WS(1−x)Sex Nanoparticles Decorated Three-Dimensional Graphene on Nickel Foam: A Robust and Highly Efficient Electrocatalyst for the Hydrogen Evolution Reaction

To find an effective alternative to scarce, high-cost noble platinum (Pt) electrocatalyst for hydrogen evolution reaction (HER), researchers are pursuing inexpensive and highly efficient materials as an electrocatalyst for large scale practical application. Layered transition metal dichalcogenides (TMDCs) are promising candidates for durable HER catalysts due to their cost-effective, highly active edges and Earth-abundant elements to replace Pt electrocatalysts. Herein, we design an active, stable earth-abundant TMDCs based catalyst, WS(1−x)Sex nanoparticles-decorated onto a 3D porous graphene/Ni foam. The WS(1−x)Sex/graphene/NF catalyst exhibits fast hydrogen evolution kinetics with a moderate overpotential of ~−93 mV to drive a current density of 10 mA cm−2, a small Tafel slope of ~51 mV dec−1, and a long cycling lifespan more than 20 h in 0.5 M sulfuric acid, which is much better than WS2/NF and WS2/graphene/NF catalysts. Our outcomes enabled a way to utilize the TMDCs decorated graphene and precious-metal-free electrocatalyst as mechanically robust and electrically conductive catalyst materials.


Introduction
Water splitting is widely considered to be an effective route for renewable, clean, and efficient energy production from the abundant water on Earth. Electrocatalytic or photocatalytic water splitting into oxygen and hydrogen may potentially address the global environmental pollution and energy crisis [1,2]. Platinum (Pt) has proved to be a most efficient hydrogen evolution reaction (HER) catalyst, however, it has low appeal to use in industrial applications due to its high cost and scarcity [3]. The development of an inexpensive, Earth-abundant, highly active, and acid-stable material to use as an electrocatalyst is a grand challenge. In recent years, tremendous effort has been made to develop efficient HER catalysts from Earth-abundant materials with lots of active edges to replace Pt, such as transition-metal-based oxides/hydroxides, non-oxides, including metal based sulfides [4][5][6], selenides [7][8][9], carbides [10,11], phosphides [12,13], borate [14], phosphate [15], and their alloys. However, so far most of the catalysts exhibit inferior efficiency compared to Pt, while many processes involve complicated material synthesis and multiple steps, which may result in the increase of cost and further limit potential applications. Graphene is a well-known material, and it has potential for use in various electrocatalyst applications, which include supercapacitor, HER, and DSSCs [16,17]. Recently, tungsten disulfide (WS 2 ), which is from the family of transition metal dichalcogenides (TMDCs), has been studied elaborately as an electrocatalyst due to its high electrocatalytic properties [18]. Various studies have been done to promote the electrocatalytic activity of WS 2 with the combination of highly conductive materials, such as macro-and meso-porous carbon materials, gold (Au), and carbon paper in a hybrid nature for oxygen and hydrogen evolution reactions (OER and HER). Davodi and co-workers [19,20] reported the nitrogen doped multi-walled carbon nanotube (MWCNT) and Ni@γ-Fe 2 O 3 /MWCNTs functionalized with nitrogen-rich emeraldine salt for alkaline HER and OER processes. Luo et al. also demonstrated Fe 3 O 4 @NiFe x O y core−shell nano-heterostructures toward the OER with an overpotential −410 mV@1 mA cm −2 and Tafel slope of 48 mV dec −1 [21]. Zhou et al. [22] used 3D hybrids of WS 2 /graphene/Ni foam as a catalyst in HER application and observed the low overpotential of −119 mV@10 mA cm −2 , the small Tafel slope of~43 mV dec −1 , and the large cathodic current density. Recently, Zhou et al. has reported ternary tungsten sulfoselenide (WS 2(1−x) Se 2x ) particles with a 3D porous metallic NiSe 2 foam to have excellent catalytic performance with −88 mV@10 mA cm −2 of overpotential, 46.7 mV dec −1 of Tafel slope, and 214.7 µA cm −2 of exchange current density [23]. Our group has recently demonstrated a facile way to prepare a MoS 2 QDs film using a solution process and WS 2 /CoSe 2 heterostructure for HER applications [24,25]. Moreover, ternary alloys of MoS 2(1−x) Se 2x and WS 2(1−x) Se 2x were synthesized as a electrocatalyst for HER by a sputtering-CVD process with the overpotentials of −141 and −167 mV to drive 10 mA cm −2 and Tafel slopes of 67 and 107 mV dec −1 , respectively [26].
