HIGHLIGHTS
• Heterostructure constructed via confining crystalline ruthenium nanodomains by hafnium dioxide matrix was fabricated through a two-step annealing method for overall water splitting.
• The synergistic effect of hafnium dioxide modification and small crystalline domain formation significantly alleviates the over-oxidation of ruthenium.
1 Introduction
H2 production through electrochemical water splitting is considered as a promising and convenient approach to store intermittent renewable energy, with high combustion enthalpy and minimal CO2 footprint [1,2,3,4,5,6]. The past decades have witnessed growing research efforts on developing efficient electrocatalysts for its two half reactions, involving the anodic oxygen evolution reaction (OER) and cathodic hydrogen evolution reaction (HER) [7,8,9,10,11]. However, the reported OER catalysts normally work effectively in alkaline environments, while acidic conditions are more suitable for HER operation [12,13,14]. Such a pH mismatch for these two branch reactions severely hinders the electrolyzer to achieve industrial H2 production [15,16]. Henceforth, the design and preparation of bi-functional electrocatalysts for overall water splitting under acidic condition are highly desired [17], but have been recognized as a long standing challenge.
Transition metal phosphides, hydroxides, phosphates and selenides have recently been demonstrated to be promising alkaline OER electrocatalysts, while their HER and acidic OER properties have remained largely unexplored [18,19,20,21]. Among these candidates, Ru-based nanomaterials demonstrate substantial potential for both OER and HER. On the one side, RuO2 is deemed as an ideal alternative to expedite the kinetics of oxygen production, which is commonly used as a benchmark to evaluate the performance of OER catalysts [22,23,24]. On the other side, Ru metal possesses a comparable affinity to hydrogen (≈65 kcal mol-1) as Pt (≈62 kcal mol-1), affording promising performance toward hydrogen generation [25,26,27]. Since Ru is much cheaper as compared with other precious metals, the development of bi-functional Ru-based catalysts for overall water splitting is expected to reduce the production cost and simultaneously simplify the practical operation process. Despite the good hydrogen production capability of metallic Ru, the over-oxidation of Ru during OER can create highly soluble Run+ species (n > 4), leading to quick degradation and significant loss in oxygen generation activity [28,29,30,31,32]. Accordingly, various strategies of elements decoration have been developed to improve the durability of Ru-based materials for OER. For example, elements including Mn [33], Cu [34], Ni [35], Pt [36] have been shown to modify the chemical environment of RuO2 via donating electrons into the RuO2 matrix, alleviating its undesired dissolution via over-oxidation. Thus, stabilizing low-valent Ru-based catalysts is necessary for achieving good stability during electro-oxidation operation. Unfortunately, the more stable low-valent RuO2-x species generally deliver a slower kinetics during OER than high-valent Ru species [31,37,38]. Additionally, this electron-injection approach cannot simultaneously meet both hydrogen and oxygen production. Hence, a new strategy is required to address this dilemma and enable high-performance overall water splitting.
Recently, Kim and coworkers demonstrated that metallic Ru possesses a better activity for OER when compared with its oxides [39]. However, it is unstable under high applied potentials during OER operation, leading to gradual dissolution via oxidation into a higher Run+ (n>4) state. Therefore, the construction of robust Ru nanocrystals holds great potentials to simultaneously achieve sustained oxygen production as well as ideal hydrogen generation. In this work, we hope to address this issue by incorporation of a guest material with strong oxidation resistance to prevent the metallic Ru from over-oxidation. Hf possesses an electron structure of 5d26s2, enabling the highest valence state of Hf in its dioxide compound. HfO2 has attracted considerable interest in thermal catalysis due to its high resistance to corrosion and oxidation [40,41]. It mostly takes a supporting role because of the moderately lower bandgap when compared with traditional substrates such as SiO2 or Al2O3 [42]. Recent studies reveal that the synergistic effect of Ru and Hf can improve the hydrogen evolution [25,43]. Herein, Ru nanocrystals with small crystalline domains were created and HfO2 was introduced to protect Ru against over-oxidation. The electrochemical measurements suggested the as-obtained catalyst required a low overpotential of 197 mV to reach 10 mA cm-2 for acidic OER, accompanied by a stable behavior over 250 h operation. Meanwhile, the HER performance was also enhanced, which enabled a stable and efficient electrocatalyst for acidic overall water splitting.
2 Experimental Section
2.1 Materials
Ruthenium acetylacetonate (97%), hafnium(IV) acetylacetonate (97%) and potassium bromide (99%) were purchased from Shanghai Macklin Biochemical Co., Ltd. All chemicals were used as received without further purification. Deionized water was used in all the experiments.
