Water electrolysis is an advanced energy conversion technology to produce hydrogen as a clean and sustainable chemical fuel, which potentially stores the abundant but intermittent renewable energy sources scalably. Since the overall water splitting is an uphill reaction in low efficiency, innovative breakthroughs are desirable to greatly improve the efficiency by rationally designing non-precious metal-based robust bifunctional catalysts for promoting both the cathodic hydrogen evolution and anodic oxygen evolution reactions. We report a hybrid catalyst constructed by iron and dinickel phosphides on nickel foams that drives both the hydrogen and oxygen evolution reactions well in base, and thus substantially expedites overall water splitting at 10 mA cm−2 with 1.42 V, which outperforms the integrated iridium (IV) oxide and platinum couple (1.57 V), and are among the best activities currently. Especially, it delivers 500 mA cm−2 at 1.72 V without decay even after the durability test for 40 h, providing great potential for large-scale applications.
The scalable storage of such abundant renewable energy sources as wind or solar energy is required to mitigate the aggravated global energy crisis while addressing the environmental issues1. Converting solar- or wind-derived electricity to hydrogen fuel via water electrolysis is an appealing means to accomplish this energy conversion and storage technology2,3,4,5,6. At present, there are mainly two commercialized water electrolysis including alkaline and proton exchange membrane (PEM) water electrolysis. PEM water electrolysis has high energy efficiency with high hydrogen production rate, but requires noble metal platinum (Pt) or iridium (Ir)-based catalysts7,8, making it unfavorable due to high cost and scarcity. The alternative, low-cost alkaline water electrolysis, is a mature technology for large-scale hydrogen production that is low-cost due to compatibility with non-noble catalysts, but it suffers from low production rates9,10. One of its grand challenges remains to the huge energy penalty caused by the uphill reaction kinetics of the catalysts that requires significantly high cell voltages (1.8–2.4 V, far larger than the thermodynamic value of 1.23 V) to catalyze the reaction with electrolysis currents of 200–400 mA cm−2, resulting in the production of less than 5% hydrogen by means of water electrolysis in the worldwide industry10,11,12. Therefore, it is urgent to rationally develop exceptionally efficient non-noble catalysts for expediting overall water splitting toward large-scale commercialization at high current densities with low cell voltages.
Currently, there exist some intriguing bifunctional catalysts to negotiate the overall water splitting efficiently in alkaline electrolytes, including transition-metal oxides (e.g., MoO2, NiCoO4)13,14,15, layered double hydroxides (LDH) (e.g., NiFe LDHs)2,16, sulfides (e.g., NiCo2S4, MoS2/Ni3S2)17,18, selenides (e.g., NiSe)19, and phosphides (e.g., CoP2/reduced graphene oxide, Ni5P4)20,21. Unfortunately, most of them can operate only steadily at low current density (<20 mA cm−2), not to mention their low energy conversion efficiency at above 200 mA cm−2 required for commercial applications. These catalysts are far from being optimized for industrial scales10,22 probably arisen from the difficulty in integrating both the merits of hydrogen evolution reaction (HER) and oxygen evolution reaction (OER) electrocatalysts in a single bifunctional catalyst in the same electrolyte (either alkaline or acid). In this regard, constructing a single bifunctional catalyst with outstanding HER and OER activities simultaneously in the same electrolyte is urgently needed.
We report here, just such a cost-effective catalyst that we discover using the straightforward strategy of hybridizing two metallic iron and dinickel phosphides (FeP/Ni2P) on commercial nickel (Ni) foams. This produces an extremely active bifunctional electrocatalyst for both OER and HER outperforming most of the catalysts with similar function, and also exceptional overall water splitting surpassing commercial alkaline electrolyzers in 1 M KOH. Specifically, we corroborate that our FeP/Ni2P hybrid performs well for HER with catalytic performance (−14 mV to achieve −10 mA cm−2) as good as that of the state-of-the-art noble Pt catalyst (−57 mV), and also for OER with the lowest overpotential (154 mV to afford 10 mA cm−2) reported thus far, substantially outperforming the benchmark IrO2 (281 mV) and other reported robust OER catalysts. Furthermore, inspired by the excellent HER and OER activity, we integrated this bifunctional catalyst directly as both the anode and cathode electrodes in an alkaline electrolyzer, and demonstrate that a cell voltage of only 1.42 V can deliver 10 mA cm−2, and a cell voltage of 1.72 V is required to deliver 500 mA cm−2 with 40 h durability, far surpassing the performance of current industrial catalysts, which require 2.40 V for 400 mA cm−2.