Recently, many efficient strategies to increase the number of active edge sites with large surface areas, high porosity, and better intrinsic electrical conductivity or the contact between the catalyst and the electrode were adopted to increase the electrocatalytic activity of electrode material. Herein, we utilized a 3D porous structure nickel (Ni) foam (NF) as a highly conductive skeleton, and produced WS 2 /NF, WS 2 -decorated graphene/NF, and WS (1−x) Se x nanoparticles-decorated graphene/NF catalysts for HER applications. The obtained electrodes exhibited low overpotentials of −145, −115, and −93 mV vs. RHE for WS 2 /NF, WS 2 /Graphene/NF, and WS (1−x) Se x /graphene/NF, respectively, at 10 mA cm −2 . The small Tafel slope was obtained for WS (1−x) Se x /graphene/NF (51 mV dec −1 ) as compared to the WS 2 /NF and WS 2 /graphene/NF (62 and 63 mV dec −1 , respectively).

Experimental Details
2.1. Synthesis of Graphene/NF, WS 2 /Graphene/NF, and WS (1−x) Se x /Graphene/NF Initially, the Ni foam (NF) was cleaned with ultrasonic baths of acetone, ethanol, and deionized water, baked at 120 • C for 5 min, and then annealed with a hydrogen (H 2 )/argon (Ar) (30/50 sccm) environment at 900 • C for 30 min in a quartz tube furnace to clean the surface of the Ni foam without breaking the vacuum. Then to prepare the graphene on NF, the mixture of H 2 /Ar/methane (CH 4 ) flow (H 2 /Ar/CH 4 = 50:100:50 sccm) was maintained for 30 min. Subsequently, the H 2 /CH 4 flow gas channel was shut off, and then rapidly cooled to room temperature in Ar environment. Furthermore, prepared graphene/NF was used as substrate for the growth of WS 2 and WS (1−x) Se x .
For WS 2 growth, ammonium tetrathiotungstate ((NH 4 ) 2 WS 4 ) (Sigma Aldrich, 99.97%) was used as the main source material. First, a precursor of (NH 4 ) 2 WS 4 (0.2 g) was dissolved in N,N-Dimethylformamide (DMF) (20 mL), and then the solution was sonicated for 30 min. The 3D graphene/Ni foam was immersed into the prepared (NH 4 ) 2 WS 4 solution and then baked at 100 • C for 30 min. Finally, synthesized films were placed in an annealing chamber and heated up to 450 • C for 30 and 45 min in a sulfur or sulfur/selenium environment to form WS 2 /Graphene/NF and WS (1−x) Se x /Graphene/NF. The gas flow Ar/H 2 flux (50/50 sccm) was maintained, and the pressure of chamber was kept at 2 × 10 −2 Torr. The same quantity of sulfur/selenium (0.3/0.3 g) powder was used.

Electrochemical Measurements
The electrochemical measurements were conducted in a three-electrode setup with a Biologic SP-300 workstation. The polarization curves were collected using a linear sweep voltammetry (LSV) with a scan rate of 10 mV.s −1 in 0.5 M H 2 SO 4 electrolyte at room temperature. For the LSV measurement, a saturated calomel reference electrode (SCE) was used as the reference electrode. WS 2 (30 min)/NF, WS 2 (45 min)/NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF were used as the working electrode. Also, a graphite rod was used as the counter electrode. All LSV measurements were probed in terms of SCE and then converted to an reversible hydrogen electrode (RHE) scale with the help of the following equation: E(RHE) = E(SCE) + E • (SCE) + 0.059 pH. Electrochemical impedance spectroscopy (EIS) measurements were carried out in a potentiostatic mode with a frequency range from 0.01 Hz to 100 kHz under an amplitude of 10 mV. All the LSV polarizations were recorded after the ohmic drop iR correction. The stability measurement was examined using a chronoamperometric analysis.

