Ying
Li
a,
Yonggui
Deng
b,
Dongqing
Liu
b,
Qianqian
Ji
*a and
Xingke
Cai
*a
aInstitute for Advanced Study, Shenzhen University, Shenzhen, China. E-mail: cai.xingke@szu.edu.cn; jiqian28@mail.ustc.edu.cn
bCollege of Mechatronics and Control Engineering, Shenzhen University, Shenzhen, China
First published on 17th November 2023
The oxygen evolution reaction (OER) is a key anode reaction for many renewable energy devices, such as electrocatalytic water splitting devices, Zn–air batteries and CO2 electrolyzers. Transition metal oxides have been broadly explored for the OER due to their good electrochemical stability and low cost. However, their generic catalytic performance and poor electrical conductivity have greatly impeded their practical applications. Fabricating oxides into two dimensional (2D) structures can increase their surface areas and modulate the electronic structures of their catalytic sites, which is a new method to improve the OER performance. However, 2D oxides still come across some challenges for the OER, such as easy restacking of the 2D materials, poor intrinsic activity of the transition metal atoms and difficulty in their mass production. In this review, we firstly introduce the background and importance of the OER. Then, the OER mechanism and strategies to optimize the OER performance for 2D oxides are thoroughly reviewed. Their initial explorations in water splitting, Zn–air battery and CO2 electrolyzer applications have also been considered. Finally, the current challenges and future opportunities in the synthesis and applications of 2D oxides are clearly highlighted.
There are currently three main types of OER catalysts. The first type consists of commercial OER catalysts such as precious metal oxides, namely RuO2 and IrO2. These materials are regarded as benchmark electrocatalysts and exhibit excellent catalytic activity. However, their large-scale application in industry has been impeded by their high price, difficult recovery, low earth-abundance, and poor resistance of precious metals to deactivation, as well as their proneness to agglomeration or dissolution during the cycling process, leading to rapid performance degradation.8–10 Consequently, the development of high-performance, metal-free/non-noble-metal catalysts is highly desirable. The second type comprises nonmetal-doped carbon nanomaterials.11 These carbon materials possess features such as significant surface area, high electronic conductivity, and suitable catalytic properties. Nonetheless, they are easily destroyed by intermediates or by-products at high oxidation potentials or high current densities when acting as carriers or direct catalytic sites. Accordingly, the inherent catalytic performance of carbon materials is not ideal, and their stability in practical applications still faces critical challenges. The third type comprises transition-metal-based nanomaterials. These materials are promising candidate electrocatalysts for industrial applications because of their low price, numerous metal oxidation states, various structural and electronic modulation strategies, and ease of large-scale preparation.12–14
To date, numerous investigations have been conducted on diverse transition-metal-based catalysts for the OER. These catalysts comprise transition-metal-based oxides, borides, phosphides, sulfides, layered double hydroxides (LDH), and metal–organic frameworks (MOFs).15–20 Generally, transition metal oxides exhibit excellent OER durability owing to their stable structure at high oxidation potentials. In contrast, transition-metal-based phosphides and sulfides are prone to inevitable structural reconfiguration during reaction and reconstruction-induced aggregation of oxyhydroxide species with low electrical conductivity, resulting in a slow charge-transfer kinetics.21 The OER stability of these electrocatalysts is severely challenged under strongly oxidizing conditions, especially at high current densities. Considering that OER electrocatalysts should meet the requirements of high activity and long-time durability for practical applications, transition-metal oxides show promising application prospects in the industrial community. Significantly, the most widely studied transition metal oxide electrocatalysts are spinel-, rutile-, and perovskite-structured nanomaterials. Nevertheless, the particle size of nanomaterials is usually larger than 200 nm, leading to low atomic utilization.22–24 These catalytic materials are generally stable during the OER, but their intrinsic catalytic performance is not ideal.
More strikingly, developing 2D-structured transition metal oxides is considered an effective method for optimizing the OER performance. In general, 2D-structured materials not only have more exposed active sites, but their performance also differs from that of conventional catalysts owing to the 2D size effect and unique crystal structure. The combination of 2D structures with electronic structure modulation strategies has resulted in a substantial enhancement in the OER performance of 2D oxide catalysts.
This review discusses the OER mechanism over a wide pH range. Various strategies, including loading 2D materials onto substrates, constructing defects, creating heterojunctions, and fabricating signal atoms, are used to enhance the interfacial charge transfer and mass transfer rates, lower the energy barrier, and enhance reaction efficiency, as described in detail. The applications of 2D oxides in water electrolysis devices, zinc–air batteries and CO2 electrolyzers are also summarized. Finally, it offers an analysis of the current challenges faced and potential future directions for 2D oxides.
Catalysts | Media | Overpot-ential | Tafel Slope | Ref. |
---|---|---|---|---|
Porous MoO2 | 1.0 M KOH | 266 | N/A | 41 |
Co/MoO2 | 1.0 M KOH | 318 | 93.9 | 33 |
CuCo2O4 | 1.0 M KOH | 260 | 64 | 34 |
r-CFO | 1.0 M KOH | 280 | 43 | 39 |
NF/H-CoMoO4 | 1.0 M KOH | 295 | N/A | 35 |
MoN/MoO2-6 | 1.0 M KOH | 292 | 98 | 42 |
NiO/RuO2/NF | 1.0 M KOH | 210 | 68.7 | 38 |
P-NiFe2O4 | 1.0 M KOH | 231 | 49 | 43 |
Fe3O4/Co3S4 | 1.0 M KOH | 270 | 56 | 44 |
N-BMO | 1.0 M KOH | 349 | 42 | 45 |
CoMoO4/MoO2 | 1.0 M KOH | 230 | 51 | 46 |
NiMoO4 | 1.0 M KOH | 239 | 71.8 | 47 |
Co1Fe1Mo1.8O/NF | 1.0 M KOH | 210 | 32 | 48 |
Co3O4/CoMoO4/NF | 1.0 M KOH | 244 | 52 | 49 |
NiO | 1.0 M KOH | 380 | 299 | 50 |
P-NiO | 1.0 M KOH | 294 | 92.6 | 51 |
Ni@C-MoO2/NF | 1.0 M KOH | 240 | 52.3 | 52 |
Co3Mo/CoMoO3 | 1.0 M KOH | ∼265 | 64.1 | 53 |
IrW/WO3-NS-A | 0.5 M H2SO4 | 229 | 88 | 54 |
4CeO2@SrIrO3 | 0.5 M H2SO4 | 238 | 71.7 | 55 |
R20-Mn | 0.5 M H2SO4 | 210 | 54.2 | 56 |
Co3O4 UNA | 1.0 M PBS | 207 | 60 | 57 |
Pd/NiFeOx | 1.0 M KOH | 180 | 59.2 | 58 |
Pd/NiFeOx | 0.5 M H2SO4 | 169 | 76.6 | 58 |
Pd/NiFeOx | 1.0 M PBS | 310 | 175.1 | 58 |
CoFe2O4 NSs | 0.2 M PBS | 275 | 42.1 | 59 |
S-NiFe2O4/NF | 1.0 M PBS | 494 | 118.1 | 60 |
S-NiFe2O4/NF | 1.0 M KOH | 267 | 36.7 | 60 |
S-doped M-SrIrO3 | 0.5 M H2SO4 | 228 | 58.4 | 61 |
Pawar et al.34 synthesized ultrathin CuCo2O4 nanosheets containing abundant nanopores on NF substrates through electrodeposition and air annealing treatment.66 The scanning electron microscopy (SEM) images revealed that the CuCo2O4 nanosheet films had a larger pore density than the Co3O4 nanosheet films, indicating that the former have a large electrochemically active surface area (Fig. 3a and b). These ultrathin nanosheet films with nanopores promote charge and mass transfer, and this unique morphology can effectively facilitate the adsorption of reactants and the desorption of intermediates and products. In detail, to eliminate the impact of the oxidation peak, the true properties the Co3O4 nanosheets resulted in an overpotential of 330 mV at 20 mA cm−2, accompanied by a Tafel slope of 67 mV dec−1, whereas the CuCo2O4 nanosheets exhibited a relatively lower overpotential of 260 mV at 20 mA cm−2 with a Tafel slope of 64 mV dec−1, revealing the more favorable electrocatalytic kinetics in the case of CuCo2O4. Moreover, the CuCo2O4 electrocatalyst exhibited outstanding durability up to 25 h at 20 mA cm−2. Notably, the linear sweep voltammetry (LSV) curves of the Co3O4 and CuCo2O4 nanosheets showed the same overpotentials before and after the stability test. The above results illustrate that structural regulation and the introduction of a support can optimize the catalytic performance and durability of transition metal oxides in alkaline solutions (Fig. 3c and d).