Electrocatalyst preparation and characterization
Our Fe–Ni–P hybrid architecture was prepared directly on commercial Ni foams by a simple thermal treatment process. Typical scanning electron microscopy (SEM) images show that the as-prepared samples are free-standing with abundant mesopores and/or nanopores at the surface (Fig. 1a and b), indicating efficacious achievement of large surface areas for facile exchange of proton or oxygen-containing intermediates5,23. In particular, numerous nanocrystals are distributed uniformly at the surface, forming plentiful surface active sites in this hybrid catalyst. The selected area electron diffraction pattern (Fig. 1c), combined with high-resolution transmission electron microscopy (TEM) images (Fig. 1d, Supplementary Fig. 1), further reveal the nanoscale features of the FeP and Ni2P particles with diameters of 5–30 nm. The interplanar spacings of these nanoparticles are resolved by TEM to be around 0.204 and 0.502 nm corresponding to the (021) and (010) planes of Ni2P crystals, and 0.181 and 0.193 nm corresponding to the (103) and (220) planes of FeP crystals. To determine the distribution of Ni, Fe, and P elements in the as-prepared samples, elemental mapping was carried out using TEM, confirming the homogenous distribution of Ni, Fe, and P elements in the FeP/Ni2P nanoparticles (Fig. 1e). The energy dispersive X-ray (EDX) spectrum (Supplementary Fig. 2) shows that the Ni, Fe, and P elements are present with an atomic ratio close to 2:1:2, consistent with the high-resolution TEM observations.
The chemical composition and oxidation states of the catalysts were further unveiled by X-ray photoelectron spectroscopy (XPS) and X-ray diffraction (XRD). The P 2p core level spectrum can be fit with two doublets (Fig. 1f), with one located at the binding energies of 129.3 and 130.1 eV attributing to phosphorus anions of metal phosphides, and the other at 133.5 and 134.3 eV indicative of phosphate-like P arisen from possible surface oxidation, as has been observed previously24,25,26. The XPS spectrum of Fe 2p3/2 core level (Supplementary Fig. 3a) can be deconvoluted into three main peaks with binding energies of 707.0, 709.9, and 711.9 eV assigned to FeP, Fe-based oxide, and phosphate, respectively, caused by possible superficial oxidation when exposing FeP samples to air26,27,28, while another peak located at 714.3 eV is arisen from the relevant satellite peak. This peak deconvolution is also applied to the Ni 2p3/2 core level spectrum (Supplementary Fig. 3b), where three binding energies located at 853.6, 856.4, and 861.0 eV are ascribed to Ni2P, Ni-PO x , and the corresponding satellite peak, respectively. These information means that both the FeP and Ni2P contribute to the overall signals with the binding energy at 129.3 eV of P 2p3/2, even though it is difficult to distinguish the binding energy difference between these two compounds. According to the survey spectrum (Supplementary Fig. 4) and distribution quantification (Supplementary Table 1), it is estimated that the percentage of surface oxidized species in FeP nanoparticles is close to 74.8%, and the percentage in Ni2P is around 13.5%, which indicates that the original Fe–Ni–P samples are heavily oxidized at the surface. A typical XRD pattern (Fig. 1g) reveals the main indexes from the as-prepared FeP/Ni2P hybrid and Ni foam support. The two strongest peaks at 45° and 52° are mainly originated from the Ni foam support (ICSD-53809). All the other peaks are the characteristic ones of FeP (ICSD-633046) and Ni2P (ICSD-646102), consistent with our TEM analysis.