Results and Discussion
Initially, the graphene was grown on a 3D NF using a chemical vapor deposition (CVD), as reported previously [27]. WS 2 was further grown by a hydrothermal process using an (NH 4 ) 2 WS 4 precursor on 3D graphene with NF. To improve the crystalline quality, the film was further annealed at 500 • C in a sulfur environment at 30~45 min to form WS 2 nanoparticle-decorated graphene on NF (WS 2 /graphene/NF). To form WS (1−x) Se x nanoparticles-decorated graphene on NF (WS (1−x) Se x /graphene/NF), a CVD deposited film was annealed at 450 • C in a sulfur and selenium environment at 30 min, respectively, to form WS (1−x) Se x onto graphene. The schematic representation is given in Figure 1. 30 min. Finally, synthesized films were placed in an annealing chamber and heated up to 450 °C for 30 and 45 min in a sulfur or sulfur/selenium environment to form WS2/Graphene/NF and WS(1−x)Sex/Graphene/NF. The gas flow Ar/H2 flux (50/50 sccm) was maintained, and the pressure of chamber was kept at 2 × 10 −2 Torr. The same quantity of sulfur/selenium (0.3/0.3 g) powder was used.

Electrochemical Measurements
The electrochemical measurements were conducted in a three-electrode setup with a Biologic SP-300 workstation. The polarization curves were collected using a linear sweep voltammetry (LSV) with a scan rate of 10 mV.s −1 in 0.5 M H2SO4 electrolyte at room temperature. For the LSV measurement, a saturated calomel reference electrode (SCE) was used as the reference electrode. WS2(30 min)/NF, WS2(45 min)/NF, WS2/graphene/NF, and WS(1−x)Sex/graphene/NF were used as the working electrode. Also, a graphite rod was used as the counter electrode. All LSV measurements were probed in terms of SCE and then converted to an reversible hydrogen electrode (RHE) scale with the help of the following equation: E(RHE) = E(SCE) + E°(SCE) + 0.059 pH. Electrochemical impedance spectroscopy (EIS) measurements were carried out in a potentiostatic mode with a frequency range from 0.01 Hz to 100 kHz under an amplitude of 10 mV. All the LSV polarizations were recorded after the ohmic drop iR correction. The stability measurement was examined using a chronoamperometric analysis.

Results and Discussion
Initially, the graphene was grown on a 3D NF using a chemical vapor deposition (CVD), as reported previously [27]. WS2 was further grown by a hydrothermal process using an (NH4)2WS4 precursor on 3D graphene with NF. To improve the crystalline quality, the film was further annealed at 500 °C in a sulfur environment at 30~45 min to form WS2 nanoparticle-decorated graphene on NF (WS2/graphene/NF). To form WS(1−x)Sex nanoparticles-decorated graphene on NF (WS(1−x)Sex/graphene/NF), a CVD deposited film was annealed at 450 °C in a sulfur and selenium environment at 30 min, respectively, to form WS(1−x)Sex onto graphene. The schematic representation is given in Figure 1. The surface morphological analysis was performed using a field emission scanning electron microscopy (FESEM) and a high-resolution transmission electron microscopy (HRTEM). Figure 2ad shows the typical FESEM images of graphene, WS2/NF, WS2/graphene/NF, and WS(1−x)Sex/graphene/NF, respectively, and its insets show the higher magnification images. The bare NF ( Figure 2a) is composed of lots of pores with sizes in tens to hundreds of micrometers, which will lead to somewhat irregular and uneven film growth which will be beneficial to enhance the HER property. From the FESEM image (Figure 2b), the regular deposition of graphene onto NF is observed with different thicknesses on the curvature of the foam. The larger area FESEM images of WS2/NF, WS2/graphene/NF, and WS(1−x)Sex/graphene/NF are provided in Figure S1. Wrinkles and ripples of graphene are spotted, which might be contributed to the differences in thermal expansion coefficients between the graphene and the Ni substrate [28]. The direct synthesis of WS2 on NF, for comparison, showed agglomerated small spherical granules with a non-uniform shape on the surface of the NF due to their curvature nature (Figure 2c). The nanoparticles with different