Fig. 3 SEM images of the (a) Co3O4 and (b) CuCo2O4 nanosheet films; (c) and (d) OER performance of Co3O4, CuCo2O4 and Ni foam.34 Reproduced with permission. Copyright 2019, Elsevier. (e) The synthetic steps of porous MoO2 nanosheets on nickel foam directly; (f) steady-state polarization curves of Ni foam, commercial Pt/C, compact MoO2, and porous MoO2 in 1.0 M KOH for the HER and OER;37 reproduced with permission. Copyright 2016, Wiley. Characterization of Co3O4 UNA. (g) SEM image and (h) AFM image of Co3O4 ultrathin nanosheets; (i) and (j) electrocatalytic OER in 1.0 M PBS (pH = 7) electrolyte.57 Reproduced with permission. Copyright 2017, Springer Nature. |
In recent years, studies on MoO2 nanosheets for the catalytic OER have gradually increased due to the numerous crystal morphologies of MoO2 (for example α-, β-, γ-, λ-, δ-, and R-MnO2), as well as the enhanced metallic character, charge transfer capability, and conductivity of MoO2.67–69 Significantly, porous 2D materials combine a considerable surface area and a larger concentration of active sites per unit mass. Jin et al.37 constructed porous 2D MoO2 nanosheet arrays on the surface of NF; these assemblies were used directly without post-treatment, avoiding the addition of organic binders. As shown in Fig. 3e, porous MoO2 was grown directly on a commercial NF substrate via a wetting chemical route, followed by an annealing process. Accordingly, the pore size dispersion in the direction parallel to the NF was 5–20 nm. As shown on the right side of Fig. 3f, the porous MoO2 exhibited excellent catalytic activity towards the OER, showing an onset potential of approximately 1.43 V. Additionally, it showcased outstanding performance compared with nickel foam, Pt/C, and compact MoO2, as it accomplished current densities of 10 and 20 mA cm−2 at 1.49 and 1.51 V, respectively. Pei et al.48 developed edge-rich Mo-doped cobalt iron oxide nanosheets assembled on NF substrates. TEM was used to examine the porous structure with edge-rich interfaces. Moreover, the proportion of Mo atoms played a pivotal role in adjusting the electronic structure. Accordingly, the Co1Fe1Mo1.8ONMs@NF electrocatalyst demonstrated outstanding performance, displaying the lowest overpotentials at 240 and 250 mV for current densities of 50 and 100 mA cm−2, respectively.
Thin films were typically synthesized by chemical vapor deposition, exfoliation, and a surfactant-assisted approach, which require special equipment and reaction conditions, or they are limited by low yields and difficulty in controlling lateral film size and structure. Furthermore, achieving high loading of ultrathin nanosheets on the electrodes without compromising their catalytic activity remains challenging. Zhang and colleagues57 presented a simple electrodeposition method for the preparation of Co3O4 and Co(OH)2 ultrathin nanosheet arrays (UNA) without the use of templates or surfactants (Fig. 3g and h). The obtained arrays show a high activity for the evolution of oxygen and hydrogen, both in alkaline and neutral media. In addition to the larger specific surface area and the higher exposure catalytic active sites resulting from the UNA structure, three additional desirable features are also achieved: efficient mass and charge transfer through the electrolyte, catalyst and electrode; high loading of ultrathin nanosheets on the electrode; and efficient release of gas bubbles from the electrode surface. In neutral media, the Co3O4 UNA exhibit much better catalytic performance than IrO2 and bare NF (Fig. 3i and j). Co3O4 UNA can deliver current densities of 10 and 50 mA cm−2 at overpotentials of 207 and 379 mV, respectively, much lower than IrO2 (389 and 683 mV). The outstanding catalytic activity of Co3O4 UNA in neutral media is attributed to the UNA structure, which has a large active surface area and allows high electrode loading of ultrathin nanosheets without affecting their catalytic activity. The performance of the electrocatalyst is frequently affected by the formation of H2 or O2 bubbles, which tend to adhere to the electrode surface, limiting the active surface area and mass transport.70 The Co3O4 UNA have a hydrophilic surface and a vertical nanosheet structure, allowing rapid release of O2 and H2 as small bubbles.71
Xia et al.33 anchored Co nanoparticles to MoO2 nanosheets (Co/MoO2) through hydrothermal treatment, followed by Ar/H2 reduction (Fig. 4a). The nanoparticles were uniformly dispersed on the nanosheets surface, as shown in the SEM image (Fig. 4b). As observed in Fig. 4c, Co/MoO2 had the lowest OER overpotential (318 mV at 10 mA cm−2) compared to CoMoO4 (355 mV), RuO2 (345 mV), Co (343 mV), and MoO2 (470 mV) in 1.0 M KOH electrolyte, which displayed outstanding OER performance. Electrochemical impedance spectroscopy (EIS) was employed in order to assess the interfacial kinetics. The smaller semicircle (corresponding to Rct) in the EIS plot suggests a faster charge transfer. It was determined that the Rct of Co/MoO2 was smaller than those of the reference materials (Fig. 4d). Furthermore, based on the result of charge density of states (DOS) in Fig. 4e, the electronic density of states of Co/MoO2 is greater than the Fermi energy levels of MoO2 and Co, which could explain the optimal reactivity of Co/MoO2. Taken together, the data show that the Co/MoO2 composite exhibits enhanced interfacial conductivity and electron transfer ability, with improved intrinsic activity, and it promotes the OER performance in alkaline solutions.75