Oxygen evolution catalysis
We first evaluated the catalytic OER activity of this Fe–Ni–P hybrid catalyst in 1.0 M KOH electrolyte6,29. Representative polarization curves in Fig. 2a and b show the geometric current density plotted against applied potential vs reversible hydrogen electrode (RHE) of this Fe–Ni–P hybrid electrode relative to Ni2P and benchmark IrO2 catalysts. The effect of capacitive current on the catalytic activity, originating from the Ni ions oxidation, is minimized by calculating the average activity from the forward and backward sweeps of a cyclic voltammetry (CV) curve (Supplementary Fig. 5)30,31. Strikingly, the Fe–Ni–P hybrid requires an overpotential of only 154 mV to deliver 10 mA cm−2, which is 127 mV less than the state-of-the-art IrO2 catalyst (281 mV). At 281 mV, our FeP/Ni2P catalyst achieves a current density up to 690 mA cm−2, which is 69-fold higher than the benchmark IrO2, demonstrating a huge improvement of the OER activity. Indeed this overpotential of 154 mV in alkaline conditions is among the lowest for catalyzing OER thus far (Supplementary Table 2), even surpassing the presently most active NiFe LDH (double layered hydroxide) catalyst (~200 mV)16,32. We measured a very small Tafel slope of 22.7 mV dec−1 in the low overpotential ranges33 (Fig. 2c, Supplementary Fig. 6), which is much smaller than those of the reference materials Ni2P (102.3 mV dec−1) and IrO2 (71.7 mV dec−1), and also smaller than most of the OER catalysts reported (Supplementary Table 2). Specifically, we further compared the OER activity with other available bifunctional catalysts as shown in Fig. 2d and e. It is evident that our catalyst requires the lowest overpotential 154 mV to achieve 10 mA cm−2, and very large current density (1277 mA cm−2) at 300 mV overpotential, indicating the potential to be used for overall water splitting with large current densities at small cell voltage.
To elucidate the origins of this remarkably high OER catalytic activity, we performed electrochemical impedance spectroscopy (EIS) and double-layer capacitance (Cdl) investigations on this FeP/Ni2P electrode. This capacitance Cdl determined by a simple CV method5,29,34,35,36 (Supplementary Fig. 7) is calculated to be 19.3 mF cm−2 for the Fe–Ni–P hybrid electrode (Fig. 2f), very close to that of the Ni2P catalyst (14.5 mF cm−2). This manifests that depositing FeP on the Ni2P surface does not result in huge changes in the active surface area, while the electrochemical OER performance of FeP/Ni2P is much better than Ni2P. For instance, our FeP/Ni2P hybrid achieves 1000 mA cm−2 at 293 mV, while Ni2P can deliver only 32 mA cm−2 at this overpotential, making our FeP/Ni2P catalyst ~30-fold better than the Ni2P catalyst, heralding that synergistic effects between FeP and Ni2P in the hybrid is the main contributor to our superior catalytic performance, not just the high active surface area. Meanwhile, the EIS spectra show that this FeP/Ni2P hybrid has a lower charge-transfer resistance at the interface of the catalysts with Ni foam, leading to faster OER kinetics compared to the Ni2P catalyst (Supplementary Fig. 8). Additionally, according to our simulations, both the FeP(001)/Ni2P and FeP(010)/Ni2P have electrons transferred from Ni2P to FeP at neutral with 0.15 C m−2 and 0.097 C m−2, or 0.075e−and 0.051e− per surface Ni, respectively. Since electrons are depleted on Ni2P, holes are created and the Fermi level on Ni2P is shifted downwards, which facilitates the OER process. Especially, the charge transfers in the presence of 2, 3, and 4 layers of FeP on Ni2P were further calculated to understand the effect of different loadings of FeP on OER activities. The corresponding values are 0.009e−, 0.075e−, and 0.078e− per surface Ni, respectively. The result of converging charge transfers in the presence of more FeP implies that there is no more advantage in charge transfer beyond a certain amount of FeP is used, which leads to similar activities. Furthermore, the catalytic OER performances were compared by growing