sizes, The surface morphological analysis was performed using a field emission scanning electron microscopy (FESEM) and a high-resolution transmission electron microscopy (HRTEM). Figure 2a-d shows the typical FESEM images of graphene, WS 2 /NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF, respectively, and its insets show the higher magnification images. The bare NF (Figure 2a) is composed of lots of pores with sizes in tens to hundreds of micrometers, which will lead to somewhat irregular and uneven film growth which will be beneficial to enhance the HER property. From the FESEM image (Figure 2b), the regular deposition of graphene onto NF is observed with different thicknesses on the curvature of the foam. The larger area FESEM images of WS 2 /NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF are provided in Figure S1. Wrinkles and ripples of graphene are spotted, which might be contributed to the differences in thermal expansion coefficients between the graphene and the Ni substrate [28]. The direct synthesis of WS 2 on NF, for comparison, showed agglomerated small spherical granules with a non-uniform shape on the surface of the NF due to their curvature nature ( Figure 2c). The nanoparticles with different sizes, due to agglomeration, were observed for WS 2 /graphene/NF from the low and higher magnification FESEM images ( Figure 2d). In the case of WS (1−x) Se x /graphene/NF, the stacked nano-plate like agglomerated grains were observed as shown in Figure 2e. The elemental composition of WS (1−x) Se x alloys were determined by the energy dispersion spectra (EDS) as presented in Figure S2 (WS (1−x) Se x -W: 32.0%, S: 16.3%, C: 4.8%, and Se: 8.0%). Ni signals are ascribed from the NF substrate. The elemental mapping images of WS 2 and WS (1−x) Se x layers are provided in Figures S3 and S4, and it confirms the homogeneous spatial distribution of W, S, C, and Se on the whole surface. The HRTEM studies were performed to reveal the layer structure of the prepared films. From the HRTEM images (Figure 3a), the multilayer of graphene was identified. In Figure 3b, WS (1−x) Se x and graphene are shown with yellow and red boxes, respectively. Figures 2 and 3 suggest the expose of active edge sites at the surface of WS (1−x) Se x /graphene/NF particles as reported in previous literature [23,29]. The WS (1−x) Se x nanosheets, with an interlayer separation of 0.64 nm, were grown intimately on the graphene/NF substrate, which are also beneficial to enhance a HER reaction. due to agglomeration, were observed for WS2/graphene/NF from the low and higher magnification FESEM images (Figure 2d). In the case of WS(1−x)Sex/graphene/NF, the stacked nano-plate like agglomerated grains were observed as shown in Figure 2e. The elemental composition of WS(1−x)Sex alloys were determined by the energy dispersion spectra (EDS) as presented in Figure S2 (WS(1−x)Sex -W: 32.0%, S: 16.3%, C: 4.8%, and Se: 8.0%). Ni signals are ascribed from the NF substrate. The elemental mapping images of WS2 and WS(1−x)Sex layers are provided in Figures S3 and S4, and it confirms the homogeneous spatial distribution of W, S, C, and Se on the whole surface. The HRTEM studies were performed to reveal the layer structure of the prepared films. From the HRTEM images (Figure 3a), the multilayer of graphene was identified. In Figure 3b, WS(1−x)Sex and graphene are shown with yellow and red boxes, respectively. Figure 2 and Figure 3 suggest the expose of active edge sites at the surface of WS(1−x)Sex/graphene/NF particles as reported in previous literature [23,29]. The WS(1−x)Sex nanosheets, with an interlayer separation of 0.64 nm, were grown intimately on the graphene/NF substrate, which are also beneficial to enhance a HER reaction.   