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Research Article | Open Access

Volume 2020 |Article ID 9068270 |

Huanhuan Liu, Zhenhua Yan, Xiang Chen, Jinhan Li, Le Zhang, Fangming Liu, Guilan Fan, Fangyi Cheng, "Electrodeposition of Pt-Decorated Ni(OH)2/CeO2 Hybrid as Superior Bifunctional Electrocatalyst for Water Splitting", Research, vol. 2020, Article ID 9068270, 11 pages, 2020.

Electrodeposition of Pt-Decorated Ni(OH)2/CeO2 Hybrid as Superior Bifunctional Electrocatalyst for Water Splitting

Received21 Aug 2020
Accepted27 Oct 2020
Published15 Dec 2020


The facile synthesis of highly active and stable bifunctional electrocatalysts to catalyze water splitting is attractive but challenging. Herein, we report the electrodeposition of Pt-decorated Ni(OH)2/CeO2 (PNC) hybrid as an efficient and robust bifunctional electrocatalyst. The graphite-supported PNC catalyst delivers superior hydrogen evolution reaction (HER) and oxygen evolution reaction (OER) activities over the benchmark Pt/C and RuO2, respectively. For overall water electrolysis, the PNC hybrid only requires a cell voltage of 1.45 V at 10 mA cm−2 and sustains over 85 h at 1000 mA cm−2. The remarkable HER/OER performances are attributed to the superhydrophilicity and multiple effects of PNC, in which Ni(OH)2 and CeO2 accelerate HER on Pt due to promoted water dissociation and strong electronic interaction, while the electron-pulling Ce cations facilitate the generation of high-valence Ni OER-active species. These results suggest the promising application of PNC for H2 production from water electrolysis.

Dedicated to the 100th anniversary of Chemistry at Nankai University

1. Introduction

Hydrogen is the ideal alternative of fossil fuels as an important clean energy and industrial material [1, 2]. Water electrolysis using electricity from renewable energy is a facile and attractive technique to produce hydrogen with high purity [3, 4]. Electrocatalysts play the paramount role in overcoming the slow dynamics of both hydrogen and oxygen evolution reactions (HER and OER) [57]. While Pt and Ru/Ir-based compounds are highly efficient to catalyze HER and OER, respectively [8, 9], their fancy price, extremely low elemental reserves, and unsatisfactory durability limit large-scale applications [1012], calling for strategies to improve stability and reduce noble metal loading [1315].

In alkaline media, although Pt is the benchmarking HER catalyst, its catalytic activity is still restrained by water dissociation due to the lack of oxyphilic surfaces to cleave the O−H bond of H2O [16, 17]. The synergistic effect mechanism of Pt and Ni(OH)2 has been indicated in previous studies: Ni(OH)2 promotes the water dissociation and the generation of hydrogen atoms, which are absorbed at Pt sites nearby to recombine into hydrogen molecules [1824]. In addition, using a bifunctional catalyst could avoid different synthetic processes of electrocatalysts and simplify the water electrolysis device to lower the cost [25]. However, Pt/Ni(OH)2 catalysts do not favor the OER due to sluggish kinetics. The electronic structure of Ni could be modulated through the integration of CeO2 in Ni(OH)2, which could further promote to form γ-NiOOH, making the Ni(OH)2/CeO2 a superb OER catalyst [26, 27]. Meanwhile, Ce can impose large electronic perturbation to Pt nanoparticles, which may enhance the HER ability of the neighboring Pt sites [28]. Therefore, the Pt-Ni(OH)2-CeO2 hybrid has great potential for electrocatalysis of both HER and OER but has not been reported previously. Besides, the Pt-based hybrid catalysts usually suffer from complicated preparation procedures, particle agglomeration, and weak adhesion between catalyst and substrate [2931].

In this study, we report a facile electrodeposition method to synthesize ultrafine Pt nanoparticles (NPs) decorated Ni(OH)2/CeO2 nanosheets (abbreviated as PNC) via anion intercalation and cathodic electrodeposition method. The Pt NPs with an average size of 3.1 nm are homogeneously deposited on the Ni(OH)2/CeO2 (abbreviated as NC) nanosheets, which could increase the exposure area of active sites and improve the utilization of Pt. Additionally, the mosaic-structured NC nanosheets not only effectively catalyze the OER but also enhance the HER activity of Pt due to electronic modulation and promoted dissociation of water. Furthermore, anion intercalation and in situ growth of the hybrid catalyst on graphite construct interfaces with strong adhesion, resulting in efficient electron transportation and enhanced stability. As a result, the prepared PNC electrocatalyst exhibits superior activity and stability to catalyze overall water electrolysis.

2. Result and Discussion

The PNC catalyst was synthesized through a two-step cathodic electrodeposition process as illustrated schematically in Figure 1(a). Graphite substrate was pretreated by applying a positive potential to allow nitrate ions inserting into graphite layers to enhance the interface of catalyst and graphite. The potential was reversed to realize the cathodic coelectrodeposition of cerium dioxide and nickel hydroxide on graphite. Subsequently, Pt NPs were deposited on the NC nanosheets to obtain the PNC hybrid electrode. In this two-step deposition process, the Pt loading can be reduced and the exposure of Pt is increased to enhance the utilization of Pt, outperforming the reverse sequence when Pt is deposited prior to transition metal hydroxide. The involved reactions in the preparation of PNC are described by equations (1)–(4). For comparison, Pt/G and Pt-Ni(OH)2 (abbreviated as PN) electrodes were obtained through a similar process.