Fig. 4 (a) Schematic illustration of the fabrication of Co/MoO2; (b) SEM image of Co/MoO2; (c) OER polarization curves of CoMoO4, Co/MoO2, MoO2, Co and RuO2; (d) Nyquist plots collected at 500 mV vs. SCE of Co/MoO2, MoO2 and Co; (e) density of states of Co/MoO2, MoO2 and Co.33 Copyright 2022, Royal Society of Chemistry; (f) a sketch map of the formation mechanism of core/shell Au NRs@MnO2 nanocomposites; (g) the OER performance of Au NRs@MnO2 with different Au/Mn ratios.76 Reproduced with permission. Copyright 2021, Elsevier. (h) Synthetic route diagram of CeO2@SrIrO3 nanosheets; (i) electrochemical OER performance in 0.5 M H2SO4 of mass activity normalized by Ir amount.55 Reproduced with permission. Copyright 2022, Elsevier. |
Core/shell Au@MnO2 nanocomposites are one of the most attractive combinations, with Au offering distinct optical, catalytic and surface-sensitive properties, while MnO2 has the advantage of a broad array of crystal structures and valence states. Despite the limitations of the universal template synthesis approach, Hu et al. utilized the local surface plasmon resonance (LSPR) effect method to create a core/shell metal@metal oxide structure of Au NRs@MnO2 nanosheets.76 In this method, Au NRs are easily oxidized by KMnO4 and undergo serious etching during the LSPR effect treatment, while in the absence of methanol or irradiation. Notably, KMnO4 was not only reduced to form MnO2,77–79 but also maintained the structural stability of the nanorods. In addition, the electrochemical activity was significantly affected by the Au/Mn ratio. In the experiment, the optimal OER performance was achieved when the Au NRs@MnO2 nanosheet composites had an Au/Mn ratio of 1:0.5 (Fig. 4g).
To date, IrO2 and RuO2, in particular the structurally robust IrO2, are recognized as the available electrocatalysts for acidic OER.80,81 Nevertheless, their terrestrial scarcity and exorbitant cost are the main bottlenecks for their large-scale application. Therefore, there is an urgent need to develop cost-effective electrocatalysts with high mass or specific activity. An original research study showed that the pseudocubic perovskite SrIrO3 with in situ surface rearrangement of IrOx/SrIrO3 offered high intrinsic OER activity.82 Simultaneously, cerium oxide (CeO2), rich in oxygen vacancies and reversible redox between Ce4+ and Ce3+, is widely used as a co-catalyst to enhance activity and stability in various catalytic fields. You and collaborators55 firstly elaborated a 0D/2D structure of CeO2 quantum dot decorated SrIrO3 nanosheets (CeO2@SrIrO3) as the promising electrocatalyst for the OER in acidic media. The synthetic route diagram for CeO2@SrIrO3 nanosheets is shown in Fig. 4h. As revealed via theoretical calculations, the rearranged charge density in the heterostructure alters the adsorption behavior of oxygen intermediates, ultimately lowering the activation energy of the OER. Moreover, the introduction of CeO2 can theoretically stabilize Sr atoms in the SrIrO3 lattice. As expected, the optimized 4CeO2@SrIrO3 electrocatalyst exhibits excellent OER performance in acidic media, delivering a low overpotential of 238 mV at 10 mA cm−2 and a long-lasting life for 50 h. Fig. 4i presents the mass activity of electrocatalysts normalized by Ir amount at 1.50 V. One can see that the 4CeO2@SrIrO3 electrocatalyst presents the highest mass activity of 249 A gIr−1 among these prepared electrocatalysts, which is almost three times higher than 82.3 A gIr−1 for the individual SrIrO3 electrocatalyst. This 0D/2D structure involving CeO2 quantum dots decorated SrIrO3 nanosheets to achieve a durable and active OER under a harsh acidic environment. Theoretical calculations further unveil that CeO2 coupling with electronic rearrangement not only lowers the energy barrier of the OER but also mitigates Sr leaching. Benefiting from the activation and stabilization dual-effect of CeO2 coupling, the 4CeO2@SrIrO3 exhibits excellent OER performance.
Guo et al.39 designed a defect-engineering strategy for obtaining the target catalyst with abundant oxygen vacancies. First, CoFe2O4 (CFO) nanosheets were successfully generated through a straightforward hydrothermal synthesis reaction. Oxygen-poor CoFe2O4 (p-CFO) was produced after treatment under a nitrogen atmosphere, whereas oxygen-rich CoFe2O4 (r-CFO) was created via a reduction reaction at ambient temperature (Fig. 5a). The O 1s XPS spectra of CFO showed two main peaks at 530.7 and 529.6 eV, which were attributed to hydroxy–oxygen (H–O) and metal–oxygen (M–O) bonds, respectively (Fig. 5b).89,90 Noticeably, a new peak appeared at 531.9 eV in the spectra of p-CFO and r-CFO, which can be attributed to oxygen vacancies.91–93 Notably, the peak area corresponding to oxygen vacancies was larger for the r-CFO nanosheet compared with p-CFO, demonstrating that the r-CFO nanosheets provide more oxygen vacancies. Furthermore, density functional theory (DFT) calculations showed that the introduction of oxygen vacancies into the r-CFO nanosheets lowered the adsorption barrier energy to 0.56 eV, thus facilitating the adsorption of the reactant on the catalyst surface. Along with oxygen vacancy doping, the slight narrowing of the bandgap was induced, which enhanced the electronic conductivity of the r-CFO nanosheets. Compared to pure CFO, the oxygen-vacancy-rich r-CFO nanosheets exhibited a smaller overpotential and Tafel slope for the OER in alkaline electrolyte. The introduction of oxygen vacancies created a small adsorption energy barrier and bandgap, improving the conductivity and charge transfer capability. Taken together, the oxygen vacancies and substrate support can also improve the intrinsic properties of catalysts.