additional Ni2P particles, FeP particles with different catalyst loadings on top of Ni foam (Supplementary Figs. 9–11). It is obvious that increasing the loading of Ni2P particles has very few effects on improving the OER performances, and an oxidation peak regarding the NiII to NiIII becomes stronger with the increase of Ni2P loadings (Supplementary Fig. 9). Once FeP particles were grown atop the Ni2P/Ni foam, the performance can be greatly enhanced due to the following reasons: the Ni2P/Ni support has good conductivity and high surface area for growing uniform FeP particles in small size with enhanced OER activity, the oxidation peak of NiII to NiIII can be weakened by FeP modification (Supplementary Fig. 9–11), and many Fe impurities are possibly provided to improve the catalytic activity of underlying Ni2P catalyst by Fe incorporation37. All these information confirms strong synergistic effects between FeP and Ni2P particles. Finally, it is noted that there are a large amount of oxidized species at the surface of original FeP/Ni2P (Supplementary Fig. 3). These surface oxidized species may play a positive role in the OER activity according to recent studies38,39,40. It is possible that they act as a labile ligand to vary the coordination or chelating modes during the redox switching process, and also facilitates the 4e multiproton-coupled electron transfers step in the OER process. The formation of metal phosphide–metal oxide interface may also be helpful to the efficient carrier transportation from the phosphide core to the oxidized species40. Therefore, we attributed the excellent OER activity of our FeP/Ni2P hybrid catalyst to the presence of surface oxidized species, fast electron transport, and synergistic effects between FeP and Ni2P.
Electrochemical durability is another key index to evaluate the performance of electrocatalysts. Obviously, after 5000 cycling test, the CV curve of this FeP/Ni2P hybrid is nearly identical to the original one, suggesting its excellent durability during cycling scans (Fig. 2g). We also probed the long-term electrochemical stability of the catalyst tested at 100 mA cm−2, finding that the real-time potential remains nearly constant during a 24 h continuous operation (Fig. 2h). These results establish the strong durability of FeP/Ni2P catalyst for OER in alkaline electrolyte. Further insights into the chemical compositions for post-OER samples by XPS (Supplementary Fig. 12) and XRD (Supplementary Fig. 13) confirm that a mixture of nickel and iron oxides/oxyhydroxides evolves at the surface of the FeP/Ni2P hybrid, possibly acting as the real active sites for OER6. This behavior is also observed for many metal sulfides41, phosphides42, or selenides19, which are easily oxidized to oxides or hydroxides under the OER process at high anodic potentials.
Hydrogen evolution catalysis
In addition to the excellent OER performance, we found that this FeP/Ni2P hybrid is highly active towards HER in the same electrolyte. It is evident that the bare Ni2P is not a good HER catalyst requiring a large overpotential of 150 mV to deliver a current density of −10 mA cm−2 (Fig. 3a, Supplementary Fig. 14). Distinctly, our FeP/Ni2P hybrid obtains −10 mA cm−2 at an extremely low overpotential of 14 mV, which is the lowest value among non-noble metal-based HER catalysts (Supplementary Table 3), and indeed is comparable to that of Pt (59 mV) in alkaline electrolyte. Meanwhile, the Tafel slope of this FeP/Ni2P catalyst is only 24.2 mV dec−1 in the low overpotential ranges (Fig. 3b, Supplementary Fig. 15), which is lower than that of Ni2P (117.3 mV dec−1) and Pt (36.8 mV dec−1). To gain further insight into the outstanding HER activity, the Cdl values (Fig. 3c, Supplementary Fig. 16) were utilized to compare the active surface area, confirming that both high active surface area (907.8 mF cm−2) and small charge-transfer resistance (Supplementary Fig. 17) contribute greatly to the outstanding HER catalytic activity of this FeP/Ni2P hybrid5,23. It is noted that the capacitance is