Figure 1(b) shows the X-ray diffraction (XRD) patterns of the prepared Pt, PN, and PNC. In addition to the reflections of graphite substrate, the diffraction peaks centered at 2θ of 40.0 and 46.5° correspond to the (111) and (200) planes of the face-centered cubic (fcc) Pt (space group of Fm-3m), respectively. The Ni(OH)2 and CeO2 signals are not observed in XRD because of weak crystalline state of Ni(OH)2 and low content of CeO2 (supplementary Figure S1). The morphology and microstructure were investigated by a scanning electron microscope (SEM) and transmission electron microscope (TEM). The prepared PN and PNC are composed of aggregated nanoparticles with interparticle pores and flat nanosheets with a thickness of 5–10 nm, while the control Pt/G is granular (Figure 1(c) inset and supplementary Figure S2). This rimous texture and interlinked lamellar morphology would facilitate the penetration of electrolyte inside the electrode and increase the active site exposure area. Contact angle tests indicate superhydrophilic property of PNC (supplementary Figure S3), which can be attributed to the rimous texture and the presence of O−H bond in hydroxide nanosheets. TEM images (Figure 1(c) and supplementary Figure S4) show uniform dispersion of Pt NPs on the hydroxide support. The average size of Pt NPs is 3.1 nm in PNC, smaller than PN (3.4 nm) and Pt/G (13.2 nm). The superhydrophilic surfaces of NC favor the nucleation and growth of Pt, leading to smaller NPs and uniform distribution [32, 33]. The high dispersion of Pt NPs on the mosaic structure of CeO2 and the weak crystallinity of Ni(OH)2 would enrich the interface between metal and oxide/hydroxide. High-resolution TEM (HRTEM) reveals lattice spacings of 0.314 and 0.227 nm (Figure 1(d)), which are separately assigned to the (111) planes of fcc CeO2 and fcc Pt. Energy dispersive spectroscopy (EDS) mapping further confirms the homogenous distribution of Pt, Ni, Ce, and O in PNC (supplementary Figure S5). As detected by EDS and inductively coupled plasma atomic emission spectroscopy (ICP-AES) (supplementary Figure S6), the Pt loadings are 8.8 and 8.2 wt.% in PN and PNC, respectively. The Pt content could be tuned by adjusting the electrodeposition time in H2PtCl6 solution (supplementary Table S1).

The oxidation states of Pt, Ni(OH)2, and CeO2were detected by X-ray photoelectron spectroscopy (XPS) spectra (Figure 2). The survey spectra confirm the presence of Pt, Ni, and O in PN and additional Ce in PNC (Figure 2(a)). As shown in Figure 2(b), Pt 4f spectra display two pairs of peaks (4f7/2 and 4f5/2), corresponding to dominant Pt(0) (75.9%) and surface Pt(II) (24.1%) in PNC. For PN, the atomic ratio of Pt(0) and Pt(II) is 90.7% and 9.3%, respectively. The higher Pt(II) content and 0.3 eV positive shift of Pt(0) peaks in PNC compared to PN suggest partial oxidation of Pt and electronic interaction between Pt and NC [28, 34, 35]. The peak shift also indicates a downshift of the d-band center of Pt in PNC, which could favor hydrogen adsorption on Pt and accelerate the recombination of Had to form H2 [3638].

As discerned by Ni 2p XPS spectra (Figure 2(c)), both Ni (II) (855.6 eV) and Ni (III) (857.1 and 856.8 eV) exist in PNC and PN. There is a 0.3 eV positive shift of Ni(III) in PNC, indicating electron transfer from Ni to Ce. The electron-pulling ability of ceria would accelerate the generation of NiOOH active sites for OER. In addition, the coexistence of Ni 3p peak in the Pt 4f region confirms Ni(II) species in Ni(OH)2 [39]. The O 1s spectrum (Figure 2(d)) of PNC shows deconvoluted peaks at 528.6, 530.5, 531.6, and 532.6 eV assigned to CeO2, Ni(OH)2, NiOOH, and H2O, respectively [26, 40]. Collecting XPS results suggest strong electron interaction and synergy effect between Pt and Ce-Ni oxide/hydroxide in PNC, which would favor the formation of more electrocatalytically active species [26, 41].

The electrocatalytic HER performances were investigated by linear sweep voltammetry (LSV). As shown in Figure 3(a), the onset potential of PNC is near 0 mV and it needs only 76 mV overpotential at 100 mA cm−2, significantly outperforming PN (105 mV), Pt/G (124 mV), and 20 wt.% Pt/C (153 mV). At a high applied current density, rapid generation and release of bubbles occur while no catalyst desquamating from the electrode surface is observed for PNC (supplementary Movie S1). The results indicate superior mechanical stability of the electrodeposited hybrid material, which is favorable for industrial application operating under large current density.

Tafel slope is a figure-of-merit to assess HER kinetics of electrocatalysts. In Figure 3(b), the PNC represents a Tafel slope of 38 mV dec−1, which is much smaller than PN, Pt/C, and Pt/G (45, 56, and 58 mV dec−1) and indicates rapid HER kinetics in PNC (Tafel-Volmer mechanism). The HER process in alkaline condition includes the Volmer adsorption step () combined with the Heyrovsky desorption step () or the Tafel recombination step () [42, 43]. In alkaline media, the Volmer step is suggested to determine the HER rate of Pt, due to the sluggish dissociation of water [44, 45]. For the PNC hybrid, the metal (hydro)oxides are efficient to split O−H bond and accelerate the Volmer step, leading to an improvement in HER kinetics. The electrode kinetics of the HER process is further investigated by conducting the EIS experiments, where the equivalent circuit was composed of an electrolyte resistance () in series with a parallel connection of a constant phase element (CPE) and a charge-transfer resistance () [46]. From the Nyquist plots (Figure 3(c)) recorded at the potential of −0.026 V vs. RHE, PNC has a smaller compared to Pt/C, Pt/G, and PN. The enhanced charge transfer is attributed to the interfacial electron interaction, plate-like nanostructure with shorter diffusion pathway, and rimous texture that allows facile electrolyte access.