2.2 Synthesis
S-Ru-HfO2 was prepared by a facile solid-phase reaction method. In a typical synthesis, 40 mg of ruthenium acetylacetonate, 20 mg of hafnium acetylacetonate, and 120 mg of potassium bromide were mixed in a solution composed of 10 mL of deionized water and 20 mL of absolute ethanol under vigorous sonication and stirring. After drying overnight in an oven at 60 °C, the obtained powder mixture was transferred into a tube furnace. The reactor was calcined at 290 °C with a heating rate of 5 °C min-1 and then, maintained at that temperature for 2 h under air condition. When the reaction was completed, this system was naturally cooled to the room temperature. Afterward, the product was washed several times with alcohol and water to remove the introduced KBr and then, freeze-dried. The obtained catalyst was denoted as S-Ru/HfO2, with “S” representing the short time calcination. After that, the sample was further annealed in nitrogen atmosphere at 290 °C for another 10 h, and the final product was labeled as L-Ru/HfO2, meaning a long-time annealing processing.
An amount of S-Ru-HfO2 was further annealed at 800 °C in N2 for 10 h, with the same heating rate of 5 °C min-1, and the obtained sample was referred as H-Ru/HfO2. For comparison, we also prepared the corresponding pure Ru sample in the same way as above except without hafnium acetylacetonate, and the achieved samples were labeled as S-Ru and L-Ru, respectively.
2.3 Characterizations
Powder X-ray diffraction (XRD) was carried out on Panalytical Empyrean with Cu Kα radiation for the crystalline phase analysis. The structures of the prepared samples were characterized by transmission electron microscopy (TEM) images (JEOL JEM-2100F) and scanning electron microscopy (SEM) images (HITACHI REGULUS-8220). X-ray photoelectron spectroscopy (Kratos Axis Supra+) was adopted to perform elemental analysis and determine the composition of the materials. The Raman spectra were recorded by the confocal laser microscopic Raman spectrometer (viaReflex). Fourier transform infrared (FTIR) spectra were recorded using a Nicolet iS50 Spectrophotometer (Thermo-Scientific). The X-ray absorption fine structure spectra (XAFS) were collected with Si(111) crystal monochromators at BL11B beamlines in the Shanghai Synchrotron Radiation Facility (SSRF) (Shanghai, China). In situ Raman spectroscopy was recorded on the XPLORA PLUS Raman spectrometer. The electrochemical cells used for Raman measurements are homemade from Teflon, with a quartz plate serving as a window through the laser. The synthesized sample was used as the working electrode and the opposite electrode, and the Ag/AgCl electrode (1.0 M KCl as the filled electrolyte) was used as the reference electrode. In order to apply a control potential to the catalyst during Raman measurements, chronoamperometry was performed at different potentials of 0-1.6 V in 0.5 M H2SO4. The inductively coupled plasma (ICP) measurement was conducted on iCAP7400(Thermo Fisher). The thickness information was characterized on an atomic force microscope (AFM; Multimode 8, Bruker) with tapping mode. Brunauer-Emmett-Teller (BET) measurement was carried out on ASAP 2460 Version 3.01.
2.4 Electrochemical Measurements
All of the electrochemical measurements were performed on the electrochemical workstation (CHI 760e, CH Instruments, Inc.), the Ag/AgCl electrode electrode was used as the reference electrode, the graphite rod was used as the counter electrode, and the as-synthesized samples were used as the working electrode to study the electrocatalytic performance. 5 mg of catalyst and 20 μL of Nafion solution (Aldrich, 5 wt%) were dispersed in 2.5 mL of water-isopropanol solution at a volume ratio of 3:2 and sonicated for 20 min to form a homogeneous ink. Load 5 μL of catalyst ink (containing 10 μg of catalyst) on a polished glassy carbon electrode with a diameter of 3 mm. A 0.5 M H2SO4 aqueous solution was selected as the electrolyte and purged with pure O2 and H2 for OER and HER measurement, respectively. The linear sweep potential with a sweep rate of 5 mV s−1 was calibrated as a reversible hydrogen electrode (RHE). The Nyquist plot is done in the range of 100 kHz to 0.05 Hz, with an amplitude of 5 mV and an overpotential of 50 mV. In addition, 1.0 M PBS solution and 1.0 M KOH were used to evaluate their performance in the neutral and alkaline electrolytes. The value of turnover frequency (TOF) is calculated by assuming that every metal atom is involved in catalysis (the TOF lower limit): TOF = J/(4×F×n), where J is at 50 mV, and the number 4 represents per mole O2 has 4 electrons, F is the Faraday constant (96,485.3 C mol-1), and n is the number of moles of metal atoms evaluated by ICP measurement.
2.5 Density Functional Theory Calculations
The density functional theory (DFT) calculation was performed on the VASP 5.3 software. The PBE-type GGA functional was used to treat the exchange-correlation energy, and the projector augmented wave (PAW) technique was used for the ion-electron interaction. During the geometric optimization, both lattice constants and atomic positions were relaxed. The convergence criterion was set as forces on each atom less than 0.02 eV Å-1 and total energy change smaller than 1.0 × 10-5 eV. The DFT-D3 method was employed for the Van der Waals force correction. The adsorption energy was calculated as the difference between the energies for the adsorbed structure and their free or isolated models.