different when the same FeP/Ni2P catalyst was used for HER and OER, which is possibly due to the different origins of active sites for the OER and HER. In particular, we prepared pure Ni2P* catalyst on Ni foam with similar mass loading in the same growth conditions as FeP/Ni2P. In this case, we found that Ni2P* catalyst still shows catalytic activity inferior to the FeP/Ni2P hybrid, and has a smaller Cdl value (Fig. 3c). After normalizing the polarization curves by the active surface area or Cdl difference, the FeP/Ni2P hybrid still exhibits better catalytic HER activity than pure Ni2P* catalyst (Supplementary Fig. 18), meaning that FeP/Ni2P has better intrinsic activity than pure Ni2P* catalyst. Then the intrinsic catalytic activity was assessed by the turnover frequency (TOF) for each active site quantified by an electrochemical method43 (Supplementary Note 1, Supplementary Fig. 19). From this method, the number of active catalytic sites for the FeP/Ni2P hybrid is around 2.5 times that of the Ni2P* catalyst, and accordingly the TOF of the FeP/Ni2P hybrid is calculated to be 0.163 s−1 at 100 mV overpotential, which is much higher than that of pure Ni2P* catalyst (0.006 s−1) at the same overpotential, suggesting that the addition of FeP particles on Ni2P surface contributes more to the improvement of the HER activities of this FeP/Ni2P hybrid. This is further supported by measuring the catalytic activities of additional Ni2P or FeP particles with different loadings grown on Ni2P/Ni support (Supplementary Fig. 9–11). More interestingly, this FeP/Ni2P hybrid still shows outstanding HER activity compared to other available bifunctional catalysts (Fig. 3d and e). To evaluate its stability during electrochemical HER, a long-term cycling test (Fig. 3f) and continuous operation for 24 h of hydrogen release at −100 mA cm−2 (Fig. 3g) were performed in 1 M KOH, demonstrating its good stability.
In order to figure out the factors contributing to the superior HER activity, we performed density functional theory (DFT) calculations on this catalyst. According to Fig. 1d, (021) and (010) lattice planes are observed on Ni2P nanoparticles. Since (021) and (010) of Ni2P have a simple common perpendicular direction (100), we chose this plane to model Ni2P (Supplementary Fig. 20). On the other hand, the two directions, (220) and (103) on FeP, do not share a common simple perpendicular direction, hence we chose two different directions, (001) and (010), to model FeP. Since the overall system involved two materials, the interactions between FeP and Ni2P were modeled by placing FeP on top of Ni2P, which is reasonable since an Ni foam was used as the material on which Ni2P and FeP were grown. The corresponding lattice distances were chosen to minimize the percent changes in both Ni2P and FeP. The hydrogen adsorption energy, ∆GH, was calculated in the same way as in our previous study5 and is shown in Supplementary Table 4. As shown in Fig. 3h, Supplementary Fig. 20 and Supplementary Table 4, pure Ni2P (001) leads to a relatively strong exothermic ∆GH (0.306 eV), indicating that it is not the most active center for the hydrogen evolution electrocatalysis, which we confirmed experimentally (Fig. 3a, b, Supplementary Fig. 18). However, this hydrogen adsorption energy │∆GH│ is reduced significantly to 0.255 and 0.230 eV for a very thin FeP (100) or FeP (010) crystal (~3 layers), respectively, hybridized atop with Ni2P. It is worth pointing out that we confine our calculation a thin layer of FeP crystal, ignoring the particulate size (5–30 nm), so we hypothesized that the as-synthesized FeP nanoparticles along with Ni2P preferentially expose the most active facets as those of bulk FeP (001) crystal, which results in further reduction of │∆GH│ to only 0.06 eV, contributing to the high activity not seen in typical FeP crystals. This conclusion is also supported by the above experiments regarding the TOF calculation. Thus, both the experiment and theory support that this hybrid catalyst is an efficient HER electrocatalyst.