Fig. 5 (a) Schematic diagram illustrating the synthesis process of r-CFO and the significant role of oxygen vacancies in electrocatalytic overall water splitting; (b) the XPS spectra of O1s for CFO, p-CFO and r-CFO; (c) the model of CFO-1 Ovac with one oxygen vacancy on the surfaces; (d) polarization curves of CFO, p-CFO, r-CFO and RuO2 for the OER; (e) adsorption energy (Eads) comparison of CFO-Fe1oct, CFO-1Ovac-Fe1oct and CFO-1Ovac-Fe2oct.39 Reproduced with permission. Copyright 2019, Royal Society of Chemistry. (f) EPR spectra of three BMO electrodes; digital photos of water contact angle for (g) BMO, (h) N-BMO and (i) A-BMO.45 Reproduced with permission. Copyright 2021, Elsevier. (j) Schematic of CoFe2O4 nanosheets.59 Reproduced with permission. Copyright 2019, Royal Society of Chemistry. (k) Schematic illustration of cation vacancy formation in 2D NiFe-LDH.86 Reproduced with permission. Copyright 2022, John Wiley and Sons. |
Ma et al.45 employed a one-step hydrothermal reaction to create Bi2MoO6 (BMO) nanosheet arrays on NF. The surface of BMO was modified via treatment with ammonia plasma, whereby N atoms were doped into BMO and oxygen vacancies were simultaneously introduced. First, to determine the density of vacancies, electron paramagnetic resonance (EPR) was utilized as primary characterization technique.94 Compared to the pristine state of BMO, N-BMO produced a sharp and intense oxygen defect signal, indicating that the concentration of oxygen defects was higher. Hydrophilicity is a well-known criterion for evaluating the gas-bubble-releasing behavior of electrocatalysts. As shown in Fig. 5g–i, the contact angle of N-BMO (27.8°) was smaller than that of BMO (53.7°) and A-BMO (29.0°), indicating that N-BMO had a lower barrier for the adsorption of H2O molecules and desorption of O2 on the electrode surface. Similarly, Chi et al.35 developed a novel category of bifunctional electrocatalyst for the OER, based on ordered 3D anoxic CoMoO4 nanosheet arrays. The target electrocatalyst was fabricated through a simple hydrothermal process, which was further enhanced by annealing under a reducing atmosphere of H2 and ammonia. These resulting materials were denoted as NF/H-CoMoO4 and NF/N-CoMoO4, respectively. Then, the NF surface was completely wrapped by well-distributed 2D CoMoO4 nanosheets. The 2D nanosheet arrays could maintain close contact with the 3D NF substrate, facilitating charge and mass transfer, resulting in stable electrocatalytic activity. Self-supported and binder-free architectured nanosheets are recognized as efficient electrodes for accelerating charge and gas diffusion. More importantly, an essential factor contributing to the improved OER performance is the existence of stable oxygen vacancies within the structure of the CoMoO4 nanosheets. Incorporating oxygen vacancies into 2D oxide materials offers a promising approach to enhance their activity, opening up new possibilities for designing and synthesizing optimal catalysts for efficient hydrogen production through water splitting.
Previous research on nanomaterials with regulated morphology and the high density of active sites generated from Prussian blue analog (PBA) precursors has been published.95 After thermal annealing, the majority of PBA-derived naomaterials formed porous or hollow structures. However, there is limited understanding about the transformation of PBAs into 2D ultrathin nanosheets. Fang et al.59 created 2D ultrathin CoFe2O4 nanosheets with numerous oxygen vacancies by reducing PBAs with NaBH4 at ambient temperature (Fig. 5j). With the large surface area, high density of surface-active sites, high electron transfer capability and durability, CoFe2O4 shows a low overpotential and Tafel slope for alkaline medium.
Interestingly, researchers have shifted their attention towards regulating cation vacancies. Wu et al.86 reported that cation vacancies in 2D NiFe-LDH arise from the leakage of metal cations due to aprotic-solvent-solvation. The resulting defective NiFe-LDH exhibits a shorter M–O length and longer M–M distance. These cation vacancies are crucial in the surface reconstruction process of NiFe-LDH, serving as a precatalyst to enhance the performance of the OER. In situ Raman spectroscopy and DFT calculations have revealed that the presence of cation defects in NiFe-LDH facilitates the localized conversion of crystalline Ni–(OH)x species to NiOOH species (Fig. 5k).
Yu and collaborators38 obtained NiO/RuO2 heterojunction nanosheets using an in situ growth strategy, as schematically illustrated in Fig. 6a. The ultrathin nanosheets grew uniformly on the NF substrate (Fig. 6b–e). Notably, NiO/RuO2/NF has a rough surface with vertical nanosheets crossing each other to form nano/microchannels. Based on this structure, the NiO/RuO2/NF electrocatalyst exhibits enhanced wettability, and the electrolyte is more accessible to the active sites at the interface.100 This unique structure also reduces the adhesion of air bubbles and accelerates the detachment of oxygen products,101 leading to enhanced mass transfer and improved catalytic performance. Multiple lattice stripes were observed in the HRTEM image (Fig. 6e). The interplanar spacings of d = 0.315, 0.254, and 0.210 nm were associated with the (110) and (011) lattice planes of RuO2 species, as well as the (200) lattice plane of NiO, respectively. The XRD pattern of NiO/RuO2 also confirmed that the obtained composite involved coexistence of NiO and RuO2 species (Fig. 6f). In the XPS analysis of NiO/RuO2/NF, a noticeable shift towards the lower binding energy region was observed for the Ru 3p peak compared to the RuO2/NF sample. Conversely, the Ni 2p peak underwent a positive shift of approximately 0.3 eV in relation to the RuO2/NF sample (Fig. 6g and h). This change indicates that the redistribution of electrons at the heterostructure interface was due to the difference in electronegativity between the NiO and RuO2 species.102 Consequently, the change in electron density around the nuclei of the Ru and Ni atoms showed the opposite results. Furthermore, RuO2 has a strong affinity for O atoms, which facilitates the desorption of *OH.103 At the same time, NiO is advantageous for water dissociation during the OER process. Therefore, the interfacial coupling effect of NiO/RuO2 enables *OH desorption and H2O dissociation, thus enhances the catalytic performance for the OER. Accordingly, the overpotential of NiO/RuO2/NF was significantly reduced to only 250 mV at a current density of 50 mA cm−2, surpassing the performance of both RuO2/NF (330 mV) and NiO/NF (390 mV).
Fig. 6 (a) Synthesis diagram of NiO/RuO2/NF; (b) SEM image; (c) and (d) TEM and (e) HRTEM images; (f) XRD pattern of NiO/RuO2; (g) and (h) the XPS spectra of Ru 3p and Ni 2p for NiO/RuO2/NF and RuO2/NF.38 Reproduced with permission. Copyright 2022, Elsevier. (i) HRTEM image of CoOx–RuO2; (j) OER polarization curves and (k) Tafel plots curves of samples.104 Copyright 2021, American Chemical Society. |
In another study conducted by Yu et al.,104 a novel approach was taken to develop CoOx–RuO2/NF by employing multi-metal oxides and a self-supported nanosheet structure strategy. This was achieved by depositing amorphous CoOx-decorated crystalline self-supporting RuO2 nanosheets onto a NF substrate through a simplified hydrothermal and annealing method. The self-supporting nanosheets exhibited several advantageous properties, including a significantly increased specific surface area, numerous exposed active sites, and a larger contact area between the active substance and the electrolyte, thereby improving the OER kinetics. The HRTEM image depicted in Fig. 6i illustrates the lattice stripes of CoOx–RuO2, the interplanar spacing of 0.255 nm is consistent with the (101) plane of RuO2, as confirmed by the XRD characterization. In some regions of the HRTEM image, no discernible lattice fringes can be observed, and these areas can be attributed to the amorphous phase of the CoOx component. The CoOx–RuO2/NF electrocatalyst showed high OER activity, achieving an overpotential of only 260 mV at 50 mA cm−2 in 1.0 M KOH. This performance surpasses that of other catalysts such as RuO2/NF, CoOx/NF, IrO2/C/NF, and NF (Fig. 6j). Furthermore, CoOx–RuO2/NF demonstrated a smaller Tafel slope value (69.6 mV dec−1) compared to the reference electrocatalyst (Fig. 6k). Conspicuously, the overpotential of CoOx–RuO2/NF was significantly minimized to 420 mV when operating under a demanding current density of 1500 mA cm−2. These findings highlight the superior reaction kinetics of CoOx–RuO2/NF for the OER process. There are many reports on the construction of multicomponent heterojunctions for achieving enhanced catalytic activity. Qian et al.36 prepared a NiCo@C-NiCoMoO/NF heterojunction electrocatalyst, including N-doped graphene-decorated NiCo alloys and mesoporous NiCoMoO nanosheets grown on 3D NF. At a current density of 1000 mA cm−2, the overpotential was remarkably reduced to just 390 mV. Furthermore, the electrocatalyst showed excellent stability over 340 h with no significant decrease in the overpotential. These results indicate that this material has high catalytic activity and prolonged durability.
The combination of bimetallic oxide nanoparticles with bimetallic oxide nanosheets to form heterojunctions is a useful approach for enhancing the OER performance. Ma et al.53 constructed Co3Mo nanoparticles/pores with CoMoO3 nanosheets to form a heterostructure (Co3Mo/CoMoO3 NPSs) for the OER under alkaline conditions. The Co3Mo/CoMoO3 heterojunction electrocatalyst exhibited excellent OER activity at a current density of 500 mA cm−2, while maintaining a low overpotential of 410 mV. In addition to the heterojunctions composed of the alloys and oxides mentioned above, heterojunction electrocatalysts composed of metal nitrides and oxides have also been reported. Du et al.105 introduced a 2D MoN/MoO2 heterostructure nanosheet, in which a heterojunction was formed via partial nitridation; MoN was fabricated by annealing the Mo-based precursors under an ammonia atmosphere. The non-uniform interface between MoN and MoO2 served as an active site, effectively enhancing both the surface reaction kinetics and conductivity. Remarkably, the MoN/MoO2-6 sample displayed a significantly low overpotential of 292 mV at a current density of 10 mA cm−2. Taken together, constructing heterojunctions offers an effective strategy for obtaining an OER catalyst with exceptional performance.
Wang et al.115 conducted a study on the multistep synthesis of OER electrocatalysts, which resulted in an unprecedented achievement of loading single Ir atoms onto a nickel oxide substrate at a record-breaking high level of approximately 18 wt%. High resolution high-angle annular dark-field (HADDF) and element sensitive X-ray absorption fine spectroscopy (XAFS) were conducted to explore the monodisperse state of Ir atoms. Fig. 7a displays bright spots of atomically dispersed Ir in the off-axis projection on the surface of nickel monoxide through HADDF-STEM images. The bright spots correspond to the constituent heavy, single Ir atoms, which were overlaid on the outermost layer of the nickel monoxide nanosheet. Based on this finding, a model of the single Ir atom on the ultrathin NiO sheets is shown in Fig. 7b, while Fig. 7c illustrates the off-axis projection that corresponds to the imaging conditions shown in Fig. 7b. The projection of Ir atoms in the [111] and [211] regions of Ir–NiO clearly reveals that these Ir atoms were situated within the same Ni atom column, indicating that the Ir atoms were successfully incorporated into the NiO crystal lattice (Fig. 7d and e). Accordingly, in this projection, the Ir atoms overlapped exactly with the Ni atoms, where the bright points were recognized as Ir atoms, as indicated by the atomic line profiles (Fig. 7f–h). The main peak at approximately 1.5 Å in the extended X-ray absorption fine structure (EXAFS) spectra of Ir L-edge corresponds to the nearest Ir–O bond, which is similar to the Ir local coordination structure in IrO2 (Fig. 7i). Furthermore, EXAFS fitting of the Ni K-edge data revealed an Ir–Ni scattering pathway, confirming single-atom Ir doping of nickel monoxide (Fig. 7j). Consequently, the HAADF-STEM and XAS results both lead to the same conclusion that Ir atoms were evenly distributed within the external layer of nickel monoxide, and they were stabilized on the oxide surface by Ir–O bonds. DFT calculations (Fig. 7k and l) further confirmed that the Ir single atoms not only serve as active sites, but also enhance the activity of the intermediates surrounding the Ni atoms. The synergy of the Ni and Ir atoms significantly improved the OER performance of nickel monoxide. Unexpectedly, the electrocatalyst exhibited an overpotential of 215 mV at 10 mA cm−2 in alkaline electrolytes (Fig. 7m). This synthesis approach offers a promising opportunity for creating highly loaded single-atom catalysts.
Fig. 7 (a) Representative HAADF-STEM micrographs of the Ir–NiO catalyst; (b) and (c) corresponding atomic models; (d)–(g) atomic STEM images along the [111] zone axis and [211] zone axis; (h) the lines represent the line profiles for HAADF intensity analysis labeled in (f) and (g); Fourier-transformed EXAFS spectra at the (i) Ir L-edge and (j) Ni K-edge of the IrNiO catalyst and the references; (k) free energy diagrams of the OER at a potential of 1.23 V vs. RHE on perfect NiO (001) and single Ir atom doped NiO (001) (IrNiO (001)); (l) DFT-calculated 2D potential landscape for an *OH species on the Ir-NiO (001) surface, the energy is relative to that of *OH adsorbed on the pristine NiO (001) surface; (m) polarization curves for the OER.115 Reproduced with permission. Copyright 2021, American Chemical Society. |
In addition to the abovementioned regulation strategies, the electronic structure and crystal structure of 2D oxides can be modulated by directly doping metallic atoms or non-metallic atoms into the main material. Heteroatom doping can introduce additional active sites, thereby increasing the interaction between the catalyst and reactants. More importantly, heteroatom doping could adjust the electronic structure of catalysts, modify their energy band structure and energy level distribution, and thereby regulate the adsorption performance of reactants and electronic transport properties.
Chen et al.116 reported the introduction of non-metallic atoms into 2D nanosheets of NiFe2O4 to improve the conductivity and electrocatalytic performance through functionalization with phosphate ions. Phosphate-ion-modified NiFe2O4 (P-NiFe2O4) nanosheets were grown on carbon cloth using a facile hydrothermal method, followed by a phosphorylation process. Electrochemical testing showed that the obtained P-NiFe2O4 nanosheets exhibited a low overpotential of 231 mV at 10 mA cm−2 in 1.0 M KOH, along with a Tafel slope of 49 mV dec−1. In addition, the P-NiFe2O4 nanosheets displayed superior stability, after 50 h operation at various current densities, and the chronoamperometry curves showed no evident decay. Previous research has validated that incorporating high-valence foreign atoms can tune the electronic and local coordination structures of electrocatalysts. In addition to the formerly described element P, S is a regularly employed element in anion engineering methodologies. Oxygen vacancies are formed when the migration or loss of lattice oxygen from their normal positions results in the formation of soluble and over-oxidized metals, therefore, stabilizing lattice vacancies is a top priority.117,118 Doping is an effective technique for increasing the activity and stability of lattice oxygen, and the S element has been demonstrated to be an excellent dopant for lattice stabilization. Yu and colleagues61 present a simple anion engineering technique for improving acidic OER performance in monoclinic SrIrO3 (M-SrIrO3) perovskite electrocatalyst. The newly made S-doped M-SrIrO3 electrocatalyst has a considerable OER activity with an overpotential of just 228 mV to achieve 10 mA cm−2 and a long-lasting durability of over 20 h in a high-acid environment, outperforming commercial IrO2 and pristine M-SrIrO3 electrocatalysts. Additionally, the DFT simulations for the S-doped M-SrIrO3 catalyst were organized in a systematic manner to investigate the underlying OER mechanism. The DFT results show that S incorporation can increase the electrical conductivity of M-SrIrO3 since the band gap of S-doped M-SrIrO3 is noticeably less than that of unadulterated M-SrIrO3. Furthermore, injecting S reduces the strong binding of reaction intermediates (O*/OH*/OOH*) on the M-SrIrO3 surface, hence facilitating the OER process. Theoretical calculations and experimental verifications indicate that the S doping can modify the electronic structure of M-SrIrO3 and lower the energy barrier of the OER, resulting in noticeably increased electrocatalytic activity toward the OER.
Precious metal atom modifications on non-precious metals can alter the chemical compositions and physical characteristics of materials.119 However, due to the large lattice discrepancy between alien metals and the metal oxide host, directly substituting noble metal atoms into the metal oxides poses a great challenge.120 Through hydrothermal and thermal annealing treatment, self-supporting porous 2D Pd/NiFeOx nanosheets with a sizable cluster of peony-like flowers were created by Zhang et al.58 The obtained Pd/NiFeOx nanosheets with more exposed active sites, which improve electrical conductivity, make it easier for electrolyte to diffuse, and encourage the formation and release of bubbles on the catalyst's surface. On NiFe-based materials, the Pd atoms primarily disperse along the edges of pores or nanoflakes of the porous 2D structure and provide active sites. The electrochemical results demonstrate that Pd/NiFeOx nanosheets exhibit outstanding catalytic activity with ultralow overpotentials of 180 mV, 169, and 310 mV at 10 mA cm−2 for the OER, and 76, 46, and 75 mV for the hydrogen evolution reaction (HER), in 1.0 M KOH, 0.5 M H2SO4, and 1.0 M phosphate-buffered saline (PBS), respectively. The following characteristics can be responsible for the effective catalytic activity and outstanding stability of both the HER and OER at all pH values: (i) the flower-like cluster made of 2D nanosheets is densely packed with uniformly sized pores, which not only provides more exposed active sites but also promotes gas adsorption and resolution. (ii) The 2D structure of Pd/NiFeOx allows for close contact between the electrolyte and the catalyst, increasing the use of exposed active sites and promoting efficient electron and mass transfer. (iii) Significant coupling of Pd atoms with NiFeOx further improves the electrocatalytic performance. (iv) Pd atom modulation of NiFeOx active sites greatly decreases reaction kinetics and increases charge transfer, therefore strengthening HER and OER activities. The results of this study present a fresh idea for the manufacture of a novel catalyst for overall water splitting over the pH range.
Defect-rich metal-based nanosheets are considered potential catalysts for electrocatalytic water splitting. The presence of nanopores on the surface/interface creates additional active sites, significantly enhancing their mass transfer capacity. Unfortunately, the simple preparation of bifunctional nanosheet electrocatalysts remains a great challenge. Song et al.47 reported an economical and efficient method for acquiring ultrathin Ni–Mo nanosheets (NiMoO4) for water splitting. NiMoO4 exhibited excellent OER performance (239 mV@10 mA cm−2). Meanwhile, P-doped NiMoO4 nanosheets displayed superior HER performance (144 mV@10 mA cm−2). In this study, researchers assembled NiMoO4 and P-doped NiMoO4 into a two-electrode system to assess their effectiveness in water-splitting performance. Overall, a major breakthrough in this study is the remarkable synergistic effect achieved through defect engineering and elemental doping, providing guidance for the development of new catalysts. Although the NiMoO4 nanosheet is a bifunctional catalyst, different catalysts have been used for electrolytic water splitting at the anode and cathode, catalyzing the OER and HER, respectively. For application to the two types of catalytic reactions, many researchers have attempted to obtain novel composite catalysts by forming a heterojunction; these catalysts can be simultaneously used for both the OER and HER. For example, Zhang et al.127 proposed the integration of components that are active for the OER and HER into a new heterostructure by developing ruthenium–doped nickel oxide ((Ru–Ni)Ox). The (Ru–Ni)Ox electrode exhibited excellent bifunctional catalytic activity (Fig. 8b and c) with minimum overpotentials of 15 mV for the HER and 237 mV for the OER at 10 mA cm−2, respectively. Accordingly, the (Ru–Ni)Ox bifunctional electrocatalyst was assembled as an anode and cathode catalyst in KOH solution (Fig. 8a), and the total water splitting only required 1.48 V to deliver 10 mA cm−2, which is lower than that of the commercial coupled Pt/C and RuO2 catalyst. Furthermore, the chronoamperometry curves at 10 mA cm−2 and 50 mA cm−2 demonstrated good long-term stability, indicating the potential of (Ru–Ni)Ox for hydrogen production (Fig. 8d–f). Coincidentally, Yu and collaborators38 discovered that CoOx–RuO2/NF presents good catalytic performance for the OER and HER. Notably, both the cathode and anode were CoOx–RuO2/NF electrocatalysts. A comparative electrolyzer consisting of Pt/C/NF as the cathode and IrO2/C/NF as the anode was assessed. The electrolyzer employing a CoOx–RuO2/NF bifunctional catalyst required only 1.49 and 1.55 V to obtain current densities of 10 and 50 mA cm−2, respectively; these values are superior to those of Pt/C/NF||IrO2/C/NF (1.63 V and 1.76 V). In the durability tests, the bifunctional catalyst remained stable for 72 h at 1500 mA cm−2, with slight attenuation in the chronoamperometry curve. This outstanding durability could be attributed to the following: (i) CoOx decorated onto RuO2 can lead to small impedances and enhance electron transport at a high current density;128 (ii) the NF support substrate is favorable for electrolyte delivery to the active sites and gas diffusion, thus enhancing the catalyst's ability to withstand high current density increased durability;129 (iii) the CoOx–RuO2/NF nanosheets are tightly integrated onto the support substrate, which could prevent detachment of the electrocatalyst.52 The above results suggest that CoOx–RuO2/NF is promising for industrial water splitting applications.