due to agglomeration, were observed for WS2/graphene/NF from the low and higher magnification FESEM images (Figure 2d). In the case of WS(1−x)Sex/graphene/NF, the stacked nano-plate like agglomerated grains were observed as shown in Figure 2e. The elemental composition of WS(1−x)Sex alloys were determined by the energy dispersion spectra (EDS) as presented in Figure S2 (WS(1−x)Sex -W: 32.0%, S: 16.3%, C: 4.8%, and Se: 8.0%). Ni signals are ascribed from the NF substrate. The elemental mapping images of WS2 and WS(1−x)Sex layers are provided in Figures S3 and S4, and it confirms the homogeneous spatial distribution of W, S, C, and Se on the whole surface. The HRTEM studies were performed to reveal the layer structure of the prepared films. From the HRTEM images (Figure 3a), the multilayer of graphene was identified. In Figure 3b, WS(1−x)Sex and graphene are shown with yellow and red boxes, respectively. Figure 2 and Figure 3 suggest the expose of active edge sites at the surface of WS(1−x)Sex/graphene/NF particles as reported in previous literature [23,29]. The WS(1−x)Sex nanosheets, with an interlayer separation of 0.64 nm, were grown intimately on the graphene/NF substrate, which are also beneficial to enhance a HER reaction.   Raman spectroscopy was further used to characterize the formation of graphene, WS 2 /NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF. From the spectrum of graphene/NF (Figure 4a), the principle bands of graphene, such as G band (1577cm −1 ), 2D band (2706 cm −1 ), and D band (1364 cm −1 ) were exhibited due to defects in the carbon lattice [30]. For WS 2 /NF, two prominent Raman peaks originated at 350.1 and 420.5 cm −1 correspond to the E 1 2g and A 1g modes, respectively [31]. In the case of WS 2 /graphene/NF, E 1 2g , and A 1g modes (351.6 and 420.5 cm −1 ) for WS 2 , two sharp peaks for graphene (G band: 1577.8 cm −1 and 2D band: 2699.8 cm −1 ) are shown [32,33]. In addition to the above peaks, a low intensity E 1 2g mode peak was observed at 250.6 cm −1 , corresponding to WSe 2 [34] for WS (1−x) Se x /graphene/NF. Our results also confirm the formation of both WS 2 and WSe 2 on porous graphene foam. Furthermore, the observed Raman results are well consistent with previously reported results of a WS 2 and WSe 2 materials system [34]. Raman spectroscopy was further used to characterize the formation of graphene, WS2/NF, WS2/graphene/NF, and WS(1−x)Sex/graphene/NF. From the spectrum of graphene/NF (Figure 4a), the principle bands of graphene, such as G band (1577cm −1 ), 2D band (2706 cm −1 ), and D band (1364 cm −1 ) were exhibited due to defects in the carbon lattice [30]. For WS2/NF, two prominent Raman peaks originated at 350.1 and 420.5 cm −1 correspond to the E 1 2g and A1g modes, respectively [31]. In the case of WS2/graphene/NF, E 1 2g, and A1g modes (351.6 and 420.5 cm −1 ) for WS2, two sharp peaks for graphene (G band: 1577.8 cm −1 and 2D band: 2699.8 cm −1 ) are shown [32,33]. In addition to the above peaks, a low intensity E 1 2g mode peak was observed at 250.6 cm −1 , corresponding to WSe2 [34] for WS(1−x)Sex/graphene/NF. Our results also confirm the formation of both WS2 and WSe2 on porous graphene foam. Furthermore, the observed Raman results are well consistent with previously reported results of a WS2 and WSe2 materials system [34].  (Figure 5a), an additional peak of Se element was detected. The expanded region of W4f, S2p, C, and Se3d peaks are provided in the Figure 5b-e. A sharp peak at 284 eV originated from graphene. The two principal peaks of W binding energy of 4f7/2 and W 4f5/2 (36.4 and 34.5 eV) doublets, which were indicative of the oxidation state of W 4+ , appeared. The S 2p1/2 and 2p3/2 orbital peaks observed at 163.6 and 161.9 eV, respectively, indicating the S2, confirmed the WS2 crystal [31,35]. The Se 3d core levels can be fitted with Se 3d5/2 (53.8 eV) and Se 3d3/2 (55.6 eV) corresponding to the −2 oxidation state of selenium [36].  (Figure 5a), an additional peak of Se element was detected. The expanded region of W4f, S2p, C, and Se3d peaks are provided in the Figure 5b-e. A sharp peak at 284 eV originated from graphene. The two principal peaks of W binding energy of 4f 7/2 and W 4f 5/2 (36.4 and 34.5 eV) doublets, which were indicative of the oxidation state of W 4+ , appeared. The S 2p 1/2 and 2p 3/2 orbital peaks observed at 163.6 and 161.9 eV, respectively, indicating the S2, confirmed the WS 2 crystal [31,35]. The Se 3d core levels can be fitted with Se 3d 5/2 (53.8 eV) and Se 3d 3/2 (55.6 eV) corresponding to the −2 oxidation state of selenium [36]. HER activities were investigated via a standard three-electrode setup with a scan rate of 10 mV s −1 in 0.5 M sulfuric acid (H2SO4) electrolyte solution by linear sweep voltammetry (LSV) with iR correction. As expected, the commercial Pt wire exhibited the lowest overpotential, which was close to zero. The WS(1−x)Sex/graphene/NF catalyst can deliver an overpotential at −93 mV vs. the reversible hydrogen electrode (RHE) for a geometric current density of 10 mA cm −2 . In contrast, WS2(45 min)/NF, and WS2/graphene/NF exhibited inferior HER activity (−114 and −115 mV vs. RHE at current 10 mA cm −2 , respectively) (Figure 6a,b). Earlier research reported that the unsaturated Se facets are highly active and improve HER activity [37,38]. Theoretical estimation supports lower Gibbs free energy for H2 adsorption onto the Se facets than the S facets [38]. Graphene is a conductive material which can increase the conduction between electrode and electrolyte and create the synergistic effect with active materials that lead to good HER properties.
The catalytic overpotential (−93 mV) of the WS(1−x)Sex/graphene/NF was quite lower than those of the reported WS2-based TMDCs in the literature, which include: Cobalt sulfide @WS2/carbon cloth (CC) hybrid catalyst (−97. The inherent property of catalytic activity for HER kinetics was probed by extracting the slopes from the linear regions in Tafel plots. A Tafel slope of 51 mV dec −1 was extracted for HER activities were investigated via a standard three-electrode setup with a scan rate of 10 mV s −1 in 0.5 M sulfuric acid (H 2 SO 4 ) electrolyte solution by linear sweep voltammetry (LSV) with iR correction. As expected, the commercial Pt wire exhibited the lowest overpotential, which was close to zero. The WS (1−x) Se x /graphene/NF catalyst can deliver an overpotential at −93 mV vs. the reversible hydrogen electrode (RHE) for a geometric current density of 10 mA cm −2 . In contrast, WS 2 (45 min)/NF, and WS 2 /graphene/NF exhibited inferior HER activity (−114 and −115 mV vs. RHE at current 10 mA cm −2 , respectively) (Figure 6a,b). Earlier research reported that the unsaturated Se facets are highly active and improve HER activity [37,38]. Theoretical estimation supports lower Gibbs free energy for H 2 adsorption onto the Se facets than the S facets [38]. Graphene is a conductive material which can increase the conduction between electrode and electrolyte and create the synergistic effect with active materials that lead to good HER properties.
From the classical theory for hydrogen evolution process, the observed Tafel slope of 36 mV dec −1 for Pt exposes the hydrogen production proceeds with the fast discharge step (Equation (1)) followed by the Tafel (Equation (3)) [53,54]. The observed intermediate Tafel slope values of 51, 62, and 63 mV·dec −1 (WS 2 /NF, WS 2 /graphene/NF and WS (1−x) Se x /graphene/NF, respectively) suggest that hydrogen production proceeds with the fast discharge step (equation 1) followed by the Tafel (Equation (3)) or Heyrovsky ion-atom reaction (Equation (2)) [17,55,56]. The observed small overpotential and Tafel slope for WS (1−x) Se x /graphene/NF could be attributed to the nanostructured particles on the porous substrate, which increase accessible active sites. EIS was performed to study the interface reactions and electrode kinetics in HER at a frequency range from 0.01 Hz to 100 kHz. The Nyquist plots revealed the charge-transfer resistance (R ct ) of Pt, WS 2 (45 min)/NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF. The R ct value of Pt, WS 2 (45 min)/NF, WS 2 /graphene/NF, and WS (1−x) Se x /graphene/NF were approximately 0.5, 2.4, 1.1, and 0.8 Ω, respectively (Figure 6d). The lower R ct value suggests a faster reaction rate between the electrode and electrolyte. The low R ct value could be due to the abundance of accessible sulfur/salinization active edges on a 3D porous substrate and result in the higher HER activity.