Overall water splitting
Given the outstanding OER and HER activities in 1 M KOH electrolyte, we further utilized this FeP/Ni2P hybrid as both anode and cathode in a two-electrode configuration for overall water splitting in the same electrolyte. Remarkably, the cell voltage to afford a current density of 10 mA cm−2 is as low as 1.42 V with a relatively low Tafel slope of 69.5 mV dec−1 (Fig. 4a, b, Supplementary Figs. 21 and 22), substantially lower than that of the coupled benchmark IrO2-Pt catalysts (1.57 V), and superior to most previously reported bifunctional electrocatalysts, which generally need cell voltages higher than 1.50 V to deliver the same current density (Fig. 4c, Supplementary Table 5). This cell voltage also manifests that the electrical-to-fuel efficiency of water-splitting electrolyzers at 10 mA cm−2 is dramatically elevated to 86.6% using only this material, making it of great potential for scale-up water electrolysis with high efficiency and low cost. Even though the best bifunctional NiFe LDH catalyst reported recently can deliver 20 mA cm−2 at a cell voltage of 1.50 V, which is close to our FeP/Ni2P catalyst (1.48 V), but a much larger cell voltage of 1.70 V is needed to achieve only 60 mA cm−2, meaning low energy conversion efficiency at high current density16. Nearly all the bifunctional electrocatalysts require larger than 1.69 V to reach 100 mA cm−2 for the overall water splitting (Fig. 4d). Even at 1.7 V cell voltage, most of the electrolyzers can only deliver current densities below 110 mA cm−2 (Fig. 4e). In contrast, our FeP/Ni2P catalyst can readily drive water electrolysis at high current densities of 100, 500, and 1000 mA cm−2 at very low cell voltages of 1.60, 1.72, and 1.78 V, respectively, showing that our catalyst performs outstandingly over the full range of current density. We further tested the long-term stability of our FeP/Ni2P electrode at 30 and 100 mA cm−2 for 36 h, showing no detectable voltage decay (Fig. 4f). Moreover, we further examined extremely high-current operation of the electrolyzer at 1.72 V for overall water splitting at 500 mA cm−2, which is a big step toward real industrial applications6,22. In comparison, commercial alkaline water electrolysis10,15 requires 1.8–2.4 V to generate 200–400 mA cm−2, while no previous bifunctional catalysts show catalytic activities superior to the commercial ones with good durability at high current density above 200 mA cm−2. In contrast, our alkaline electrolyzer only requires 1.72 V to afford 500 mA cm−2 while also exhibiting excellent stability for more than 40 h confirmed by steady chronopotentiometric testing (Fig. 4f). Especially, using the gas chromatography-based technique5, we found that H2 and O2 are the only gas products during water electrolysis, and the molar ratio between H2 and O2 is close to 2:1 (Supplementary Fig. 23), suggesting that nearly all the electrons are actively involved in the catalytic reaction. This demonstrates outstanding overall-water-splitting activity of our hybrid catalyst, making it an excellent condition for industrial use.
In summary, we developed an FeP/Ni2P hybrid catalyst supported on 3D Ni foam that proves to be an outstanding bifunctional catalyst for overall water splitting, exhibiting both extremely high OER and HER activities in the same alkaline electrolyte. Indeed, it requires a very low cell voltage of 1.42 V to afford 10 mA cm−2 in alkaline water electrolyzers, while at the commercially practical current density of 500 mA cm−2, it demands only a voltage of 1.72 V lower than those for any reported bifunctional catalysts, and maintains its excellent catalytic activity for more than 40 h at a current density of 500 mA cm−2, paving the way for promising large-scale hydrogen generation.
Red phosphorous powder (Sigma-Aldrich, ≥97%, CAS No. 7723-14-0), Iron(III) nitrate nonahydrate [Sigma-Aldrich, Fe(NO3)3·9H2O, ≥99.95%, CAS No. 7782-61-8], Pt wire (CH Instruments, Inc.), Nafion 117 solution (5%; Sigma-Aldrich), iridium oxide powder (Alfa Aesar, IrO2, 99%), potassium hydroxide (Alfa Aesar, KOH, 50% wt/vol), and Ni foam (areal density 320 g cm−2) (ref. 2) were used without further purification.