Fig. 8 (a) Schematic illustration showing the reaction route of the water electrolysis; (b, c) HER and OER curves. (d) Overall water splitting (e) comparison of potentials of (Ru–Ni)Ox (+, −), RuO2 (+)‖Pt/C (−), NiO (+, −), and bare NF (+, −); (f) Chronoamperometry curves of (Ru–Ni)Ox (+, −).127 Reproduced with permission. Copyright 2021, Elsevier. Overall water splitting application in 0.5 M H2SO4 electrolyte; overall water splitting application in 0.5 M H2SO4 electrolyte: (g) working principal diagram of two-electrode water splitting devices; (h) polarization plots of 4CeO2@SrIrO3||Pt-C based electrolyzer and benchmark IrO2||Pt/C based electrolyzer; (i) Faraday efficiency of the OER conducted at 10 mA cm−2 using a 4CeO2@SrIrO3 electrode.55 Reproduced with permission. Copyright 2022, Elsevier. |
Strontium iridate perovskites are potential OER electrocatalysts in acidic environments. You et al.55 reported CeO2 quantum dot decorated SrIrO3 nanosheet synthesis using a sol–gel and wet chemistry approach. The obtained 4CeO2@SrIrO3 was employed as both the anode and cathode in a two-electrode system for the overall water splitting in 0.5 M H2SO4 electrolyte. It was found that to achieve 10 mA cm−2 only required a cell voltage of 1.51 V, favorably rivaling 1.66 V over the commercial noble-based water electrolyzer. The durability of 4CeO2@SrIrO3 was evaluated using chronoamperometry, where the electrocatalyst remained continuously stable for 50 h at 10 mA cm−2 in harsh acidic media. The results illustrate that 4CeO2@SrIrO3 manifests excellent performance in the overall water splitting process. The catalyst was characterized after long-term durability testing, where there was no obvious change in the morphology before and after the test, unveiling the exceptional catalytic stability of this electrocatalyst. The stable structure and catalytic performance of the 4CeO2@SrIrO3 ultrathin nanosheet catalysts are attributed to three factors: (i) the surface CeO2 coating plays a protective role to stabilize SrIrO3. (ii) This interfacial interaction, a novel mixed-dimensional electrocatalyst presents fast rapid kinetics. (iii) The interfacial charge redistribution reduces the energy barrier of the OER. All these factors result in enhanced electrochemical performance.
Aside from crystalline 2D oxides, amorphous materials also exhibit a highly active surface containing abundant dangling bonds and numerous undercoordinated active sites, making them potential electrocatalysts for overall water splitting over a wide pH range. Do et al.130 recently reported a simple synthetic approach to confine atomically thin Pd–PdO nanodomains within amorphous RuO2. The Pd2RuOx catalyst exhibits an OER overpotential of 225 mV@10 mA cm−2 and a HER overpotential of 14 mV@10 mA cm−2 in 1.0 M KOH. It is noteworthy that the overall water splitting voltage is only 1.49 V@10 mA cm−2, demonstrating high mass activity and work stability. This remarkable performance can be ascribed to the ultrathin 2D morphology and amorphous structure with abundant undercoordinated active sites of the materials. This finding offers a new insight and a rational design approach for highly efficient electrocatalysts utilizing 2D amorphous oxides.
The working principle of rechargeable zinc–air batteries is represented by eqn (3.1). When the battery is discharged, the anode undergoes oxidation, converting Zn metal into ZnO, while at the cathode, O2 participates in the oxygen reduction reaction (ORR) to produce OH−. Conversely, when the battery is charged, ZnO returns to Zn metal at the anode, and the OH− will produce oxygen via an oxidation reaction at the cathode. The charge/discharge reaction of rechargeable Zn–air batteries is reversible, where the reaction is represented by the following equation:
Total reaction equation:131
2Zn + O2 (g) ↔ 2ZnO, E = 1.66 V vs. SHE | (3.1) |
Electrochemical reactions of electrodes during discharge.
Zinc anode:
Zn + 4OH− ↔ Zn(OH)42− + 2e− | (3.2) |
Zn(OH)42− → ZnO + H2O + 2OH−, E = −1.26 V vs. SHE | (3.3) |
Air cathode:
O2(g) + 4e− + 2H2O → 4OH−, E = 0.4 V vs. SHE | (3.4) |
Electrochemical reactions of electrodes during charge.
Zinc anode:
ZnO + H2O + 2e− → Zn + 2OH− | (3.5) |
Air cathode:
4OH− → O2(g) + 4e− + 2H2O | (3.6) |
The advancement of economical and high-performance electrocatalytic materials as replacements for noble-metal-based catalysts and enhancing the electrocatalytic activity of oxygen is the goal of large-scale practical applications. Thus far, there are few reports of 2D oxide-based anode catalysts for Zn–air batteries. Li et al.132 developed a strategy for doping heteroatoms into bimetallic oxides by creating a 2D structure, followed by doping, mixing, and post-doping steps. The local coordination environments around the metal catalytic sites within the 2D materials were modified. Notably, the Co3+/Co2+ and Mn3+/Mn2+ ratios increased as the electronic structure was tuned, leading to further optimization of the adsorption and desorption of intermediates during the OER.133 A schematic illustration of the Zn–air rechargeable battery is shown in Fig. 9a. The LSV test results show that N/PCu0.1Co0.3Mn0.6O2/CNTs possess an overpotential of 160 mV at 10 mA cm−2 (Fig. 9b). DFT calculations showed that the adsorption energy of the *OH radicals was markedly decreased following non-metal doping. Specifically, adsorption of the second *OH species to form the *OOH species is RDS, which corresponds to the overpotential of 0.41 V. Compared to other catalyst models, Cu0.1Co0.3Mn0.6O1.8N0.2P0.2 composites have the lowest energy barrier for the RDS, indicating their superior catalytic activity for the OER (Fig. 9c). Moreover, the target catalyst exhibited good ORR performance (E1/2 = 0.82 V) and the zinc–air batteries using it as a cathode catalyst outperformed commercially available noble metal-based catalysts in terms of stability, peak power density, and voltage gap (Fig. 9d–h). Kumar et al.134 developed a low-cost and stable trimetallic oxide catalyst NiCoMoO4@rGO via a one-step hydrothermal method, where changes in the electrical environment of the active sites were modified via site-selective Mo substitution. Operando XAS, in situ XRD and DFT analyses revealed the crucial role of Mo atoms in reducing the overpotential and optimizing the energy barriers. In Zn–air batteries, the NiCoMoO4@rGO electrocatalyst exhibited a significantly higher specific capacity and corresponding energy density, proving an interesting concept for designing bifunctional electrocatalysts.
Fig. 9 (a) Schematic illustration of the rechargeable Zn–air battery; (b) the OER electrocatalytic performance of LSV curves in 1.0 M KOH; (c) the potential free energy profiles of the intermediate states in the OER on Co0.4Mn0.6O2, Cu0.1Co0.3Mn0.6O2. Cu0.1Co0.3Mn0.6O1.8N0.2, and Cu0.1Co0.3Mn0.6O1.8N0.2P0.2 nanosheets at zero potentials; (d) the power density and discharge curves using N/P-Cu0.1Co0.3Mn0.6O2/CNTs and IrO2-Pt/C as cathodes; (e) the charge and discharge curves; (f) digital photo of the LED lamp powered by two connected zinc-air batteries. (g) The cycling performance at 10 mA cm−2. (h) The difference of the voltage plateaus during charge and discharge for the first and last cycle.132 Reproduced with permission. Copyright 2023, Elsevier. |
Mi et al.135 reported hierarchical Co2FeO4 nanosheet arrays on an Fe foil carrier, which underwent a topotactic transformation process from the CoFe-LDH precursor, as bifunctional catalysts (Fig. 10a). Electrolysis was performed at a specific potential range, and gas chromatography and nuclear magnetic resonance techniques were utilized to qualitatively and quantitatively analyse products. After a constant voltage response for 1 h in CO2 saturated 0.1 M KHCO3, the faradaic efficiency of the CO product reached up to 92% at −1.0 V and 17% at −0.8 V. At the other end of the bifunctional membrane, the overpotential of Co2FeO4 at 10 mA cm−2 is 230 mV in 1.0 M KOH, which is smaller than Ir (300 mV). The good performance of Co2FeO4 could be due to the mass transfer ability and rich active sites originating from the nanoarray structure. DFT calculation further confirmed the Co–O–Fe sites form *COOH and *O intermediates in Co2FeO4 toward oxygen evolution and CO2 activation (Fig. 10b–e). The OER catalysts for coupling CO2RR under near-neutral conditions have traditionally relied on precious metals. Meng et al.26 developed a non-noble metal based OER electrocatalyst through one-step synthesis, and the obtained NiFe-HC electrocatalyst displays a distinctive flower-shaped plate morphology (Fig. 10f). Remarkably, the OER activity of NiFe-HC requires excess commercial IrO2 and Pt/C. Integrating a NiFe-HC anode with a CO2RR catalyst cathode in a CO2 electrolyzer under 2 M KHCO3, results in the selective conversion of CO2 to CO with a higher than 97% faradaic efficiency at 20 mA cm−2 (Fig. 10g). This facile approach to obtaining an inexpensive and efficient anode OER electrocatalyst could greatly boost the scalability and sustainability of the CO2RR for industrial applications.
Fig. 10 (a) Schematic diagram for the synthesis of Co2FeO4 nanosheet arrays on the Fe substrate. Gibbs free energies diagrams for (b) CO2RR and (d) OER on Co2FeO4 (311); Pathways for (c) CO2RR and (e) OER on Co2FeO4 (311).135 Reproduced with permission. Copyright 2020, John Wiley and Sons. (f) SEM image of NiFe-HC. (g) Experiment setup of the CO2 electrolyzer.26 Reproduced with permission. Copyright 2019, PANS. |
(1) Currently, the primary research of 2D oxide-based materials for the OER focus on transition metal oxides. These include oxides of Co, Ni, Mn, Fe, Cu, and Mo. The development of 2D oxide materials with high intrinsic catalytic activity, such as noble-metal oxide and bimetallic oxide nanosheets, is expected to extend the type of 2D metal oxides.136
(2) Although there have been many recent reports on the use of bulk oxides such as MnO2 and RuO2 for acidic OER, reports of the 2D structure of 3d/4d transition metal oxides are limited in acidic environments. The exploration of stable 2D oxide OER electrocatalysts under acidic conditions is crucial for achieving effective electrolytic hydrogen production.
(3) The strategies for modulating 2D oxides should be further enriched, such as the simultaneous loading of various single atoms or the direct synthesis of 2D oxides with high entropy atoms, to improve the catalytic performance and stability of the oxides.137,138
(4) The energy devices associated with the OER are not limited zinc–air batteries, and include alkali metal–air batteries such as lithium–air batteries, sodium–air batteries, potassium–air batteries, as well as ammonia oxidation, and methanol oxidation devices.
(5) Currently, the fabrication of 2D structures using 3d transition metal materials is relatively straightforward. In contrast, the synthesis of noble metal (such as Ir, Ru, Rh, and Au) based 2D structures remain extremely difficult, as noble metal atoms prefer to form 3D close-packed structures.139 Therefore, the synthesis of 2D oxides based on precious metal has potential for OERs in acidic media.140,141
(6) The OER process is greatly impacted by various factors, including the reaction and service conditions, as well as their interactions, such as local pH and its gradient distribution, and the types/concentrations of exotic ions.142 As reported, inactive anions (MoO42−, PO33−) have been employed as electrolyte additives in alkaline electrolyte due to their dissolvable property.143 Consequently, exploring the effect of inactive ions in 2D oxides is imperative for the design of efficient catalysts.
Overall, we believe that achieving efficient OER is a major challenge for the future exploration of new energy devices, and 2D oxides are critical nanomaterials for this process because of their unique structures and properties. Therefore, we expect that this review will contribute to the development of the energy conversion and storage fields.
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