The mass activities were calculated to evaluate the utilization ratio of Pt in the catalysts (Figure 3(d)). At the overpotential of 150 mV, the PNC electrode achieves a remarkable current density of 3.144 A mg−1Pt, which is almost 10 and 1.6 times those of the counterpart 20 wt.% Pt/C and PN (0.316 and 2.011 A mg−1Pt). The improvement of the mass activity of Pt could be ascribed to the high dispersion and ultrafine particle of Pt. The highest HER activities of PN and PNC are attained when the Pt mass loadings are 8.8 wt.% and 8.2 wt.%, respectively (supplementary Figure S7). Moreover, cyclic voltammetry (CV) curves at different scan rates are measured to obtain the electrochemical double-layer capacitance () for evaluating the electrochemical active surface areas (ECSAs) (supplementary Figure S8). The current densities are normalized by ECSA or mass of the catalyst to determine specific activity or mass activity at an overpotential of 150 mV. Clearly, PNC delivers overwhelming values as compared to PN, Pt/C, and Pt/G (supplementary Figure S9). The intrinsic catalytic activity can be further evaluated by the turnover frequency (TOF) [47]. Assuming Pt as HER active site, the calculated TOF of PNC is 3.488 s−1 at overpotential of 150 mV, significantly outperforming PN (2.127 s−1), Pt/G (0.254 s−1), and Pt/C (0.455 s−1) (Figure 3(e)). Besides, PNC exhibits superior HER performance as compared with those of previously reported electrocatalysts (supplementary Table S2).

The long-term catalytic durability was investigated by CV sweeping for 1000 cycles, indicating negligible activity loss of the PNC electrode. The overpotential only slightly increases by 21 mV at 1000 mA cm−2, surpassing that of Pt/C (116 mV) (Figure 3(f) and supplementary Figure S10). The catalytic stability of PNC was further tested by chronopotentiometry at a large current density of 1000 mA cm−2. As shown in Figure 3(f) inset, PNC shows only a very small increase of overpotential after 70 h test, while Pt/C experiences an apparent increase in polarization. Microscopy imaging on cycled electrode reveals that PNC retains its texture and morphology without noticeable particle agglomeration or inhomogeneous elemental distribution, irrespective of a particle size increase of Pt NPs from 3.1 to 5.6 nm (Supplementary Figure S11). Furthermore, the XRD analysis suggests no phase change, while the XPS results show essentially preservation of the oxidation states of Pt and Ce states but an increase in the proportion of Ni (II) species (supplementary Figure S12). The confinement of Pt NPs in hydroxide and the firm adhesion of electrodeposit on graphite could account for the remarkable catalytic and structural stability at large current density.

The OER performances were also assessed by LSV curves (Figure 4(a)). The PNC exhibits a lower overpotential of 186 mV (100 mA cm−2), as compared to PN (279 mV), RuO2 (321 mV), and Pt/G (1094 mV). The current fluctuation in the LSV curves of RuO2 results from the formation of large O2 bubbles. Differently, PNC manifests enhanced and stable OER performance without rigorous fluctuation or large bubble generation at high current density (supplementary Movie S2). Furthermore, the Tafel slope of PNC is 54 mV dec−1, lower than that of PN (63 mV dec−1), RuO2 (71 mV dec−1), and Pt/G (95 mV dec−1) (Figure 4(b)). Remarkably, the OER activity of PNC is among the highest referencing results (supplementary Table S3).

Figure 4(c) shows the EIS data to assess the OER kinetics. At the potential of 1.474 V vs. RHE, a much lower value (1.4 Ω) was obtained on PNC, in comparison to PN (3.7 Ω), Pt/G (18.4 Ω), and RuO2 (3.1 Ω). Continuous CV sweeping was tested to investigate the OER durability of PNC (Figure 4(d)). The OER overpotential at 1000 mA cm−2 increases only 12 mV after 1000 cycles, revealing insignificant change as compared with RuO2 (343 mV) (supplementary Figure S13). In addition, the chronopotentiometric response (Figure 4(d) inset) shows unconspicuous decay at 1000 mA cm−2 for 70 h, further indicating superior OER catalytic stability of PNC. A combination of SEM, TEM, EDS, and XRD characterizations indicates no apparent change in morphology, composition, and phase but a slight increase of particle size after extended OER electrocatalysis on PNC (supplementary Figures S14 and 15). Of note is that an increased ratio of NiOOH, which has been regarded as the active center of OER [26, 48], can be analyzed by XPS results (supplementary Figure S15d).

Based on the excellent performances of PNC for both the HER and the OER, a symmetric two-electrode cell was constructed using PNC as a bifunctional electrode for water electrolysis. As shown in Figure 5(a), the cell delivers a current density of 10 mA cm−2 at an applied voltage of 1.5 V, 100 mV lower than that of the benchmark Pt/C || RuO2 couple (1.55 V). The PNC hybrid competes favorably with most electrocatalysts reported previously for overall water splitting (supplementary Table S4). Remarkably, in the extended stability test at a large current density of 1000 mA cm−2, a constant potential of 2.06 V can be well maintained for 85 h with the faintest degradation (Figure 5(b)). A large amount of bubbles release uniformly from the electrode surfaces without any shedding (supplementary Movie S3). Moreover, the volumes of collected H2 and O2 match well with the theoretical values as a function of time during electrolysis at 1000 mA cm−2 (supplementary Figure S16), indicating nearly 100% faradaic efficiency of PNC || PNC electrolyzer. Excitingly, the PNC-based device can be actuated by a 1.5 V battery for vigorous, stable generation, and release of gas (supplementary Figure S17 and Movie S3), again confirming the high efficiency of PNC to electrolyze water.

Figure 5(c) schematically shows the reaction mechanism of the electrolyzer. We propose that metal hydroxide in PNC promotes the rupture of O−H in water and the generation of adsorbed H atoms (Hads), which adsorb on the Pt surface to recombine into hydrogen molecule. Meanwhile, the OH ions are transformed into O2 on the anode with different metal centers [22, 26, 49]. To gain further insight into the water dissociation process, we performed preliminary DFT calculations on the configuration and evolution of PNC hybrid and dissociation energy of H2O on the interface (Figure 5(d) and supplementary Movie S4). The water is adsorbed at the interface of Ni(OH)2 and CeO2, where O is connected with the Ni atom in Ni(OH)2 and H forms a weak hydrogen bond interaction with O in CeO2. These interactions jointly promote the activation of water, resulting in the fracture of O−H bond in water and the formation of the final structure in Figure 5(d). The process is exothermic (about −2.74 eV), indicating that water dissociation can proceed spontaneously at this interface. Accordingly, the superior performance of PNC can be attributed to the synergistic effect among Pt, Ni(OH)2, and CeO2 in the hybrid, together with the beneficial texture, microstructure, and wettability.

3. Conclusion

In summary, we report the electrodeposition of Pt-Ni(OH)2-CeO2 hybrid on graphite and its application for efficient electrocatalysis of water splitting. In 1.0 M KOH, the PNC electrode needs only overpotentials of 76 and 186 mV to afford 100 mA cm−2 current density for HER and OER, respectively. The turn over frequency and Pt-based mass activity towards HER are significantly improved on PNC than the benchmark Pt/C. Remarkably, when PNC electrode is directly utilized as the anode and cathode, the assembled symmetric water electrolyzer well works at a low applied cell voltage of 1.45 V. Additionally, respectable stability of PNC is attained at 1000 mA cm−2. The superior activity is due to high dispersion of Pt NPs and electronic interaction among Pt, Ni(OH)2, and CeO2 while the durability is ascribed to strong deposit/graphite adherence, electrode hydrophilicity, and facilitated release of gas bubbles. The results indicate that Pt-decorated hydroxide/oxide electrodeposited on graphite is a promising electrocatalyst for overall water electrolysis.

4. Materials and Methods

4.1. Material Synthesis

To prepare the PNC hybrid, cathodic galvanostatic electrodeposition was applied and performed using a two-electrode system in a 50 ml electrolytic bath at 25°C. The working and counter electrode are two graphite plates ( cm) [26]. The graphite plate was first preprocessed by applying an anodic current of 20 mA cm−2 for 300 s to realize NO3 intercalation in the interlamination. Then, a cathodic current of −20 mA cm−2 was applied for 300 s in a nitrate solution containing 0.09 M Ni(NO3)2 and 0.01 M Ce(NO3)3. After that, cathodic depositions at −20 mA cm−2 were performed for different time (50, 100, 150, and 200 s) in 0.02 M H2PtCl6 solution. For comparison, PN was obtained from electrodeposition in 0.1 M Ni(NO3)2 and 0.02 M H2PtCl6 using a similar process, while Pt/G was prepared in 0.02 M H2PtCl6 at 20 mA cm−2 for 300 s.

4.2. Material Characterizations

A JEOL JSM-7500F microscope was used to obtain SEM images. TEM and HRTEM were carried out on a FEI Talos F200X G2 system equipped with EDS. A Rigaku MiniFlex 600 diffractometer was used to measure the XRD patterns. XPS data were collected with a Kratos Axis Ultra DLD spectrometer. Elemental analysis was obtained on ICP-AES (PerkinElmer Optima 83000).

4.3. Electrochemical Measurements

All electrochemical tests were tested by a three-electrode system on AMETEK Parstat 4000 electrochemical workstation in 1.0 M KOH. The electrodeposited electrodes, Hg/HgO, and graphite rod were employed as the working, reference, and counter electrode, respectively. To study the HER performance, LSV curves were tested at 10 mV s−1 from −0.8 to −1.6 V vs. Hg/HgO. The OER activity was tested from 0 to 2.0 V vs. Hg/HgO. To test EIS, the frequency range is set from 100 kHz to 0.01 Hz. Water electrolysis was detected in a two-electrode system, and LSV curves were measured from 1.0 to 2.0 V at 10 mV s−1. Potentials were reported versus reversible hydrogen electrode (RHE) unless noted, in line with the equation . All LSV curves have been iR corrected unless otherwise specified.

The values were determined from the double layer region (without faradaic processes) in the CV curves recorded at different scan rates. The ECSA of the prepared catalysts was calculated according to where is the double-layer capacitance and is the specific capacitance (0.040 mF cm−2) [50].

The TOF was determined by the following equation [51, 52]: where is the current density at a given overpotential (150 mV), is the Faraday constant (96,485 C mol−1), is the electrode surface area (1 cm2), and is the number of moles of active species on the electrode. The Pt content in PN and PNC was quantified by ICP-AES. In TOF calculation, Pt atoms are counted as the active sites in PN and PNC.

4.4. DFT Calculation

Density function theory calculation was performed by using the CP2K package [53]. PBE functional [54] with Grimme D3 correction [55] was used to describe the system. Unrestricted Kohn-Sham DFT has been used as the electronic structure method in the framework of the Gaussian and plane wave method [56, 57]. The Goedecker-Teter-Hutter (GTH) pseudopotentials [58, 59] and DZVPMOLOPT-GTH basis sets [56] were utilized to describe the molecules. A plane-wave energy cut-off of 500 Ry has been employed.

Conflicts of Interest

The authors declare no conflict of interest.

Authors’ Contributions

F. Y. Cheng and Z. H. Yan supervised the research. H. H. Liu carried out the experiments, measured and analyzed the data, and drafted the manuscript. X. Chen, J. H. Li, and L. Zhang participated in electrochemical measurements. J. H. Li, F. M. Liu, and G. L. Fan assisted material characterization and DFT calculation. All the authors participated in the discussion of results and manuscript.


This work was supported by the National Natural Science Foundation of China (21871149, 52001171, and 51571125), the Ministry of Science and Technology (2018YFB1502100), the Tianjin Project (18JCZDJC31100), the Ministry of Education (B12015), the NCC Fund (NCC2020FH03), and the Fundamental Research Funds for the Central Universities.

Supplementary Materials

Figure S1: powder XRD patterns of Ni(OH)2 and NC scratched down from the Ti mesh. Figure S2: SEM images of Pt/G (a, b), PN (c, d), and PNC (e, f) at low (a, c, e) and high (b, d, f) magnification. Figure S3: contact angles measured on graphite substrate (a) before and (b–d) after the electrodeposition of Pt (b), PN (c), and PNC (d). Figure S4: (a, b) TEM images and particle size distribution of PN. (c, d) TEM images and particle size distribution of Pt/G. Figure S5: elemental mapping images of PNC. Figure S6: EDS spectra of (a) Pt, (b) PN, and (c) PNC. Figure S7: HER polarization curves of (a) PN and (b) PNC hybrid with different Pt loadings. Figure S8: CV curves of (a) Pt/C, (b) electrodeposited Pt, (c) PN, and (d) PNC. (e) The corresponding linear fitting of the current density versus scan rates. (f) Comparison of ECSA. Figure S9: (a) specific and mass activities derived from the HER polarization curves at 150 mV. Figure S10: polarization curves of 20 wt.% Pt/C before and after 1000 HER cycles. Figure S11: (a) SEM, (b) TEM, (c) HRTEM, and (d) elemental mapping images of PNC after 70 h of HER stability test at 1000 mA cm−2. Insets (a) and (b) show high-magnification SEM image and size distribution of Pt nanoparticles, respectively. Figure S12: (a) XRD pattern of PNC after HER stability test for 70 h at 1000 mA cm−2. High-resolution XPS spectra of (b) Pt 4f, (c) Ni 2p3/2, and (d) O 1s of PNC after stability test. Figure S13: polarization curves of RuO2 before and after 1000 OER cycles. Figure S14: (a) SEM, (b) TEM, (c) HRTEM, and (d) elemental mapping images of PNC after 70 h of OER stability test at 1000 mA cm−2. Insets (a) and (b) show high-magnification SEM image and size distribution of Pt nanoparticles, respectively. Figure S15: (a) XRD patterns of PNC after OER stability test. High-resolution XPS spectra of (b) Pt 4f, (c) Ni 2p3/2, and (d) O 1s regions of PNC after stability test. Figure S16: generated and theoretical volumes of H2 and O2 over time at a constant current density of 1000 mA cm−2 in PNC || PNC electrolyzer. Figure S17: digital photographs of the PNC || PNC electrolyzer powered by a 1.5 V battery. Table S1: Pt contents in PN and PNC with different electrodeposition time in the H2PtCl6 precursor solutions. Table S2: the comparison of HER performances of PNC with other electrocatalysts. Table S3: the comparison of OER performances of PNC with other electrocatalysts. Table S4: comparison of water splitting performance of PNC electrocatalyst with other bifunctional electrocatalysts reported before. Movie S1: the formation and release of bubbles on the PNC electrode surface for HER at different current densities. Movie S2: the formation and release of bubbles on the PNC electrode surface for OER at different current densities. Movie S3: the process of water splitting at different densities and the gas generation and release on electrode surface when the PNC || PNC electrolyzer is powered by a 1.5 V battery. Movie S4: the movie of DFT calculated the water dissociation process on the PNC interface. (Supplementary Materials)


  1. R. F. Service, “The hydrogen backlash,” Science, vol. 305, no. 5686, pp. 958–961, 2004. View at: Publisher Site | Google Scholar
  2. K. S. Joya, Y. F. Joya, K. Ocakoglu, and R. van de Krol, “Water-splitting catalysis and solar fuel devices: artificial leaves on the move,” Angewandte Chemie International Edition, vol. 52, no. 40, pp. 10426–10437, 2013. View at: Publisher Site | Google Scholar
  3. C. C. L. McCrory, S. Jung, I. M. Ferrer, S. M. Chatman, J. C. Peters, and T. F. Jaramillo, “Benchmarking hydrogen evolving reaction and oxygen evolving reaction electrocatalysts for solar water splitting devices,” Journal of the American Chemical Society, vol. 137, no. 13, pp. 4347–4357, 2015. View at: Publisher Site | Google Scholar
  4. L. Wu, L. Yu, X. Xiao et al., “Recent advances in self-supported layered double hydroxides for oxygen evolution reaction,” Research, vol. 2020, article 3976278, 17 pages, 2020. View at: Publisher Site | Google Scholar
  5. N. Jiang, B. You, M. Sheng, and Y. Sun, “Electrodeposited cobalt-phosphorous-derived films as competent bifunctional catalysts for overall water splitting,” Angewandte Chemie International Edition, vol. 54, no. 21, pp. 6251–6254, 2015. View at: Publisher Site | Google Scholar
  6. Q. Gao, R. Wu, Y. Liu et al., “Synthesis of PdSx-mediated polydymite heteronanorods and their long-range activation for enhanced water electroreduction,” Research, vol. 2019, article 8078549, 11 pages, 2019. View at: Publisher Site | Google Scholar
  7. H. Sun, X. Xu, Z. Yan et al., “Porous multishelled Ni2P hollow microspheres as an active electrocatalyst for hydrogen and oxygen evolution,” Chemistry of Materials, vol. 29, no. 19, pp. 8539–8547, 2017. View at: Publisher Site | Google Scholar
  8. Y. Lee, J. Suntivich, K. J. May, E. E. Perry, and Y. Shao-Horn, “Synthesis and activities of rutile IrO2 and RuO2 nanoparticles for oxygen evolution in acid and alkaline solutions,” Journal of Physical Chemistry Letters, vol. 3, no. 3, pp. 399–404, 2012. View at: Publisher Site | Google Scholar
  9. X. Zhao, J. Meng, Z. Yan, F. Cheng, and J. Chen, “Nanostructured NiMoO4 as active electrocatalyst for oxygen evolution,” Chinese Chemical Letters, vol. 30, no. 2, pp. 319–323, 2019. View at: Publisher Site | Google Scholar
  10. H. Zhu, J. Zhang, R. Yanzhang et al., “When cubic cobalt sulfide meets layered molybdenum disulfide: a core–shell system toward synergetic electrocatalytic water splitting,” Advanced Materials, vol. 27, no. 32, pp. 4752–4759, 2015. View at: Publisher Site | Google Scholar
  11. H. Shi, Y. T. Zhou, R. Q. Yao et al., “Intermetallic Cu5Zr clusters anchored on hierarchical nanoporous copper as efficient catalysts for hydrogen evolution reaction,” Research, vol. 2020, article 2987234, 12 pages, 2020. View at: Publisher Site | Google Scholar
  12. H. Sun, X. Xu, Z. Yan et al., “Superhydrophilic amorphous Co–B–P nanosheet electrocatalysts with Pt-like activity and durability for the hydrogen evolution reaction,” Journal of Materials Chemistry A, vol. 6, no. 44, pp. 22062–22069, 2018. View at: Publisher Site | Google Scholar
  13. R. Subbaraman, D. Tripkovic, K. C. Chang et al., “Trends in activity for the water electrolyser reactions on 3d M(Ni,Co,Fe,Mn) hydr(oxy)oxide catalysts,” Nature Materials, vol. 11, no. 6, pp. 550–557, 2012. View at: Publisher Site | Google Scholar
  14. X. Zheng, B. Zhang, P. de Luna et al., “Theory-driven design of high-valence metal sites for water oxidation confirmed using in situ soft X-ray absorption,” Nature Chemistry, vol. 10, no. 2, pp. 149–154, 2018. View at: Publisher Site | Google Scholar
  15. F. Dionigi and P. Strasser, “NiFe-based (oxy)hydroxide catalysts for oxygen evolution reaction in non-acidic electrolytes,” Advanced Energy Materials, vol. 6, no. 23, article 1600621, 2016. View at: Publisher Site | Google Scholar
  16. B. E. Conway and G. Jerkiewicz, “Nature of electrosorbed H and its relation to metal dependence of catalysis in cathodic H2 evolution,” Solid State Ionics, vol. 150, no. 1-2, pp. 93–103, 2002. View at: Publisher Site | Google Scholar
  17. B. Ruqia and S. L. Choi, “Pt and Pt–Ni(OH)2 Electrodes for the hydrogen evolution reaction in alkaline electrolytes and their nanoscaled electrocatalysts,” ChemSusChem, vol. 11, no. 16, pp. 2643–2653, 2018. View at: Publisher Site | Google Scholar
  18. D. Strmcnik, P. P. Lopes, B. Genorio, V. R. Stamenkovic, and N. M. Markovic, “Design principles for hydrogen evolution reaction catalyst materials,” Nano Energy, vol. 29, pp. 29–36, 2016. View at: Publisher Site | Google Scholar
  19. G. Wang, J. Parrondo, C. He, Y. Li, and V. Ramani, “Pt/C/Ni(OH)2 Bi-Functional electrocatalyst for enhanced hydrogen evolution reaction activity under alkaline conditions,” Journal of the Electrochemical Society, vol. 164, no. 13, pp. F1307–F1315, 2017. View at: Publisher Site | Google Scholar
  20. L. Wang, Y. Zhu, Z. Zeng et al., “Platinum−nickel hydroxide nanocomposites for electrocatalytic reduction of water,” Nano Energy, vol. 31, pp. 456–461, 2017. View at: Publisher Site | Google Scholar