Stability is another key factor to elucidate the performance of catalysts. For this purpose, we tested the stability of WS (1−x) Se x /graphene/NF electrode using potential cycling in the range from −0.5 to +0.1 V with a scan rate of 50 mV·s −1 . After a 20 h operation in a 0.5 M H 2 SO 4 solution, the polarization curve was little changed from the initial one, which indicated no observable degradation after long-term cycling tests (Figure 7a). The long-term electrochemical stability of this electrode was also examined. The cathodic current density for the WS (1−x) Se x /graphene/NF catalyst remained stable and exhibited no obvious degradation for electrolysis at a fixed overpotential of −93 mV for more than 20 h, which indicated the potential usage of this catalyst maintained its catalytic activity over a long time in the electrochemical process (Figure 7b). From the classical theory for hydrogen evolution process, the observed Tafel slope of 36 mV dec −1 for Pt exposes the hydrogen production proceeds with the fast discharge step (Equation (1)) followed by the Tafel (Equation (3)) [53,54]. The observed intermediate Tafel slope values of 51, 62, and 63 mV·dec −1 (WS2/NF, WS2/graphene/NF and WS(1−x)Sex/graphene/NF, respectively) suggest that hydrogen production proceeds with the fast discharge step (equation 1) followed by the Tafel (Equation (3)) or Heyrovsky ion-atom reaction (Equation (2)) [17,55,56]. The observed small overpotential and Tafel slope for WS(1−x)Sex/graphene/NF could be attributed to the nanostructured particles on the porous substrate, which increase accessible active sites.  (Figure 6d). The lower Rct value suggests a faster reaction rate between the electrode and electrolyte. The low Rct value could be due to the abundance of accessible sulfur/salinization active edges on a 3D porous substrate and result in the higher HER activity.
Stability is another key factor to elucidate the performance of catalysts. For this purpose, we tested the stability of WS(1−x)Sex/graphene/NF electrode using potential cycling in the range from −0.5 to +0.1 V with a scan rate of 50 mV·s −1 . After a 20 h operation in a 0.5 M H2SO4 solution, the polarization curve was little changed from the initial one, which indicated no observable degradation after long-term cycling tests (Figure 7a). The long-term electrochemical stability of this electrode was also examined. The cathodic current density for the WS(1−x)Sex/graphene/NF catalyst remained stable and exhibited no obvious degradation for electrolysis at a fixed overpotential of −93 mV for more than 20 h, which indicated the potential usage of this catalyst maintained its catalytic activity over a long time in the electrochemical process (Figure 7b).

Conclusions
In summary, an effective and efficient strategy was adopted for the synthesis of WS 2 and ternary WS (1−x) Se x /graphene/NF for a robust and stable self-standing hydrogen evolving catalyst. The novel WS (1−x) Se x /graphene/NF catalyst showed good HER catalytic properties in acidic electrolyte with an overpotential of −93 mV to drive 10 mA cm −2 , a small Tafel slope of 51 mV dec −1 , and a high exchange current density with excellent long-term durability. Our results proved that Se incorporated WS 2 /graphene/NF exhibits the highest electrocatalytic activity for HER, and it is stable in acidic media over a long period among the other electrodes due to high active edge sites and porous structures.  Figure S2: EDS spectrum for WS (1−x) Se x /graphene/NF. Figure S3: (a) FESEM image of WS2/graphene/NF and its elemental mapping images of (b) Ni (c) W (d) S and (e) Se elements. Figure S4: