy sources [1, 2]. Currently, hydrogen is produced mainly by steam methane reforming and coal gasification, leading to the ensuing problem of CO2 release [3, 4]. To provide a more environmentally friendly route to hydrogen power, the development of clean hydrogen production technology is required. Electrocatalytic water splitting represents the most promising solution for producing hydrogen using a carbon-free system [5, 6]. However, the dominant use of Pt-based catalysts for the hydrogen evolution reaction (HER) hinders the widespread implementation of electrocatalytic hydrogen production systems, due to their high costs and limited abundance. Hence, there have been significant efforts to replace Pt-based catalysts with highly active, durable, and non-precious electrocatalysts for the HER [7–19]. Notable examples of non-precious metal catalysts include metal sulfides, metal phosphides, metal carbides, and heteroatom-doped carbons. Among the various classes of non-precious metal-based electrocatalysts [7–82], nanostructured molybdenum sulfides (MoS x , x = 2–3) have been most widely studied, owing to their high activities, excellent stabilities, and precious metal-free compositions [7–68]. Although bulk MoS2 exhibits negligible catalytic activity for the HER [83], pioneering theoretical and experimental works by Nørskov and Chorkendorff have demonstrated that nanostructured MoS x catalysts are able to catalyze the HER with high efficiency [20, 21]. During the last decade, significant progress has been made in designing MoS x catalysts at the nanoscale, which has resulted in advanced MoS x -based catalysts with enhanced HER performances.

In this review, we highlight the key findings reported to date regarding identification of the active sites of MoS x catalysts, and synthetic strategies for engineering their structures to yield high active site densities for the HER. Over the past decade, there have been a number of important developments relating to the active sites present in MoS x catalysts. For example, the edge of MoS2 was first proposed as a catalytic active site by theoretical calculations in 2005 [20], which was later experimentally demonstrated with a model catalyst composed of MoS2 nanoparticles grown on a Au(111) surface [21]. Since then, various studies focused on maximizing active edge site densities via structural engineering approaches of MoS x catalysts, including space-confined growth [22–25], vertical alignment [26–28], nano-assembly [29–31], and the design of biomimetic molecular catalysts [32–34]. The basal planes of MoS2, which were believed to be inert in the HER, have also been successfully activated to show meaningful activity by several strategies, including phase engineering from the 2H phase to the metallic 1T phase [26, 35–38], heteroatom doping [39–41], defect site generation [42–47], and strain engineering [40, 48, 49]. Despite significant investigations into the structural engineering of MoS2-based electrocatalysts to enhance the HER performance, a number of questions remain regarding the active sites and reaction mechanisms. For example, in the case of the amorphous MoS x , identification of its active sulfur sites for hydrogen adsorption has not yet been clarified due to its structural complexity [50–54].

In this review, we first discuss the basic concepts for the electrocatalytic production of hydrogen, in addition to the activity parameters commonly employed for evaluation of the HER activity. We highlight a number of important results regarding the active sites of MoS x -based HER catalysts, and summarize representative synthetic strategies for engineering their structures to enhance the number of active sites in different 2H-MoS2, 1T-MoS2, and amorphous MoS x structures. We conclude the review by highlighting the current challenges and future research directions in relation to MoS x -based HER catalysts.

2 Hydrogen evolution reaction

2.1 Hydrogen evolution from water

The electrocatalytic production of hydrogen via water splitting is composed of two half reactions:

$$\begin{aligned} {\text{Anode}}{:} \, & 2 {\text{H}}_{ 2} {\text{O }} \leftrightarrow {\text{ O}}_{ 2} + {\text{ 4H}}^{ + } + {\text{ 4e}}^{ - } \left( {{\text{oxygen evolution reaction}},\,{\text{OER}}} \right) \\ & {\text{E}}_{\text{a}} = { 1}. 2 3 {\text{ V}} - 0.0 5 9\cdot{\text{pH }}\left( {{\text{V vs}}.{\text{ normal hydrogen electrode}},\,{\text{NHE}}} \right) \\ \end{aligned}$$
$$\begin{aligned} {\text{Cathode}}{:} \,& 4 {\text{H}}^{ + } + {\text{ 4e}}^{ - } \leftrightarrow {\text{ 2H}}_{ 2} \left( {{\text{hydrogen evolution reaction}},\,{\text{HER}}} \right) \\ &{\text{E}}_{\text{c}} = \, 0{\text{ V}} - 0.0 5 9\cdot{\text{pH }}\left( {{\text{V vs}}.\,{\text{NHE}}} \right) \\ \end{aligned}$$
In this review, we will focus on the HER taking place at the cathode. Thermodynamically, the HER occurs with 0 V (vs. reversible hydrogen electrode, RHE) of applied potential, as shown in Fig. 1. However, for practical operations, a large excess potential, i.e., the overpotential (η c ), is required, and the development of highly efficient HER electrocatalysts is directly linked to the reduction of the overpotential.
Fig. 1

I-V curve for the full water splitting reaction

2.2 HER activity parameters

2.2.1 Overpotential to drive a current density of −10 mA cm−2

Generally, the comparison of HER activities has been made in terms of the overpotential at a current density of −10 mA cm−2. This current density corresponds to an efficiency of approximately 10% in solar-to-fuel devices [84], and the derivation is as follows:
  1. 1.

    Integration of the solar spectrum (AM1.5G) yields a value of 100 mW cm−2, referred to as “1 sun”.

     
  2. 2.

    As the redox potential for water oxidation is ~1.2 V, an 100% efficient solar-to-fuel device would give 100 (mA V cm−2)/(1.2 V) = 83 mA cm−2 under AM1.5G.

     
  3. 3.

    Thus, a 10% efficient solar-to-fuel device would give 8.3 mA cm−2.

     

Therefore, the ranking of HER catalysts by comparison of the overpotentials required to drive a current density of −10 mA cm−2 is reasonable in a practical context.

2.2.2 Tafel slope

The Tafel slope is an important kinetic parameter, and is derived from the equation:
$$\left| \eta \right| = \frac{2.3RT}{\alpha nF}log\frac{J}{{J_{0} }}$$
where η is the overpotential, R is the ideal gas constant, T is the absolute temperature, α is the electrochemical transfer coefficient, n is the number of electrons involved in the electrode reaction, F is the Faraday constant, J is the measured current density, and J 0 is the exchange current density. In addition, J 0 is related to the electron-transfer rate of the reaction, reflecting the intrinsic catalytic activity of the catalyst. From the above equation, the Tafel slope is defined as \(\frac{2.3RT}{\alpha nF}\) and bears the units mV dec−1. The Tafel slope is therefore determined from the linear regression line of the Tafel plots (η vs. logJ), which can be derived from the I-V polarization curve.

The Tafel slope has been used to access the HER mechanism taking place. More specifically, in an acid, the HER proceeds by the initial adsorption of a hydrogen atom on the catalyst surface \(({\text{H}}_{{({\text{aq}})}}^{ + } + {\text{ e}}^{ - } \leftrightarrow {\text{H}}_{\text{ad}} )\), which is referred to as the Volmer step. Subsequently, molecular hydrogen is produced via the chemical recombination of two Had atoms (2Had ↔ H2 (g); the Tafel step), or through a second electron transfer (\(({\text{H}}_{{({\text{aq}})}}^{ + } + {\text{ H}}_{\text{ad}} + {\text{ e}}^{ - } \leftrightarrow {\text{H}}_{{ 2 { }({\text{g}})}}\); the Heyrovsky step) [7].

The HER following the Volmer–Tafel mechanism gives rise to Tafel slope of 29 mV dec−1, whereas the HER via the Volmer–Heyrovsky mechanism yields 38 mV dec−1. In both cases, the combination of two hydrogen atoms is the rate-determining step with lower value indicating faster reaction rate. When the Volmer step is the rate-determining step or the catalyst surface coverage is close to 1, the Tafel slope increases to 116 mV dec−1. The most of MoS x catalysts have shown Tafel slopes in the range of 60–100 mV dec−1, following the Volmer–Heyrovsky mechanism.

2.2.3 Turnover frequency

The precise evaluation of each surface site’s activity is important to obtain a fundamental understanding of the origin of catalytic activity. The intrinsic activity can be assessed by calculating the turnover frequency (TOF), which is defined as the turnover rate per surface active site. While the comparison of TOFs is meaningful, a fair comparison of TOFs has not yet been carried out due to variations in methods for measuring the active sites in addition to the issues associated with different catalyst structures.

Depending on which sites are assigned as active centers, the TOF can be varied by many orders of magnitude. Theoretically, it is widely accepted that hydrogen atoms bind to surface S sites. However, the majority of studies have calculated TOFs by assuming that surface Mo atoms are the active sites, as the multiple chemical states for S render the calculation difficult. An alternative method is measuring an electrochemically active surface area (ECSA), which can probe all catalytically active surface sites, except the inert areas. Indeed, in some cases, ECSA-derived TOFs have afforded a fairer comparison between different electrocatalysts [80, 82].

It should be noted that the main active sites can differ according to the catalyst structure. For example, only edge sites are active in 2H-MoS2, while both edge and basal sites are active in 1T-MoS2. For amorphous MoS x catalysts, the identification of active sites have been difficult due to complexity of their structures. Therefore, a standard method for TOF calculations should be established for fair comparison of MoS x catalysts with different catalyst structures.

2.2.4 Gibbs free energy

The Gibbs free energy (∆G H) for atomic hydrogen adsorption has been widely used as an activity descriptor for HER catalysts. According to the Sabatier principle, particularly strong or weak interactions between reaction intermediates and catalysts can lower the overall catalyst efficiency. The HER activity therefore exhibits a volcano-shaped relationship as a function of ∆G H [21]. Among the various catalysts examined, Pt catalyst exhibits the highest HER performance, with a ∆G H value close to zero. It has been employed as a figure-of-merit for examining the HER performances of newly developed electrocatalysts. Generally, ∆G H values are deduced by theoretical calculations using a simplified model to reflect the experimental conditions.

3 Active sites in molybdenum sulfides

3.1 Active edge sites

The active edge sites of MoS x -based HER electrocatalysts bear a remarkable resemblance to those of the nitrogenase and hydrogenase enzymes, which exhibit excellent activities and selectivities in their natural systems (Fig. 2a) [20]. To date, considerable progress has been made to synthesize highly active and stable heterogeneous electrocatalysts whose structures mimic the active sites of such natural catalysts [32–34]. In 2005, theoretical calculations by Nørskov and coworkers revealed that the ∆G H value of the MoS2 edge is almost thermo-neutral, suggesting that the MoS2 edge is a highly plausible active site for the HER (Fig. 2b) [20]. Indeed, this was demonstrated experimentally using a model catalyst comprising MoS2 nanoparticles grown on a Au(111) surface (Fig. 2c) [21]. This work revealed that the electrochemical HER activity exhibits a linear correlation with edge length of MoS2 (Fig. 2d). These pioneering works have provided an important evidence that the active sites of MoS2 are located at the edge planes. Since these findings were reported, significant advances have been achieved in increasing the density of active edge sites [22–34], as will be discussed in Sect. 4.1.
Fig. 2

a Active sites of the nitrogenase and hydrogenase, and depiction of the Mo-edge on MoS2 slab. b Free energy diagram for hydrogen adsorption. c STM image of MoS2 nanoparticles on a Au(111) surface. d The exchange current density versus the MoS2 edge length

(Figures reprinted with permission from Refs. [20, 21])

Depending on the size of the MoS2 nanosheets employed, the edges of MoS2 can be covered with 0, 50, 75, or 100% sulfur atoms [55, 85, 86], where the sulfur coverage on the edges can significantly affect the adsorption of H atoms, which is directly correlated to HER kinetics. DFT calculations revealed that the most favorable edge configurations correspond to Mo edges covered by 50% S, where ∆GH = 0.06 eV [87]. In addition to the sulfur coverage, the hydrogen coverage on the edges is also an important factor to determine the hydrogen binding energy [88].

3.2 Active sites in 2H- and 1T-MoS2

MoS2 has several polymorphs with distinct atomic configurations and electronic structures. Among these polymorphs, 2H-MoS2 and 1T-MoS2 structures are the most widely investigated for use as electrocatalysts in the HER. These polymorphs exhibit trigonal prismatic and octahedral unit cell structures, respectively (Fig. 3a–c) [17]. In addition, 1T-MoS2 has a dense atomic configuration in the basal surfaces and a high electronic conductivity, which is six orders of magnitude greater than that of 2H-MoS2, thereby resulting in an enhanced HER performance of 1T-MoS2 compared to 2H-MoS2. However, the preparation of 1T-MoS2 is more complicated than that of 2H-MoS2, due to its metastable nature. In this regard, significant efforts have been directed to prepare the stable and highly pure 1T-MoS2 polymorph using chemical Li-intercalation [35, 36], electrochemical Li-intercalation [26, 37], and a pressurized hydrothermal process [38]. For example, The Chhowalla group prepared the 1T phase MoS2 through an exfoliation reaction using lithium borohydride, where a significantly higher yield was obtained than that using n-butyllithium (i.e., 80% vs. ~50%) [36]. Using the exfoliated 1T-MoS2 sample, the main active sites of the two polymorphs, i.e., 2H-MoS2 and 1T-MoS2, were compared. Upon partial oxidation of the edges, the HER activity of 2H-MoS2 was significantly reduced, while that of 1T-MoS2 remained unaffected, suggesting that the main active site of the 2H-MoS2 polymorph is located at the edge sites, while that of 1T MoS2 may be located at basal sites. (Fig. 3d, e).
Fig. 3

a Unit cell structures of 2H-MoS2 and 1T-MoS2. HRTEM images for b 2H-MoS2 and c 1T-MoS2. d Schematic representation of the oxidation process and partial restoration of the MoS2 edges after several voltammetric cycles. e HER polarization curves of 1T and 2H MoS2 before and after edge oxidation. Dashed lines indicate the iR-corrected polarization curves

(Figures reprinted with permission from Refs. [17, 35, 36])

3.3 Activating inert basal sites

The basal plane of the 2H-MoS2 polymorph has long been considered inert towards the HER, essentially rendering the large basal surface useless. However, several theoretical calculations have suggested that the inert basal planes of MoS2 can be exploited as potential active sites following activation by heteroatom doping, defect site generation, and strain engineering (Fig. 4) [39–49]. For example, heteroatom doping into MoS2 can produce high dopant concentrations on the surface, thereby modifying the hydrogen absorption strength of nearby surface atoms (Fig. 4a). More specifically, Du and co-workers suggested that doping MoS2 with a heteroatom in combination with a small compressive strain can yield an ideal ∆G H for hydrogen binding in the HER (Fig. 4b, c) [40]. In addition, defects are known to perturb the local density of states, creating additional energy levels below the conduction bands [89]. In this context, Wang and co-workers evaluated the effect of sixteen different structural defects on activating the basal plane of MoS2 monolayers (Fig. 4d) [43]. The theoretical results suggested that six defects, including sulfur vacancies, greatly enhanced the HER performance of MoS2 (Fig. 4e). These theoretical findings were later verified experimentally, as discussed in Sects. 4.3 and 4.4.
Fig. 4

a The volcano-shaped relationship between the (log(i0)) and ∆G H. Free energy diagram for the HER on b Rh-doped MoS2, and c Ag-doped MoS2, at different strains. d 16 Examples of different structural defects. e ∆G H of the HER process on each defect region

(Figures reprinted with permission from Refs. [39, 40, 43])

3.4 Active sites in amorphous MoS x

In addition to the crystalline MoS2 structure, amorphous MoS x has attracted significant attention due to its facile preparation under mild conditions, such as wet chemical synthesis [60] and electrodeposition [58, 59, 61]. Unlike MoS2, the active sites present in amorphous MoS x have received little attention due to the complex polymeric structure of such compounds (Fig. 5a) [52]. It contains short-range atomic arrangements with [Mo3S13]2− clusters as building units (Fig. 5b). Similar to MoS2, the question of active sites on amorphous MoS x has been unavoidably and continuously raised. Recently, the sulfur atoms present in amorphous MoS x have been directly confirmed as the catalytic active sites for the HER via operando Raman spectroscopic analysis [54]. However, the sulfur atoms exist in four key states, namely bridging S2 2−, terminal S2 2−, unsaturated S2−, and apical S2−. Due to the diverse sulfur chemical states present in the amorphous MoS x , identification of the catalytically active sulfur sites for proton reduction is challenging. Interestingly, Yeo and co-workers reported a linear correlation between TOFs for the HER and the percentage of S species with higher electron binding energies using X-ray photoelectron spectroscopy (XPS) (Fig. 5c) [53]. This work suggested bridging S2 2− species as the potential catalytic active sites. In addition, Yano and Hu and co-workers investigated the structural changes taking place in the amorphous MoS x under HER conditions using in situ X-ray absorption spectroscopy (Fig. 5d) [51]. They proposed a reaction mechanism, where the catalytic species is similar to MoS2, which corroborates an earlier result by Nilsson and Jaramillo and co-workers [50]. Although significant efforts have been devoted to revealing the active sites for proton reduction, the identification and confirmation of genuine catalytically active sulfur sites remain elusive.
Fig. 5

a Coordination polymeric structure of the amorphous MoS x containing [Mo3S13]2− building blocks. b Arrangement of the cluster units in a 1D unfolding chain. c TOFs versus the percentage of S atoms with high electron binding energy. d Proposed catalytic cycle for the HER over amorphous MoS x

(Figures reprinted with permission from Refs. [51–53])

4 Synthetic strategies for increasing active site densities

4.1 Nanospace-confined growth

Reducing the particle size of MoS2 is the most straightforward method that can increase the density of active edge sites. However, thermodynamics tends to favor growth through the basal plane because the formation of edge sites is highly energetic due to the under-coordinated atomic configuration. To overcome this challenge, confinement growth within a nanospace has been reported [22–25]. The Jaramillo group successfully synthesized a mesoporous MoS2 structure using a silica template with double-gyroid (DG) morphology (Fig. 6a) [22]. The resulting DG MoS2 structure exhibited a high surface curvature, thereby exposing a large fraction of active edge sites. The DG MoS2 exhibited a higher HER performance than high aspect-ratio core–shell MoO3–MoS2 nanowires (Fig. 6b). In addition, the DG MoS2 gives a Tafel slope of 50 mV dec−1, which is relatively low compared to previously reported MoS2-based HER catalysts (Fig. 6c). In this direction, our group prepared layer number-controlled MoS2 nanosheets using the nanospace confined-growth approach [23]. In this work, the pores of mesoporous silica templates were partially filled with carbon, and MoS2 structures were subsequently grown inside the residual nanospace of the silica-carbon composites. After the etching of silica template, MoS2 nanostructures embedded in the frameworks of ordered mesoporous carbons (MoS2@OMC) were generated. As shown in the TEM images (Fig. 6d), the formation of an extended basal plane was successfully hindered with a size <5 nm in the lateral direction. It was found that the TOF increased upon decreasing the layer number in MoS2, and this trend in activity could be correlated to the physical and chemical properties of MoS2 nanoplates (Fig. 6e). These results indicate that space confinement growth paves the way to controlling the surface structure and size of MoS2 at the nanoscale to ultimately develop effective catalysts with high densities of active edge sites at the surface.
Fig. 6

a Synthetic procedure and structural model for the mesoporous MoS2 with a double-gyroid (DG) morphology. b Cyclic voltammogram of DG MoS2 (1 min sample) versus core–shell MoO3-MoS2 nanowires (NW) at 5 mV s−1. c Tafel plot of DG MoS2 (1 min sample) versus core–shell MoO3-MoS2 NW. d Synthetic procedure for the MoS2 nanosheets embedded on ordered mesoporous carbon nanorods (MoS2@OMC), and TEM images for 1L-, 2L-, 3L-, and 4L-MoS2@OMC. e TOFs versus the number of layers in the MoS2

(Figures reprinted with permission from Refs. [22, 23])

4.2 Phase engineering

As mentioned in Sect. 3.2, the active sites, which were limited to the edges in 2H-MoS2, have been expanded to basal surfaces via phase engineering from trigonal prismatic (2H-MoS2) to metallic octahedral (1T-MoS2) structures (Fig. 7a, b). For example, the Jin group demonstrated that the chemical exfoliation of 2H-MoS2 using n-butyllithium significantly enhances the HER activity through the formation of metallic 1T-MoS2 [35]. This phenomenon was ascribed to the fast electron transport and increased number of active sites guaranteed by the metallic 1T-MoS2 nanosheets. These 1T-MoS2 nanosheets required a low overpotential of 187 mV to drive a current density of −10 mA cm−2, compared to ~313 mV for 2H-MoS2 (Fig. 7c). Furthermore, the Tafel slope of 43 mV dec−1 for 1T-MoS2 was significantly lower than that of 2H-MoS2 (i.e., 110 mV dec−1), indicating fast HER kinetics in 1T-MoS2 (Fig. 7d). As an alternative phase engineering technique, the Cui group reported the use of an electrochemical Li intercalation method to generate the 1T-MoS2 phase (Fig. 7e) [26]. This method allowed the vertically-aligned 2H-MoS2 to be converted into 1T-MoS2, which exhibited an enhanced HER performance (Fig. 7f, g). In addition to the intercalation of Li ions, mechanical strains also induced the partial formation of 1T-MoS2 structures, thereby activating the HER [67]. However, despite numerous reports focusing on the use of phase engineering to enhance HER performances, the origin of the HER activity has not yet been completely elucidated. Decoupling of the intrinsic activities of 1T phase from the overall HER activity is required to reach a fundamental understanding of the active sites present in MoS2 polymorphs.
Fig. 7

Dark-field scanning transmission electron microscopy images of a 2H-MoS2, and b 1T-MoS2. c Polarization curves of the 2H- and 1T-MoS2 for the HER, and d the corresponding Tafel plots. Filled symbols indicate the iR-corrected data. e Galvanostatic discharge curve representing the lithiation process. f Polarization curves of the pristine and lithiated MoS2 for the HER, and g the corresponding Tafel plots

(Figures reprinted with permission from Refs. [9, 26, 35])

4.3 Heteroatom-doping

The incorporation of heteroatoms into the basal surface of MoS2 nanosheets can significantly modify the electronic structure of in-plane S atoms neighboring the heteroatom, thereby altering the adsorption strength of H atoms. In this context, the Bao group reported the doping of single Pt atoms into the in-plane domain of MoS2 nanosheets (Pt-MoS2) [39], where the resulting Pt-MoS2 exhibited an enhanced HER performance compared with the undoped MoS2. Furthermore, they also screened the HER activities of MoS2 doped with a number of transition metals, resulting in volcano-shaped relationships with the adsorption free energy of the H atoms (∆G H) (Fig. 4a). Their study suggests a novel method for activating the inert in-plane domain of MoS2 catalysts, which may also be extended to other 2D materials applicable in a variety of catalytic reactions.

4.4 Defect and strain engineering

The inert basal surfaces of 2H-MoS2 have also been successfully activated by creating defect sites and/or inducing strain [42–47]. The first example of defect engineering conducted by Xie and co-workers focused on the exposure of additional active edge planes by forming cracks on the surfaces of nanosheets (Fig. 8a) [42]. They reported that defect-rich MoS2 exhibited a significantly enhanced HER performance compared with defect-free MoS2 (Fig. 8b). In addition, the Ajayan group demonstrated that oxygen plasma treatment and H2 annealing introduced additional active sites within the MoS2 monolayer, significantly improving the HER activity [44]. Recently, more rational and controllable defect modulation has been reported through combined experimental and theoretical studies [45–47]. Allwood and co-workers prepared MoS2 nanocrystals and activated the Mo atoms in the basal surface of MoS2 nanocrystals by S depletion [45], with the resulting activated MoS2 exhibiting an very high HER performance (~150 mV at −10 mA cm−2 and a Tafel slope of ~29 mV dec−1). Cao and co-workers also verified the importance of S vacancies on the catalytic activity for the HER [46], estimating the intrinsic TOFs of the edge sites, S vacancies, and grain boundaries as approximately 7.5, 3.2, and 0.1 s−1, respectively. Finally, the Zheng and Nørskov groups reported that straining of the S-vacancies further enhances the HER activity (Fig. 8c–e) [48]. The experimental results was further verified with theoretical results that optimum level of strain and S-vacancy can tune the ΔG H close to zero, guaranteeing the highest intrinsic HER activity.
Fig. 8

a Structural models of the defect-free and defect-rich MoS2 structures. b Polarization curves of the defect-free and defect-rich MoS2 structures for the HER. c Schematic representations of the top and side views of MoS2 containing strained S-vacancies on the basal planes. d Free energy versus the HER reaction coordinate for the S-vacancy range of 0–25%. e Polarization curves for the strained, vacancy, and strained vacancy MoS2 for the HER

(Figures reprinted with permission from Refs. [42, 48])

5 Summary and future challenges

In this review, we have highlighted recent major achievements regarding elucidation of the active sites in MoSx-based electrocatalysts for the HER, and summarized synthetic strategies for designing MoSx electrocatalysts with enhanced HER activities. The edge site of MoS2 was initially identified as the active site for the HER, which then triggered the development of new HER catalysts that can maximize the density of active edge sites, thereby boosting HER activity. The basal surface of MoS2, which were previously believed to be inert towards the HER, can be converted into HER active species via appropriate structural engineering, which include phase transformation, heteroatom doping, defect site generation, and strain engineering. In addition to the crystalline MoS2, amorphous MoSx has also been extensively studied as an efficient electrocatalyst for the HER. Amorphous MoSx can possess abundant active edge structures originating from the building blocks of [Mo3S13]2− clusters, however, the multiple chemical states of sulfur in such species hamper identification of the actual active sulfur states. A comprehensive and systematic study to reveal the key active sites in different MoSx structures still remains a challenging task. Understanding of active sites would enable high-performance MoSx elecrocatalysts for the HER.

Declarations

Authors’ contributions

BS and SHJ wrote the manuscript. Both authors read and approved the final manuscript.

Acknowledgements

Not applicable.

Competing interests

The authors declare that they have no competing interests.

Funding

This work was supported by the Korea Institute for Advancement of Technology (KIAT) funded by the Ministry of Trade, Industry and Energy (MOTIE) (KIAT_N0001754) and the Korea Evaluation Institute of Industrial Technology (KEIT) funded by the MOTIE (10050509). B.S. acknowledges the Global Ph.D. Fellowship (NRF-2013H1A2A1032647).

Publisher’s Note

Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

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

Authors’ Affiliations

(1)
Department of Chemistry, Ulsan National Institute of Science and Technology (UNIST)
(2)
School of Energy and Chemical Engineering, Ulsan National Institute of Science and Technology (UNIST)

References

  1. J.A. Turner, Science 305, 972 (2004)View ArticleGoogle Scholar
  2. J.K. Norskov, C.H. Christensen, Science 312, 1322 (2006)View ArticleGoogle Scholar
  3. J.N. Armor, Appl. Catal. A 176, 159 (1999)View ArticleGoogle Scholar
  4. A. Haryanto, S. Fernando, N. Murali, S. Adhikari, Energy Fuels 19, 2098 (2005)View ArticleGoogle Scholar
  5. J. Ivy, Summary of electrolytic hydrogen production milestone completion report, U.S. Department of Energy (2004)Google Scholar
  6. T.E. Mallouk, Nat. Chem. 5, 362 (2013)View ArticleGoogle Scholar
  7. D. Merki, X. Hu, Energy Environ. Sci. 4, 3878 (2011)View ArticleGoogle Scholar
  8. M.-R. Gao, Y.-F. Xu, J. Jiang, S.-H. Yu, Chem. Soc. Rev. 42, 2986 (2013)View ArticleGoogle Scholar
  9. M. Chhowalla, H.S. Shin, G. Eda, L.-J. Li, K.P. Loh, H. Zhang, Nat. Chem. 5, 263 (2013)View ArticleGoogle Scholar
  10. C.G. Morales-Guio, L.-A. Stern, X. Hu, Chem. Soc. Rev. 43, 6555 (2014)View ArticleGoogle Scholar
  11. J.D. Benck, T.R. Hellstern, J. Kibsgaard, P. Chakthranont, T.F. Jaramillo, ACS Catal. 4, 3957 (2014)View ArticleGoogle Scholar
  12. J. Yang, H.S. Shin, J. Mater. Chem. A 2, 5979 (2014)View ArticleGoogle Scholar
  13. Y. Yan, B. Xia, Z. Xu, X. Wang, ACS Catal. 4, 1693 (2014)View ArticleGoogle Scholar
  14. M. Zeng, Y. Li, J. Mater. Chem. A 3, 14942 (2015)View ArticleGoogle Scholar
  15. Y. Zheng, Y. Jiao, M. Jaroniec, S.Z. Qiao, Angew. Chem. Int. Ed. 54, 52 (2015)View ArticleGoogle Scholar
  16. P.C.K. Vesborg, B. Seger, I. Chorkendorff, J. Phys. Chem. Lett. 6, 951 (2015)View ArticleGoogle Scholar
  17. R. Lv, J.A. Robinson, R.E. Schaak, D. Sun, Y. Sun, T.E. Mallouk, M. Terrones, Acc. Chem. Res. 48, 56 (2015)View ArticleGoogle Scholar
  18. D. Voiry, J. Yang, M. Chhowalla, Adv. Mater. 28, 6197 (2016)View ArticleGoogle Scholar
  19. Q. Ding, B. Song, P. Xu, S. Jin, Chemistry 1, 699 (2016)View ArticleGoogle Scholar
  20. B. Hinnemann, P.G. Moses, J. Bonde, K.P. Jørgensen, J.H. Nielsen, S. Horch, I. Chorkendorff, J.K. Nørscov, J. Am. Chem. Soc. 127, 5308 (2005)View ArticleGoogle Scholar
  21. T.F. Jaramillo, K.P. Jørgensen, J. Bonde, J.H. Nielsen, S. Horch, I. Chorkendorff, Science 317, 100 (2007)View ArticleGoogle Scholar
  22. J. Kibsgaard, Z. Chen, B.N. Reinecke, T.F. Jaramillo, Nat. Mater. 11, 963 (2012)View ArticleGoogle Scholar
  23. B. Seo, G.Y. Jung, Y.J. Sa, H.Y. Jeong, J.Y. Cheon, J.H. Lee, H.Y. Kim, J.C. Kim, H.S. Shin, S.K. Kwak, S.H. Joo, ACS Nano 9, 3728 (2015)View ArticleGoogle Scholar
  24. C. Zhu, X. Mu, P.A. van Aken, Y. Yu, J. Maier, Angew. Chem. Int. Ed. 53, 2152 (2014)View ArticleGoogle Scholar
  25. X. Zheng, J. Xu, K. Yan, H. Wang, Z. Wang, S. Yang, Chem. Mater. 26, 2344 (2014)View ArticleGoogle Scholar
  26. H. Wang, Z. Lu, S. Xu, D. Kong, J.J. Cha, G. Zheng, P.-C. Hsu, K. Yan, D. Bradshaw, F.B. Prinz, Y. Cui, Proc. Natl. Acad. Sci. 110, 19701 (2013)View ArticleGoogle Scholar
  27. D. Kong, H. Wang, J.J. Cha, M. Pasta, K.J. Koski, J. Yao, Y. Cui, Nano Lett. 13, 1341 (2013)View ArticleGoogle Scholar
  28. M. Chatti, T. Gengenbach, R. King, L. Spiccia, A.N. Simonov, Chem. Mater. 29, 3092 (2017)View ArticleGoogle Scholar
  29. T. Wang, L. Liu, Z. Zhu, P. Papakonstantinou, J. Hu, H. Liu, M. Li, Energy Environ. Sci. 6, 625 (2013)View ArticleGoogle Scholar
  30. J. Ding, Y. Zhou, Y. Li, S. Guo, X. Huang, Chem. Mater. 28, 2074 (2016)View ArticleGoogle Scholar
  31. D.Y. Chung, S.-K. Park, Y.-H. Chung, S.-H. Yu, D.-H. Lim, N. Jung, H.C. Ham, H.-Y. Park, Y. Piao, S.J. Yoo, Y.-E. Sung, Nanoscale 6, 2131 (2014)View ArticleGoogle Scholar
  32. T.F. Jaramillo, J. Bonde, J. Zhang, B.-L. Ooi, K. Andersson, J. Ulstrup, I. Chorkendorff, J. Phys. Chem. C 112, 17492 (2008)View ArticleGoogle Scholar
  33. H.I. Karunadasa, E. Montalvo, Y. Sun, M. Majda, J.R. Long, C.J. Chang, Science 335, 698 (2012)View ArticleGoogle Scholar
  34. J. Kibsgaard, T.F. Jaramillo, F. Besenbacher, Nat. Chem. 6, 248 (2014)View ArticleGoogle Scholar
  35. M.A. Lukowski, A.S. Daniel, F. Meng, A. Forticaux, L. Li, S. Jin, J. Am. Chem. Soc. 135, 10274 (2013)View ArticleGoogle Scholar
  36. D. Voiry, M. Salehi, R. Silva, T. Fujita, M. Chen, T. Asefa, V.B. Shenoy, G. Eda, M. Chhowalla, Nano Lett. 13, 6222 (2013)View ArticleGoogle Scholar
  37. H. Wang, Z. Lu, D. Kong, J. Sun, T.M. Hymel, Y. Cui, ACS Nano 8, 4940 (2014)View ArticleGoogle Scholar
  38. X. Geng, W. Sun, W. Wu, B. Chen, A. Al-Hilo, M. Benamara, H. Zhu, F. Watanabe, J. Cui, T. Chen, Nat. Commun. 7, 10672 (2016)View ArticleGoogle Scholar
  39. J. Deng, H. Li, J. Xiao, Y. Tu, D. Deng, H. Yang, H. Tian, J. Li, P. Ren, X. Bao, Energy Environ. Sci. 8, 1594 (2015)View ArticleGoogle Scholar
  40. G. Gao, Q. Sun, A. Du, J. Phys. Chem. C 120, 16761 (2016)View ArticleGoogle Scholar
  41. D. Escalera-López, Y. Niu, J. Yin, K. Cooke, N.V. Rees, R.E. Palmer, ACS Catal. 6, 6008 (2016)View ArticleGoogle Scholar
  42. J. Xie, H. Zhang, S. Li, R. Wang, X. Sun, M. Zhou, J. Zhou, X.W. Lou, Y. Xie, Adv. Mater. 25, 5807 (2013)View ArticleGoogle Scholar
  43. Y. Ouyang, C. Ling, Q. Chen, Z. Wang, L. Shi, J. Wang, Chem. Mater. 28, 4390 (2016)View ArticleGoogle Scholar
  44. G. Ye, Y. Gong, J. Lin, B. Li, Y. He, S.T. Pantelides, W. Zhou, R. Vajtai, P.M. Ajayan, Nano Lett. 16, 1097 (2016)View ArticleGoogle Scholar
  45. L. Lin, N. Miao, Y. Wen, S. Zhang, P. Ghosez, Z. Sun, D.A. Allwood, ACS Nano 10, 8929 (2016)View ArticleGoogle Scholar
  46. G. Li, D. Zhang, Q. Qiao, Y. Yu, D. Peterson, A. Zafar, R. Kumar, S. Curtarolo, F. Hunte, S. Shannons, Y. Zhu, W. Yang, L. Cao, J. Am. Chem. Soc. 138, 16632 (2016)View ArticleGoogle Scholar
  47. C. Tsai, H. Li, S. Park, J. Park, H.S. Han, J.K. Nørskov, X. Zheng, F. Abild-Pedersen, Nat. Commun. 8, 15113 (2017)View ArticleGoogle Scholar
  48. H. Li, C. Tsai, A.L. Koh, L. Cai, A.W. Contryman, A.H. Fragapane, J. Zhao, H.S. Han, H.C. Manoharan, F. Abild-Pedersen, J.K. Nørskov, X. Zheng, Nat. Mater. 15, 48 (2016)View ArticleGoogle Scholar
  49. H. Li, M. Du, M.J. Mleczko, A.L. Koh, Y. Nishi, E. Pop, A.J. Bard, X. Zheng, J. Am. Chem. Soc. 138, 5123 (2016)View ArticleGoogle Scholar
  50. H.G. Sanchez Casalongue, J.D. Benck, C. Tsai, R.K.B. Karlsson, S. Kaya, M.L. Ng, L.G.M. Pettersson, F. Abild-Pedersen, J.K. Nørskov, H. Ogasawara, T.F. Jaramillo, A. Nilsson, J. Phys. Chem. C 118, 29252 (2014)View ArticleGoogle Scholar
  51. B. Lassalle-Kaiser, D. Merki, H. Vrubel, S. Gul, V.K. Yachandra, X. Hu, J. Yano, J. Am. Chem. Soc. 137, 314 (2015)View ArticleGoogle Scholar
  52. P.D. Tran, T.V. Tran, M. Orio, S. Torelli, Q.D. Truong, K. Nayuki, Y. Sasaki, S.Y. Chiam, R. Yi, I. Honma, J. Barber, V. Artero, Nat. Mater. 15, 640 (2016)View ArticleGoogle Scholar
  53. L.R.L. Ting, Y. Deng, L. Ma, Y.-J. Zhang, A.A. Peterson, B.S. Yeo, ACS Catal. 6, 861 (2016)View ArticleGoogle Scholar
  54. Y. Deng, L.R.L. Ting, P.H.L. Neo, Y.-J. Zhang, A.A. Peterson, B.S. Yeo, ACS Catal. 6, 7790 (2016)View ArticleGoogle Scholar
  55. J. Bonde, P.G. Moses, T.F. Jaramillo, J.K. Nørskov, I. Chorkendorff, Faraday Discuss. 140, 219 (2008)View ArticleGoogle Scholar
  56. Y. Li, H. Wang, L. Xie, Y. Liang, G. Hong, H. Dai, J. Am. Chem. Soc. 133, 7296 (2011)View ArticleGoogle Scholar
  57. Z. Chen, D. Cummins, B.N. Reinecke, E. Clark, M.K. Sunkara, T.F. Jaramillo, Nano Lett. 11, 4168 (2011)View ArticleGoogle Scholar
  58. D. Merki, S. Fierro, H. Vrubel, X. Hu, Chem. Sci. 2, 1262 (2011)View ArticleGoogle Scholar
  59. D. Merki, H. Vrubel, L. Rovelli, S. Fierro, X. Hu, Chem. Sci. 3, 2515 (2012)View ArticleGoogle Scholar
  60. J.D. Benck, Z. Chen, L.Y. Kuritzky, A.J. Forman, T.F. Jaramillo, ACS Catal. 2, 1916 (2012)View ArticleGoogle Scholar
  61. H. Vrubel, X. Hu, ACS Catal. 3, 2002 (2013)View ArticleGoogle Scholar
  62. Y. Yu, S.-Y. Huang, Y. Li, S.N. Steinmann, W. Yang, L. Cao, Nano Lett. 14, 553 (2014)View ArticleGoogle Scholar
  63. D.J. Li, U.N. Maiti, J. Lim, D.S. Choi, W.J. Lee, Y. Oh, G.Y. Lee, S.O. Kim, Nano Lett. 14, 1228 (2014)View ArticleGoogle Scholar
  64. M.-R. Gao, M.K.Y. Chan, Y. Sun, Nat. Commun. 6, 7493 (2015)View ArticleGoogle Scholar
  65. D. Kiriya, P. Lobaccaro, H.Y.Y. Nyein, P. Taheri, M. Hettick, H. Shiraki, C.M. Sutter-Fella, P. Zhao, W. Gao, R. Maboudian, J.W. Ager, A. Javey, Nano Lett. 16, 4047 (2016)View ArticleGoogle Scholar
  66. D.R. Cummins, U. Martinez, A. Sherehiy, R. Kappera, A. Martinez-Garcia, R.K. Schulze, J. Jasinski, J. Zhang, R.K. Gupta, J. Lou, M. Chhowalla, G. Sumanasekera, A.D. Mohite, M.K. Sunkara, G. Gupta, Nat. Commun. 7, 11857 (2016)View ArticleGoogle Scholar
  67. J.H. Lee, W.S. Jang, S.W. Han, H.K. Baik, Langmuir 30, 9866 (2014)View ArticleGoogle Scholar
  68. J. Deng, H. Li, S. Wang, D. Ding, M. Chen, C. Liu, Z. Tian, K.S. Novoselov, C. Ma, D. Deng, X. Bao, Nat. Commun. 8, 14430 (2017)View ArticleGoogle Scholar
  69. D. Voiry, H. Yamaguchi, J. Li, R. Silva, D.C.B. Alves, T. Fujita, M. Chen, T. Asefa, V.B. Shenoy, G. Eda, M. Chhowalla, Nat. Mater. 12, 850 (2013)View ArticleGoogle Scholar
  70. J. Yang, D. Voiry, S.J. Ahn, D. Kang, A.Y. Kim, M. Chhowalla, H.S. Shin, Angew. Chem. Int. Ed. 52, 13751 (2013)View ArticleGoogle Scholar
  71. B. Seo, H.Y. Jeong, S.Y. Hong, A. Zak, S.H. Joo, Chem. Commun. 51, 8334 (2015)View ArticleGoogle Scholar
  72. D.-Y. Wang, M. Gong, H.-L. Chou, C.-J. Pan, H.-A. Chen, Y. Wu, M.-C. Lin, M. Guan, J. Yang, C.-W. Chen, Y.-L. Wang, B.-J. Hwang, C.-C. Chen, H. Dai, J. Am. Chem. Soc. 137, 1587 (2015)View ArticleGoogle Scholar
  73. N. Kornienko, J. Resasco, N. Becknell, C.-M. Jiang, Y.-S. Liu, K. Nie, X. Sun, J. Guo, S.R. Leone, P. Yang, J. Am. Chem. Soc. 137, 7448 (2015)View ArticleGoogle Scholar
  74. D. Yoon, B. Seo, J. Lee, K.S. Nam, B. Kim, S. Park, H. Baik, S.H. Joo, K. Lee, Energy Environ. Sci. 9, 850 (2016)View ArticleGoogle Scholar
  75. H. Vrubel, X. Hu, Angew. Chem. Int. Ed. 51, 12703 (2012)View ArticleGoogle Scholar
  76. W.-F. Chen, C.-H. Wang, K. Sasaki, N. Marinkovic, W. Xu, J.T. Muckerman, Y. Zhu, R.R. Adzic, Energy Environ. Sci. 6, 943 (2013)View ArticleGoogle Scholar
  77. Y.-T. Xu, X. Xiao, Z.-M. Ye, S. Zhao, R. Shen, C.-T. He, J.-P. Zhang, Y. Li, X.-M. Chen, J. Am. Chem. Soc. 139, 5285 (2017)View ArticleGoogle Scholar
  78. W.-F. Chen, K. Sasaki, C. Ma, A.I. Frenkel, N. Marinkovic, J.T. Muckerman, Y. Zhu, R.R. Adzic, Angew. Chem. Int. Ed. 51, 6131 (2012)View ArticleGoogle Scholar
  79. P. Liu, J.A. Rodriguez, J. Am. Chem. Soc. 127, 14871 (2005)View ArticleGoogle Scholar
  80. E.J. Popczun, J.R. Mckone, C.G. Read, A.J. Biacchi, A.M. Wiltrout, N.S. Lewis, R.E. Schaak, J. Am. Chem. Soc. 135, 9267 (2013)View ArticleGoogle Scholar
  81. J. Tian, Q. Liu, A.M. Asiri, X. Sun, J. Am. Chem. Soc. 136, 7587 (2014)View ArticleGoogle Scholar
  82. B. Seo, D.S. Baek, Y.J. Sa, S.H. Joo, CrystEngComm 18, 6083 (2016)View ArticleGoogle Scholar
  83. H. Tributsch, J.C. Bennett, J. Electroanal. Chem. 81, 97 (1977)View ArticleGoogle Scholar
  84. Y. Gorlin, T.F. Jaramillo, J. Am. Chem. Soc. 132, 13612 (2010)View ArticleGoogle Scholar
  85. L.P. Hansen, Q.M. Ramasse, C. Kisielowski, M. Brorson, E. Johnson, H. Topsøe, S. Helveg, Angew. Chem. Int. Ed. 50, 10153 (2011)View ArticleGoogle Scholar
  86. W. Zhou, X. Zou, S. Najmaei, Z. Liu, Y. Shi, J. Kong, J. Lou, P.M. Mjayan, B.I. Yakobson, J.-C. Idrobo, Nano Lett. 13, 2615 (2013)View ArticleGoogle Scholar
  87. C. Tsai, K. Chan, F. Abild-Pedersen, J.K. Nørskov, Phys. Chem. Chem. Phys. 16, 13156 (2014)View ArticleGoogle Scholar
  88. C. Tsai, F. Abild-Pedersen, J.K. Nørskov, Nano Lett. 14, 1381 (2014)View ArticleGoogle Scholar
  89. J. Hong, Z. Hu, M. Probert, K. Li, D. Lv, X. Yang, L. Gu, N. Mao, Q. Feng, L. Xie, J. Zhang, D. Wu, Z. Zhang, C. Jin, W. Ji, X. Zhang, J. Yuan, Z. Zhang, Nat. Commun. 6, 6293 (2015)View ArticleGoogle Scholar

Copyright

© Korea Nano Technology Research Society 2017

Advertisement