  21. H. Yin, S. Zhao, K. Zhao et al., “Ultrathin platinum nanowires grown on single-layered nickel hydroxide with high hydrogen evolution activity,” Nature Communications, vol. 6, no. 1, article 6430, 2015. View at: Publisher Site | Google Scholar
  22. R. Subbaraman, D. Tripkovic, D. Strmcnik et al., “Enhancing hydrogen evolution activity in water splitting by tailoring Li+−Ni(OH)2−Pt interfaces,” Science, vol. 334, no. 6060, pp. 1256–1260, 2011. View at: Publisher Site | Google Scholar
  23. Y. Wang, L. Chen, X. Yu, Y. Wang, and G. Zheng, “Superb alkaline hydrogen evolution and simultaneous electricity generation by Pt-decorated Ni3N nanosheets,” Advanced Energy Materials, vol. 7, no. 2, article 1601390, 2017. View at: Publisher Site | Google Scholar
  24. C. Chen, Y. Kang, Z. Huo et al., “Highly crystalline multimetallic nanoframes with three-dimensional electrocatalytic surfaces,” Science, vol. 343, no. 6177, pp. 1339–1343, 2014. View at: Publisher Site | Google Scholar
  25. Y. Zhu, W. Zhou, Y. Zhong et al., “A perovskite nanorod as bifunctional electrocatalyst for overall water splitting,” Advanced Energy Materials, vol. 7, no. 8, article 1602122, 2017. View at: Publisher Site | Google Scholar
  26. Z. Yan, H. Sun, X. Chen et al., “Anion insertion enhanced electrodeposition of robust metal hydroxide/oxide electrodes for oxygen evolution,” Nature Communications, vol. 9, no. 1, article 2373, 2018. View at: Publisher Site | Google Scholar
  27. G. Fan, H. Sun, F. Cheng, and J. Chen, “Progress in DFT study on 3d transition metal oxide/hydroxide electrocatalyst for oxygen evolution,” Scientia Sinica Chimica, vol. 49, no. 5, pp. 741–751, 2019. View at: Publisher Site | Google Scholar
  28. A. Bruix, J. A. Rodriguez, P. J. Ramírez et al., “A new type of strong metal-support interaction and the production of H2 through the transformation of water on Pt/CeO2(111) and Pt/CeOx/TiO2(110) catalysts,” Journal of the American Chemical Society, vol. 134, no. 21, pp. 8968–8974, 2012. View at: Publisher Site | Google Scholar
  29. J. Park, H. Wang, M. Vara, and Y. Xia, “Platinum cubic nanoframes with enhanced catalytic activity and durability toward oxygen reduction,” ChemSusChem, vol. 9, no. 19, pp. 2855–2861, 2016. View at: Publisher Site | Google Scholar
  30. E. Jung, H. Y. Park, A. Cho, J. H. Jang, H. S. Park, and T. Yu, “Aqueous-phase synthesis of metal hydroxide nanoplates and platinum/nickel hydroxide hybrid nanostructures and their enhanced electrocatalytic properties,” Applied Catalysis B: Environmental, vol. 225, pp. 238–242, 2018. View at: Publisher Site | Google Scholar
  31. R. Kavian, S. I. Choi, J. Park et al., “Pt−Ni octahedral nanocrystals as a class of highly active electrocatalysts toward the hydrogen evolution reaction in an alkaline electrolyte,” Journal of Materials Chemistry A, vol. 4, no. 32, pp. 12392–12397, 2016. View at: Publisher Site | Google Scholar
  32. Y. Liu, C. M. Hangarter, D. Garcia, and T. P. Moffat, “Self-terminating electrodeposition of ultrathin Pt films on Ni: an active, low-cost electrode for H2 production,” Surface Science, vol. 631, pp. 141–154, 2015. View at: Publisher Site | Google Scholar
  33. Y. Zhou, J. M. Perket, and J. Zhou, “Growth of Pt nanoparticles on reducible CeO2(111) thin films: effect of nanostructures and redox properties of ceria,” Journal of Physical Chemistry C, vol. 114, no. 27, pp. 11853–11860, 2010. View at: Publisher Site | Google Scholar
  34. H. Feng, Z. Xu, L. Ren et al., “Activating titania for efficient electrocatalysis by vacancy engineering,” ACS Catalysis, vol. 8, no. 5, pp. 4288–4293, 2018. View at: Publisher Site | Google Scholar
  35. X. Zheng, P. Cui, Y. Qian et al., “Multifunctional active-center-transferable platinum/lithium cobalt oxide heterostructured electrocatalysts towards superior water splitting,” Angewandte Chemie International Edition, vol. 59, no. 34, pp. 14533–14540, 2020. View at: Publisher Site | Google Scholar
  36. M. Lao, K. Rui, G. Zhao et al., “Platinum/nickel bicarbonate heterostructures towards accelerated hydrogen evolution under alkaline conditions,” Angewandte Chemie International Edition, vol. 58, no. 16, pp. 5432–5437, 2019. View at: Publisher Site | Google Scholar
  37. X. Cheng, Y. Li, L. Zheng et al., “Highly active, stable oxidized platinum clusters as electrocatalysts for the hydrogen evolution reaction,” Energy & Environmental Science, vol. 10, no. 11, pp. 2450–2458, 2017. View at: Publisher Site | Google Scholar
  38. V. R. Stamenkovic, B. S. Mun, M. Arenz et al., “Trends in electrocatalysis on extended and nanoscale Pt-bimetallic alloy surfaces,” Nature Materials, vol. 6, no. 3, pp. 241–247, 2007. View at: Publisher Site | Google Scholar
  39. J. Ji, L. L. Zhang, H. Ji et al., “Nanoporous Ni(OH)2 thin film on 3D ultrathin-graphite foam for asymmetric supercapacitor,” ACS Nano, vol. 7, no. 7, pp. 6237–6243, 2013. View at: Publisher Site | Google Scholar
  40. A. N. Mansour and C. A. Melendres, “Characterization of α-Ni(OH)2 by XPS,” Surface Science Spectra, vol. 3, no. 3, pp. 255–262, 1994. View at: Publisher Site | Google Scholar