These metal phosphides (Ni2P and FeP) were grown by chemical vapor deposition in a tube furnace, in which Ni foam, Fe(NO3)3, and phosphorus were utilized as the Ni, Fe, and P sources, respectively. Namely, we first immersed a commercially hydrophobic Ni foam into an aqueous Fe(NO3)3 solution (0.37 M), which was then converted to mainly Ni2P and a very small fraction of FeP at 450 °C in Ar atmosphere, with phosphorus powder supplied upstream. After that, the samples were naturally cooled down under Ar gas protection, which became hydrophilic after first phosphidation. In the following, a second-time phosphidation was performed after the samples were immersed into the Fe(NO3)3 solution again. The catalyst loading is around 8 mg cm−2 for the FeP/Ni2P catalyst. For comparison, the as-prepared Ni2P samples were obtained in the same growth conditions without the addition of Fe(NO3)3, and the Ni2P* samples were grown in the same experimental conditions by using Ni(NO3)2 (0.37 M) instead of Fe(NO3)3. Three different concentrations of Fe(NO3)3 (0.25, 0.37, and 0.50 M) and Ni(NO3)2 (0.17, 0.37, and 0.50 M) precursors were prepared to grow different catalyst loadings of FeP (6.0, 8.0, and 12.5 mg cm−2) or Ni2P particles (3.0, 7.5, and 10.5 mg cm−2) on the surface, respectively, so as to optimize the experimental conditions and relevant catalytic activities for the HER and OER. The optimal loading of FeP/Ni2P hybrid catalysts was found to be around 8 mg cm−2 on Ni foam.
The electrochemical tests were performed via a typical three-electrode configuration in 100 ml 1 M KOH electrolyte6,29. The polarization curves for the HER were recorded by linear sweep voltammetry with a scan rate of 1.0 mV s−1. For the OER and overall water splitting, in order to minimize the effect of capacitive current originating from the Ni ions oxidation on the catalytic performance, CV curves with the forward and backward sweeps with a very small scan rate of 1 mV s−1 were utilized to calculate the average activity. A carbon paper was used as the counter electrode for both the HER and OER tests. The scan rate for the cycling tests was set to 50 mV s−1. All the potentials shown here were converted to RHE.
GGA level of DFT was employed to calculate the relative energies of relevant structures in this study. More specifically, PBE44,45 functional with the D3 46 correction was used for both geometry optimizations and the single point free energies. Geometry optimizations were performed in VASP47,48 with projected augmented wave (PAW)49,50 and VASPsol51 solvation. The kinetic energy cutoff was 300 eV for geometry optimization, and 13 Hartree (354 eV) for single point energy. The single point free energies were calculated in jDFTx52,53,54,55,56 with CANDLE57 implicit solvation and GBRV uspp pseudopotentials. The final free energy G was calculated as G = F − neU + ZPE + Hvib − TSvib, where F is the energy of the solvated Kohn–Sham DFT electronic system, ne is the number of electrons, and U is the chemical potential for the electrons. Also, in order to understand the charge transfer process between Ni2P and FeP, we calculated the Mulliken charges of the hybrid FeP/Ni2P structure and summed up the charges for each compound. Since Mulliken charges can only be rigorously defined using localized basis functions, we performed this set of DFT calculations on the same structures used in the HER part of the study using Gaussian basis functions in CRYSTAL14 with PBE and the same k-point grid.
The data that support the findings of this work are available from the corresponding author upon reasonable request.
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This project has been partially supported by the US Department of Energy under a grant DE-SC0010831. J.S. and S.C. also express their acknowledgements to the support from TcSUH as the TcSUH Robert A. Welch Professorships in High Temperature Superconducting (HTSg) and Chemical Materials (E-0001). W.A.G. and Y.H. acknowledge support from NSF (CBET 1512759). The calculations were performed on PEREGRINE (NREL), XSEDE (NSF ACI-1053575), and NERSC (DOE DE-AC02-05CH11231). J.B. thanks the support by the Robert A. Welch Foundation (E-1728). H.Z. acknowledge the supports from Hundred Youth Talents Program of Hunan Province and the'XiaoXiang Scholar' Talents Foundation of Hunan Normal University.
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Journal of Materials Science (2018)