3 Results and Discussion
3.1 Synthesis and Characterizations of Ru/HfO2 Electrocatalysts
The sample fabrication was conducted via a solid-state method as modified from literature, which has also been used in our recent studies to develop high-performance catalysts [44,45,46]. As illustrated in Fig. 1A, a certain amount of Ru(acac)3 and Hf(acac)4 was mixed with KBr for annealing, to achieve the hybrid of Ru and Hf in the composite, referred as S-Ru/HfO2. In this system, KBr regulated the diffusion of metal atoms, leading to a sheet-like structure with low aggregation [47]. The slow diffusion rates of Ru and Hf on KBr surface could impair their combination, resulting in a weak interaction between themselves associated with a poor stability [45,47]. Hence, we envisioned that an additional annealing after KBr removing may strengthen the interaction between these two components, which could not only regulate the chemical environment and structure of active sties, but also provide an improved durability via strengthening the binding within the sample system [44]. Subsequently, the KBr template was removed via carefully washing, followed by an additional annealing to promote the crystallinity, affording sample denoted as L-Ru/HfO2.
Fig. 1 A Schematic illustration for the synthesis of L-Ru/HfO2 catalyst. Characterization of S-Ru/HfO2: B TEM and C HRTEM images, D SAED pattern. Characterization of L-Ru/HfO2: E TEM and F HRTEM images, G SAED pattern. HAADF-STEM images and corresponding EDX elemental mapping for H S-Ru/HfO2 and i S-Ru/HfO2 |
Figures S1 and 1B displayed the typical SEM and TEM images of S-Ru/HfO2, where a clear two-dimensional feature without any particle nor fragment was discerned over the whole images, revealing the well flat configuration control during sample growth using this molten salt method. The microstructure was further studied by high-resolution TEM (HRTEM) in Fig. 1C. Clearly, S-Ru/HfO2 exhibited a fuzzy pattern without any ordered atomic arrangement in the recorded image. In addition, diffused rings were observed in the selected area electron diffraction (SAED) pattern (Fig. 1D). These results indicated the amorphous structure of S-Ru/HfO2, which should be generated by the slow diffusion of Ru and Hf atoms on KBr template as observed in our previous studies [44,45]. Although materials in amorphous phase normally exhibited high kinetics for catalysis [48], a rapid loss in activity was obtained owing to the existence of rich unsaturated atoms, lattice distortions as well as vacancies. This feature led to a low stability and thus severely hindered its practical application. In order to enhance the contact between Ru and Hf species, a subsequent thermal annealing was performed accordingly. Both SEM (Fig. S2) and TEM (Fig. 1E) images demonstrated that the sheet-like morphology was well maintained. The AFM image indicated a height profile of approximately 4.8 nm in thickness (Fig. S3). Of note, roughing occurred on the surface of L-Ru/HfO2. Brunauer-Emmett-Teller (BET) measurement indicated an increased surface area from 46.61 to 56.00 m2 g-1 for S-Ru/HfO2 and L-Ru/HfO2, respectively, and both of them were assigned to type IV isotherms [49] (Fig. S4). Apparently, crystallographic fringes appeared in the recorded HRTEM image (Fig. 1F). The lattice spacing of 0.325 and 0.236 nm was assigned to orthogonal HfO2 (002) (PDF#40-1173) and hexagonal Ru (100) (PDF#89-3942) crystallographic planes, respectively. Clear interface was discerned between Ru and HfO2, which suggested the intimate contact formed at their interface region. Meanwhile, the diffractive rings appeared in Fig. 1G confirmed the improved crystallinity of Ru and HfO2 in L-Ru/HfO2. All of these comparisons illustrated the effective modification on microstructure of the hetero-interface by post-annealing.
An intimate interfacial interaction could ensure improved structure stability for both Ru and HfO2, which held great potential to achieve high durability during operation. As depicted in the left of Fig. 2A, the disordered arrangement in amorphous materials would result in weak interactions between the atoms of both same type and different species, thereby leading to a weak Ru-HfO2 contact. Controlled annealing was able to increase the crystallinity of both Ru and HfO2, offering an ordered atomic arrangement and enhancing their interfacial interaction. However, this interface effect was closely related to the size of crystalline domains. For a large-sized Ru crystal, the interior Ru atoms almost remained as before, only edged Ru atoms around the interface were affected (middle in Fig. 2A). In contrast, when the crystalline Ru domain significantly decreased, most Ru atoms could be protected by their surrounding HfO2 layer, enabling a higher resistance toward oxidation and corrosion (right panel in Fig. 2A). Henceforth, constructing heterostructure with small crystalline regions would benefit the interaction between Ru and HfO2. HRTEM characterizations demonstrated that all of the generated Ru and HfO2 crystalline domains were less than 5 nm (Fig. 2B). This was consistent with the XRD observation as no diffractive peaks existing on the recorded pattern of L-Ru/HfO2 (Fig. S5). Furthermore, high-angle annular dark-field scanning TEM (HAADF-STEM) image and the corresponding energy-dispersive X-ray spectroscopy (STEM-EDS) elemental mapping were performed (Fig. 1H, I). Obviously, S-Ru/HfO2 displayed a discrete distribution for Ru and Hf over the sheet-like catalyst, while their distribution became quite uniform for L-Ru/HfO2. This further suggested the post-annealing drove the diffusion of atoms to make a more intimate interaction between these two components.
Fig. 2 A Schematic illustration of the interaction between Ru and HfO2. B HRTEM images for L-Ru/HfO2. Physical characterizations on these samples: C Raman spectra, D High resolution XPS spectra of Ru 3p orbital, E XANES spectra, F Ru K-edge EXAFS spectra, and WT-EXAFS spectra for G L-Ru/HfO2 and H S-Ru/HfO2 |
Raman spectra were subsequently performed to give more insights on the interface structure between Ru and HfO2 (Fig. 2C). There are three peaks located at 491.7, 621.8, and 681.5 cm-1 on pure Ru nanosheets (both of L-Ru and S-Ru), which corresponded to Eg, A1g, and B2g vibration modes of Ru-O bond, respectively [50]. The intensity of these peaks became much stronger for L-Ru than those of S-Ru, indicating the high sensitivity of bare Ru to oxygen, which may result from the partial oxidation of Ru when exposed to air [51]. Interestingly, these vibration peaks almost disappeared on S-Ru/HfO2 and L-Ru/HfO2, suggesting the HfO2 incorporation could effectively prevent Ru metal from oxidation. After that, X-ray diffraction photoelectron spectroscopy (XPS) was conducted to detect their surface chemical state and elemental composition. The recorded survey spectrum of L-Ru/HfO2 showed the presence of Ru, Hf, C, and O elements in the catalyst (Fig. S6). The peaks at 484.4 and 462.3 eV in the high-resolution XPS profile corresponded to Ru 3p1/2 and Ru 3p3/2, respectively (Fig. 2D). The prominent Ru 3p3/2 peak exhibited a positive shift of 0.3 eV for L-Ru as compared with that of L-Ru/HfO2. Furthermore, it was deconvolved to Ru0 (462.1 eV) and Ruδ+ (465.4 eV) [44]. The ratio of Ru0/Ruδ+ for S-Ru was 1.97, which significantly decreased to 0.91 after the post-annealing (L-Ru). In contrast, this ratio showed a slight change from S-Ru/HfO2 (2.09) to L-Ru/HfO2 (2.15). Additionally, the amount of Ru0 in the heterostructure catalyst was much greater than that of pure Ru without HfO2 protection. The comparison of O 1s spectra also suggested more Ru0 content in L-Ru/HfO2, with a smaller portion of lattice O as compared with L-Ru in Fig. S7. These results validated the HfO2 moderation endowed Ru metal with a higher resistance toward oxidation, which held the potential to provide improved stability for Ru in OER operation as well as a high HER response to realize overall water splitting. In the meantime, Fig. S8 addressed the positive shift of Hf 4f signal for L-Ru/HfO2 than L-Hf, unveiling electrons transferring from HfO2 to Ru. This benefited to maintain Ru site in the metallic state during oxidation.
Afterward, X-ray absorption spectroscopy (XAS) was conducted to investigate the electronic configuration and local chemical environment of L-Ru/HfO2. As shown in Fig. 2E, X-ray absorption near-edge structure (XANES) analysis demonstrated that the Ru K-edge of S-Ru/HfO2 suited between commercial Ru foil and RuO2, which suggested the metaphase of Ru with partial positively charged state between Ru0 and Ru4+ [50]. Notably, L-Ru/HfO2 exhibited a much more negative absorption edge than S-Ru/HfO2, which almost coincided with that of Ru foil. Beyond, the white line intensity of Ru foil was smaller than S-Ru/HfO2 but larger than L-Ru/HfO2, revealing the majority of Ru atoms in L-Ru/HfO2 possessed Ru0 state with negligible oxidation. Furthermore, the peak of S-Ru/HfO2 in the pre-edge region disappeared on L-Ru/HfO2, which indicated the strengthened interaction between Ru and HfO2, with more empty orbitals of Ru being filled by the electron injection during the post-annealing procedure. The two scattering peaks observed at ~2.4 and 1.7 Å in EXAFS were indexed to Ru-Ru and Ru-O-Hf coordination, respectively (Fig. 2F and Table S1). Apparently, the Ru-Ru peak of L-Ru/HfO2 was significantly stronger than Ru-O, verifying the majority of metallic Ru state in the crystalline heterostructure. In contrast, S-Ru/HfO2 exhibited a relatively high intensity for Ru-O peak but the intensity of Ru-Ru bonding was much lower as compared. The enlarged view in Fig. 2F unraveled the Ru-O-Hf peak of L-Ru/HfO2 shifted to a smaller distance when compared to that of S-Ru/HfO2, presumably originating from the stronger interaction imposed between Ru and HfO2. The Ru-Ru coordination numbers increased from 4.7 to 6.6 as S-Ru/HfO2 transformed to L-Ru/HfO2 (Table S1), further confirming the higher crystallinity induced more Ru atoms to be coordinated and protected by HfO2. On basis of these discussions, it was concluded that the Ru sites were more effectively protected by the HfO2 matrix in L-Ru/HfO2 and thereby generated a higher oxidation resistance for the higher crystalline catalyst during operation. Besides, the wavelet transforms of Ru-edge EXAFS oscillations demonstrated the maximum-intensity values of L-Ru/HfO2 were located at k ≈ 4.9 and 9.1 Å−1, which were assigned to Ru-O-Hf and Ru-Ru scattering paths, respectively (Fig. 2G). It also reflected that L-Ru/HfO2 possessed more metallic Ru states and fewer Ru-O bonds than S-Ru/HfO2 (Fig. 2G, H), exhibiting a metallic feature that quite close to Ru foil. Since ICP measurements disclosed a similar atomic ratio of Ru to Hf for S-Ru/HfO2 (0.88) and L-Ru/HfO2 (0.80), we attributed the more stable Ru0 state of L-Ru/HfO2 to the enhanced interfacial interaction constructed by increasing the crystallinity of Ru and HfO2.
As a control, S-Ru/HfO2 was annealed at 800 °C to increase the crystalline domain size for comparison, and the obtained sample was denoted as H-Ru/HfO2. Obviously, strong diffraction peaks were found in the recorded XRD pattern, which were well assigned to hexagonal Ru and HfO2 as marked in Fig. S9. These intensified diffraction peaks reflected the further growth of crystalline domains in the sample. The main Ru peak became rather sharper and stronger, implying large-size crystalline Ru domains were formed as expected.
3.2 Electrocatalytic Performances
Electrochemical measurement was subsequently carried out to evaluate the water splitting performance using a three-electrode technique. First, we examined their OER behavior in O2-saturated 0.5 M H2SO4 because of its sluggish kinetics as compared with HER. Figure 3A illustrated both S-Ru/HfO2 and L-Ru/HfO2 displayed a more negative potential than the commercial RuO2 reference, at which the recorded current density increased sharply. Specifically, L-Ru/HfO2 exhibited the smallest onset potential among these catalysts, with their order following: L-Ru/HfO2 (1.38 V) < S-Ru/HfO2 (1.40 V) < RuO2 (1.42 V) < L-Ru (1.43 V) < S-Ru (1.53 V). Meantime, the required overpotential for L-Ru/HfO2 to achieve the benchmark 10 mA cm-2 current density was 197 mV, which was lower than S-Ru/HfO2 (212 mV) and much smaller than those of RuO2 (234 mV), L-Ru (256 mV) and S-Ru (>400 mV). Figure S10 addressed the optimization of Ru metal content, which indicated that 40 mg Ru(acac)3 is the optimal precursor dosage. Moreover, the smallest Tafel slope of L-Ru/HfO2 (46.8 mV dec-1) in Fig. S11 signified the much faster oxygen generation kinetics acquired on the catalyst with small crystalline domains. Accordingly, the electrochemical impedance spectroscopy (EIS) was measured at an overpotential of 200 mV, and the obtained curves confirmed the accelerated oxygen production on L-Ru/HfO2 (Fig. S12). Also, L-Ru/HfO2 and S-Ru/HfO2 overperformed H-Ru/HfO2 for OER operation (Fig. S13). Furthermore, both the double layer capacitance and turnover frequency imposed the advance of L-Ru/HfO2 (Fig. S14). As a result, L-Ru/HfO2 demonstrated excellent OER activity which exceeded most recently reported RuO2-based acidic OER catalysts (Fig. 3J).
Fig. 3 The electrochemical measurements of these samples in the three-electrode system in 0.5 M H2SO4 solution: A LSV curves, B the chronoamperometry measurement with the i-t response at 10 mA cm-2, and the LSV polarization curves recorded before and after were inset in, and C the first cycle of CV scan during OER activation. D The digital photos observed on electrode surface during the first cycle of CV scan for each sample activation. E OER LSV curves for these sampled measured in 1.0 M KOH and 1.0 M PBS. F HER LSV curves for these sampled measured in 0.5 M H2SO4 solution. G Comparison of LSV curves obtained during OER and HER operation in the KSCN involved electrolyte. H The digital image of the assembled PEM electrolyzer. I Polarization curves achieved on these catalysts assembled PEM electrolyzers and durability estimation on L-Ru/HfO2||L-Ru/HfO2 coupled PEM electrolyzer. J Comparison of η10 for acidic OER on L-Ru/HfO2 with recently reported Ru-based catalysts. The detailed information for these compared catalysts can be found in the supporting information file. |
Besides, the catalytic durability of L-Ru/HfO2 was examined using a chronoamperometry approach, through keeping the potential corresponding to the current density of 10 mA cm-2. The recorded i-t profiles were collected in Fig. 3B. Overall, L-Ru/HfO2 exhibited superior stability compared to other samples. Specifically, the initial current density of L-Ru/HfO2 decreased to 7.36 mA cm-2 after 250 h of acidic oxygen production, representing 73% current density was well retained during the long-term operation. Instead, other samples demonstrated rapid decays within 50 h. For instance, S-Ru underwent severe oxidation to form soluble high-valent Ru oxides, so its activity disappeared just within hundreds of seconds. The measured polarization curves demonstrated slight difference between linear sweep voltammetry (LSV) before and after the continuous OER evaluation for L-Ru/HfO2 (inset in Fig. 3B). What’s more, the first cyclic voltammetry (CV) cycle of each sample during catalyst activation was collected for comparison. As shown in Fig. 3C, pure Ru catalysts displayed an apparent oxidized peak around 1.47 V, which was assigned to continuous oxidation of RuO2 through a transition state to Ru(V) or Ru(VI) driven by applied oxidized potentials [52]. When combined with HfO2, this oxidation peak exhibited an obvious positive shift to 1.60 V for S-Ru/HfO2. Furthermore, this peak became rather featureless on L-Ru/HfO2, confirming the strengthened antioxidant effects on Ru endowed by crystalline HfO2 protection. This behavior was in agreement with the image as observed on the electrode surface in Fig. 3D. Clearly, the electrolyte around S-Ru electrode appeared yellow color, which was attributed to the rapid dissolution of over-oxidized Ru-based species. Likely, L-Ru/HfO2 exhibited colorless and transparent as the original electrolyte did, accompanied by large bubbles generated on the electrode surface. Therefore, the HfO2 presence afforded an improved anti-oxidation for L-Ru/HfO2 to keep Ru in metallic state as expected. Besides, the structure characterization indicated L-Ru/HfO2 could maintain the original sheet-like morphology with fine crystalline domains of Ru and HfO2 after subjecting the long-term stability estimation (Fig. S15). The ICP measurement suggested the atomic Ru/Hf ratio decreased to 0.68 after the durability evaluation. The obtained Ru 3p3/2 XPS spectra further verified that substantial Ru atoms maintained in metallic state under HfO2 protection. However, the atoms of L-Ru and S-Ru were almost transformed to RuO2 during OER operation (Fig. S16). These results illustrated a relatively small change in structure and composition of L-Ru/HfO2 during the 250 h of OER testing and also affirmed the stability enhancement as synergistically modified by HfO2 decoration and forming small crystalline domains.
A pH-universal catalyst was desired to adapt to different application scenarios. Accordingly, we studied the OER behavior of L-Ru/HfO2 in alkaline and neutral environment. As seen in Fig. 3E, L-Ru/HfO2 required an overpotential of 254 and 313 mV to reach 10 mA cm-2 in 1 M KOH and 1 M PBS electrolytes, respectively, which were better than all the controlled samples including RuO2. In addition, as the counterpart reaction for OER, hydrogen evolution performance of these as-synthesized samples was also investigated and compared with commercial Pt/C (Figs. 3F and S17). Obviously, L-Ru/HfO2 needed an overpotential of 18.9 mV to reach the reference current density of 10 mA cm-2 toward HER in 1 M KOH, overperformed other samples as well as commercial Pt/C catalyst (46.1 mV) (Fig. S17A). In the meantime, the onset potential of L-Ru/HfO2 (6.71 mV) was smaller than those of all controlled materials. Also, L-Ru/HfO2 exhibited the smallest Tafel slope (25.1 mV dec−1) among them, implying an accelerated Volmer-Tafel kinetic (Fig. S18A). The achieved small impedance of 15.1 Ω demonstrated a high charge transfer capacity for L-Ru/HfO2 (Fig. S18B). And the chronoamperometry test proved its good stability for continuous hydrogen production (Fig. S19). Moreover, the HER performance was examined in 1.0 M PBS, where L-Ru/HfO2 catalyst still exhibited the highest activity with 37.9 mV overpotential requirement to achieve 10 mA cm-2 current density in the neutral solution (Fig. S17B). In acidic environment, L-Ru/HfO2 overperformed all the Ru-based reference samples (Fig. 3F), implying the strengthened water dissociation ability of L-Ru/HfO2 to supply protons from water molecule for reduction. Since the OH* reactant also came from water dissociation for non-alkaline OER, this observation implied the Ru metal with HfO2 modification enabled an improved oxygen production in the acidic environment.
Next, control experiment was performed to disclose the pivotal role of Ru for this overall catalysis, by means of the blocking effect of SCN- ions on Ru atoms [40]. As observed in Fig. 3G, L-Ru/HfO2 almost lost its catalytic ability for both OER and HER in presence of KSCN, with negligible current density responses. As such, HfO2 was inactive toward both OER and HER, and the actual Ru sites with HfO2 protection should determine the overall water splitting. Therefore, constructing Ru/HfO2 heterostructure with small crystalline domains could endow Ru sites with an enhanced stability, accompanied by an improved intrinsic activity. Finally, we assembled a proton exchange membrane (PEM) to study the potential of practical application. The as-achieved L-Ru/HfO2 was employed as both cathode and anode catalysts, which were further assembled with a Nafion 115 membrane in 0.5 M H2SO4 to construct an electrolyzer for overall water splitting evaluation (Fig. 3H). As compared in Fig. 3I, L-Ru/HfO2 needed 1.57 and 1.67 V voltages to reach the cell current densities of 100 and 300 mA cm-2, respectively, which were superior to S-Ru/HfO2 (1.63 V at 100 mA cm−2 and 1.74 V at 300 mA cm−2) and commercial Pt/C||RuO2 (1.66 V at 100 mA cm-2 and 1.79 V at 300 mA cm-2). The behavior was in consistent with the above observations as obtained by three-electrode measurement, confirming the efficient kinetics for this bi-functional catalyst. Apart from this, L-Ru/HfO2 assembled electrolyzer presented no significant attenuation of current density after a long period of water electrolysis (Fig. 3I), which was similar to above HER and OER stability measurements, demonstrating its potential for practical use in the water electrolyzer system.
3.3 In Situ Spectra Characterizations and DFT Calculations
The electrochemical in situ Raman spectroscopy was then carried out to gain deeper insights on L-Ru/HfO2 for acidic oxygen evolution. As shown in Fig. 4A, the Raman peak at 187.9 cm-1 on L-Ru/HfO2 was assigned to the Ru-Ru binding vibration, while L-Ru without HfO2 modification displayed featureless on this signal (Fig. 4B). This verified that the majority of Ru atoms in L-Ru/HfO2 maintained metallic state, but the Ru atoms of L-Ru, especially those on surface, were preferable in an oxidized state. In a closer observation, the Ru-Ru peak of L-Ru/HfO2 exhibited a gradual shift toward the positive direction following potential increasing (Fig. 4C). When the applied potential was higher than 1.0 V, the Ru-Ru binding peak weakened and shifted negatively. Even up to 1.6 V, this bond signal was discerned in the recorded spectrum, suggesting the robust Ru0 state of L-Ru/HfO2 in the OER potential window region. Henceforth, HfO2 decoration significantly enhanced the anti-oxidation ability of Ru, thereby improving its stability. This was conductive to realize overall water splitting under a wide operating potential window. The vibration profiles at 609.8, 1198.2, and 798.8 cm-1 corresponded to M-OH [50], M-O [53] and M-OOH [54] binding modes, respectively, and the “M” represented active sites of catalyst for reaction (Fig. 4C, d). These oxygen related species were generally regarded as main intermediates evolved during oxygen production.
Fig. 4 In situ Raman spectra recorded on A L-Ru/HfO2 and B L-Ru. C, D The magnified spectra of corresponding vibration regions for Fig. A and B, respectively. The in situ high-resolution XPS spectra of Ru 3p signals under an applied voltage of 2.0 V for E L-Ru/HfO2 and F S-Ru/HfO2 |
As compared with L-Ru, L-Ru/HfO2 exhibited a relatively steady M-OH profile, which was independent of potential variations. This indicated a stable chemical environment and robust structure for L-Ru/HfO2 to continuously supply OH from water molecule dissociation that could provide favorable reactants to ensure durable oxygen production. Previous studies reported the O*→OOH* conversion was the rate-determining step for OER, thus a moderate M-O bonding was beneficial to accelerate O2 production [39]. As seen in Fig. 4B, D, the M-O peaks were extremely sharp and strong on L-Ru. Accordingly, they became rather wider and weaker for L-Ru/HfO2 (Fig. 4A, C), indicating an effective alleviation to achieve moderate *O combination on Ru by HfO2 modification. This was conductive to reduce the energy barrier from *O to *OOH conversion, thereby ensuring the continuous progress of oxygen generation. Therefore, the M-OOH signals measured on L-Ru/HfO2 became quite stronger than those of L-Ru, which implied more *OOH species generated by HfO2 decoration due to its appropriate *O→*OOH conversion.
In order to examine the microelectronic structure response, in situ XPS characterization was thus performed. When applying a 2.0 V oxidized voltage, there was no significant change occurring in Ru 3p orbital of L-Ru/HfO2 (Figs. 4E and S20). However, it underwent a positive shift of 0.8 eV for S-Ru/HfO2 (Fig. 4F) as the external potential was applied. This represented that the crystalline improvement endowed Ru with a higher antioxidant capacity, which enabled it to maintain the metallic state under OER oxidation potentials and environment.
Subsequently, DFT calculations were performed according to experimental results. The HfO2 (001) crystal plane in orthorhombic symmetry and Pmnb space group was built to mimic HfO2 crystalline surface as observed in the TEM and XRD data. In light of previous reports, Ru13 cluster was selected to model the Ru counterpart [25]. Also, RuO2 (001) slab structure was taken and investigated for comparison. All of these structures were displayed in Fig. S21. Recent studies revealed three mechanisms for OER, including adsorbate evolution mechanism (AEM), lattice oxygen mechanism (LOM) and dual-site oxide mechanism (DSM) [25,38]. Considering the Ru active sites in L-Ru/HfO2 were mainly kept in metallic state, the LOM pathway was excluded, and thus, we focused on the AEM and DSM in the following discussions, with their depiction shown in Fig. 5A. The corresponding free energy variation diagrams were compared in Fig. 5B, in which, each reaction step exhibited an endothermic feature at zero potential. Apparently, the conversion from O* to OOH* was the rate-determining step for Ru/HfO2, with a large barrier of 2.21 and 1.68 eV for the AEM and DSM paths, respectively, which were in agreement with previous reports. Although the limiting energy barrier of Ru/HfO2 in AEM pathway was greater than that of RuO2, its DSM root was significantly suppressed with a relatively lower barrier. Charge density difference calculation unveiled the electron transfer at interface, and the accumulated charge density at Ru sites was consistent with the XPS observations (Fig. 5C). The d-band center was sensitive to the intermediate adsorption. The presence of HfO2 enabled a downshift of d-band center position from −2.54 to −2.86 eV, making it farther away from the Fermi level as shown in the calculated density of states in Fig. 5D. Therefore, the interaction between adsorbed *O and active Ru site was weakened, facilitating the *O→*OOH conversion for continuous oxygen production.
Fig. 5 DFT calculations. A AEM and DSM paths of OER on the catalyst surface. B Free energy change diagrams for OER over Ru/HfO2 catalyst through different paths. C Charge density difference at the interface of Ru/HfO2, with the warm color and cold color representing charge accumulation and depletion, respectively. D Calculated projected DOS with d-band center highlighted for the active sites. E Adsorption energy of water molecule on these catalysts. F FTIR profiles of L-Ru and L-Ru/HfO2 before and after the water vapor treatment. G Water dissociation energy diagrams (inset: corresponding optimized Ru/HfO2 structures for water dissociation, with gray, light green, red and white balls representing Ru, Hf, O, and H atoms, respectively) |
Since H2O adsorption was the initial step that strongly affected the kinetics of acidic OER, we thereby evaluated its adsorption effect on Ru/HfO2. Apparently, Ru/HfO2 exhibited a significantly strengthened adsorption energy for H2O molecule than both pure Ru and RuO2 (Fig. 5E). This phenomenon was also confirmed by FTIR spectra. As compared in Fig. 5F, L-Ru/HfO2 exhibited an obvious increment in hydroxyl peak after being held in water vapor environment, while L-Ru displayed a less response to the water vapor adsorption. These results revealed the more feasible water adsorption ability on Ru benefited from HfO2 decoration, which facilitated water molecules to be continuously adsorbed on the catalyst surface in acidic environment, ensuring that the oxygen generation was kept running.
Furthermore, the transition state variation obtained from nudged elastic band calculations revealed a significantly suppressed energy barrier for Ru/HfO2 to dissociate water molecule into *OH and *H species (Fig. 5G). Thus, a strengthened water adsorption associated with an alleviated dissociation capability was simultaneously obtained by HfO2 modification, which enabled a boosted oxygen production rate on Ru/HfO2 in acidic media. On the other hand, *H adsorption free energy (ΔG*H) was considered as a key descriptor to describe the ability of adsorbed *H recombining H2 molecules and thus, was valid for predicting the HER capability. Figure S22 illustrated the quite thermoneutral ΔG*H on Ru/HfO2, facilitating H2 release and promoting the Tafel step of HER.
4 Conclusions
In summary, L-Ru/HfO2 hybridized nanosheets composed of small crystalline domains were fabricated through a two-step annealing method, which could act as a stable catalyst for both acidic OER and HER, as well as in pH-universal conditions. The as-obtained L-Ru/HfO2 catalyst exhibited a low overpotential of 197 mV to reach 10 mA cm-2, associated with a slight degradation during continuous OER operation at 10 mA cm-2 for 250 h in 0.5 M H2SO4. When assembled with a proton exchange membrane, the bi-functional L-Ru/HfO2 catalyst-based electrolyzer presented a voltage of 1.57 and 1.67 V to reach 100 and 300 mA cm-2 current density, respectively, exceeding most reported Ru-based materials and commercial Pt/C||RuO2 electrolyzer. The electronic state study revealed the synergism of HfO2 modification and ultrasmall crystalline domain formation endowed Ru with improved anti-oxidation capability, leading to a metallic state that quite close to Ru foil. Both in situ Raman and in situ XPS characterizations confirmed the robust metallic Ru in L-Ru/HfO2 for catalysis. Combined with simulations, it suggested the limiting step of *O→*OOH conversion was accelerated through an dual-site oxide path and also the water adsorption and dissociation steps were strengthened. Consequently, a robust catalyst for overall water splitting was obtained, and it may also establish new directions for designing robust materials for energy conversion and storage in wide conditions.
Declarations
Conflict of interests
The authors declare no interest conflict. They have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
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Supplementary Information The online version contains supplementary material available at https://doi.org/10.1007/s40820-024-01384-7.