  41. T. Tang, W. J. Jiang, S. Niu et al., “Electronic and morphological dual modulation of cobalt carbonate hydroxides by Mn doping toward highly efficient and stable bifunctional electrocatalysts for overall water splitting,” Journal of the American Chemical Society, vol. 139, no. 24, pp. 8320–8328, 2017. View at: Publisher Site | Google Scholar
  42. Y. Liu, Q. Li, R. Si et al., “Coupling sub-nanometric copper clusters with quasi-amorphous cobalt sulfide yields efficient and robust electrocatalysts for water splitting reaction,” Advanced Materials, vol. 29, no. 13, article 1606200, 2017. View at: Publisher Site | Google Scholar
  43. X. Ma, W. Zhang, Y. Deng, C. Zhong, W. Hu, and X. Han, “Phase and composition controlled synthesis of cobalt sulfide hollow nanospheres for electrocatalytic water splitting,” Nanoscale, vol. 10, no. 10, pp. 4816–4824, 2018. View at: Publisher Site | Google Scholar
  44. J. O.'. M. Bockris, “The origin of ideas on a hydrogen economy and its solution to the decay of the environment,” International Journal of Hydrogen Energy, vol. 27, no. 7-8, pp. 731–740, 2002. View at: Publisher Site | Google Scholar
  45. J. Durst, A. Siebel, C. Simon, F. Hasché, J. Herranz, and H. A. Gasteiger, “New insights into the electrochemical hydrogen oxidation and evolution reaction mechanism,” Energy and Environmental Science, vol. 7, no. 7, pp. 2255–2260, 2014. View at: Publisher Site | Google Scholar
  46. X. Long, G. Li, Z. Wang et al., “Metallic iron−nickel sulfide ultrathin nanosheets as a highly active electrocatalyst for hydrogen evolution reaction in acidic media,” Journal of the American Chemical Society, vol. 137, no. 37, pp. 11900–11903, 2015. View at: Publisher Site | Google Scholar
  47. X. Zou and Y. Zhang, “Noble metal-free hydrogen evolution catalysts for water splitting,” Chemical Society Reviews, vol. 44, no. 15, pp. 5148–5180, 2015. View at: Publisher Site | Google Scholar
  48. S. Lee, K. Banjac, M. Lingenfelder, and X. Hu, “Oxygen isotope labeling experiments reveal different reaction sites for the oxygen evolution reaction on nickel and nickel iron oxides,” Angewandte Chemie International Edition, vol. 58, no. 30, pp. 10295–10299, 2019. View at: Publisher Site | Google Scholar
  49. P. A. Thiel and T. E. Madey, “The interaction of water with solid surfaces: fundamental aspects,” Surface Science Reports, vol. 46, no. 1-8, pp. 1–308, 2002. View at: Google Scholar
  50. S. Niu, W. J. Jiang, T. Tang, L. P. Yuan, H. Luo, and J. S. Hu, “Autogenous growth of hierarchical NiFe(OH)x/FeS nanosheet-on-microsheet arrays for synergistically enhanced high-output water oxidation,” Advanced Functional Materials, vol. 29, no. 36, p. 1902180, 2019. View at: Publisher Site | Google Scholar
  51. X. Lu and C. Zhao, “Electrodeposition of hierarchically structured three-dimensional nickel−iron electrodes for efficient oxygen evolution at high current densities,” Nature Communications, vol. 6, no. 1, article 6616, 2015. View at: Publisher Site | Google Scholar
  52. L. Zhang, Z. Yan, X. Chen et al., “Facile synthesis of amorphous MoSx-Fe anchored on Zr-MOFs towards efficient and stable electrocatalytic hydrogen evolution,” Chemical Communications, vol. 56, no. 18, pp. 2763–2766, 2020. View at: Publisher Site | Google Scholar
  53. J. Hutter, M. Iannuzzi, F. Schiffmann, and J. VandeVondele, “Cp2k: atomistic simulations of condensed matter systems,” Wiley Interdisciplinary Reviews: Computational Molecular Science, vol. 4, no. 1, pp. 15–25, 2014. View at: Publisher Site | Google Scholar
  54. J. P. Perdew, K. Burke, and M. Ernzerhof, “Generalized gradient approximation made simple,” Physical Review Letters, vol. 77, no. 18, pp. 3865–3868, 1996. View at: Publisher Site | Google Scholar
  55. S. Grimme, “Semiempirical gga-type density functional constructed with a long-range dispersion correction,” Journal of Computational Chemistry, vol. 27, no. 15, pp. 1787–1799, 2006. View at: Publisher Site | Google Scholar
  56. J. VandeVondele and J. Hutter, “Gaussian basis sets for accurate calculations on molecular systems in gas and condensed phases,” The Journal of Chemical Physics, vol. 127, no. 11, article 114105, 2007. View at: Publisher Site | Google Scholar
  57. J. VandeVondele, M. Krack, F. Mohamed, M. Parrinello, T. Chassaing, and J. Hutter, “Quickstep: fast and accurate density functional calculations using a mixed gaussian and plane waves approach,” Computer Physics Communications, vol. 167, no. 2, pp. 103–128, 2005. View at: Publisher Site | Google Scholar
  58. S. Goedecker, M. Teter, and J. Hutter, “Separable dual-space Gaussian pseudopotentials,” Physical Review B, vol. 54, no. 3, pp. 1703–1710, 1996. View at: Publisher Site | Google Scholar
  59. C. Hartwigsen, S. Goedecker, and J. Hutter, “Relativistic separable dual-space Gaussian pseudopotentials from H to Rn,” Physical Review B, vol. 58, no. 7, pp. 3641–3662, 1998. View at: Publisher Site | Google Scholar

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