Oxygen-deficient perovskites for oxygen evolution reaction in alkaline media: a review

Oxygen vacancies in complex metal oxides and specifically in perovskites are demonstrated to significantly enhance their electrocatalytic activities due to facilitating a degree of control in the material’s intrinsic properties. The reported enhancement in intrinsic OER activity of oxygen-deficient perovskites surfaces has inspired their fabrication via a myriad of schemes. Oxygen vacancies in perovskites are amongst the most favorable anionic or Schottky defects to be induced due to their low formation energies. This review discusses recent efforts for inducing oxygen vacancies in a multitude of perovskites, including facile and environmentally benign synthesis strategies, characterization techniques, and detailed insight into the intrinsic mechanistic modulation of perovskite electrocatalysts. Experimental, analytical, and computational techniques dedicated to the understanding of the improvement of OER activities upon oxygen vacancy induction are summarized in this work. The identification and utilization of intrinsic activity descriptors for the modulation of configurational structure, improvement in bulk charge transport, and favorable inflection of the electronic structure are also discussed. It is our foresight that the approaches, challenges, and prospects discussed herein will aid researchers in rationally designing highly active and stable perovskites that can outperform noble metal-based OER electrocatalysts.


Introduction
The global energy crisis associated with the increasing demand for energy as well as the rapid depletion of fossil fuels and carbon dioxide (CO 2 ) emissions associated with their use is one of the grand challenges facing humanity today. In fact, the International Energy Agency reported that the global energy demand is expected to rise to 26 TW by 2040 compared with 18 TW in 2013, corresponding to 44 Gt/year of CO 2 emissions [1]. This has motivated the global community to maximize deployment of renewable energy sources in order to meet the ever-growing energy demand in a sustainable manner [2,3]. Hydrogen (H 2 ) being a carbon-free energy carrier is an ideal sustainable energy source that can potentially replace non-renewable carbon-based fossil fuels due to its high specific energy [4][5][6]. Currently, the primary technologies that are used to produce hydrogen include partial oxidation, steam reforming of methane, and coal gasification.
However, these technologies involve the generation of significant amounts of greenhouse gasses, which is the main cause for global warming [7,8].
Amongst various progressive technologies, electrochemical water splitting driven by electricity produced from renewable energy sources, such as solar or wind energy, has emerged as an effective approach to sustainably produce high-purity hydrogen with zero carbon emissions [1,9]. Photochemical and photoelectrochemical water splitting materials have also seen an afresh interest in research over the past decade. However, they face limitations due to reactordesign predicaments [10,11]. Water splitting is composed of two half-reactions, including the hydrogen evolution reaction (HER), at the cathode (2H + (aq) + 2e − → H 2 (g) acidic, 2H 2 O + 2e − → H 2 + 2OH − alkaline) and the oxygen evolution reaction (OER) at the anode (H 2 O(l) → ½ O 2 (g) + 2H + (aq) + 2e − acidic, 2OH − → ½ O 2 + H 2 O + 2e − alkaline) [7]. Under standard conditions, water-splitting electrolyzers require a predicted thermodynamic potential of 1.23 V to drive the HER and OER half-reactions in alkaline and acidic media [12]. However, water splitting is kinetically an uphill reaction and entails sluggish reaction kinetics especially for the OER. This inflicts a considerable overpotential requirement (the difference between the thermodynamic potential and experimentally measured potential) to overcome the kinetic energy barriers and generate appreciable current densities [2]. Practically, the applied potentials required to drive water splitting processes are around 1.8-2.2 V, which consumes approximately 50% excess potential than the thermodynamic equilibrium value. The latter results in low energy conversion efficiencies which hampered the widespread application of water-splitting technology.
Achieving high electrocatalytic activities hence improved conversion efficiencies in water-splitting electrolyzers that can be realized by determining the origin of overpotential through fundamentally understanding the correlation between the electrocatalytic activity and the water-splitting reactions mechanism. The OER is the limiting reaction in water splitting and requires high overpotential because it involves 4-electron transfer steps [13,14]. An additional kinetic energy barrier is involved with every reaction step where the slowest step is regarded as the rate-determining step (RDS), and it can impose a significant increase in the overpotential required to drive the overall water-splitting reaction.
Alkaline OER proceeds via the oxidation of an adsorbed hydroxyl anion on the metal active site (M) to form an M-OH intermediate (Eq. (1)). Then, protons and electrons are removed from M-OH to form M-O (Eq. (2)). Subsequently, oxygen formation follows two possible pathways. In one route, M-O reacts with a hydroxyl anion to form hydroperoxide M-OOH followed by another proton-coupled electron transfer process to produce molecular O 2 (Eqs. (3) and (4)) [15][16][17][18]. In another route, a direct combination of two M-O intermediates produces O 2 (Eq. (5)) [19].
In practice, efficient and cost-effective electrolytic water splitting requires highly active and stable electrocatalysts that can minimize the required energy input (overpotential) [20]. Current state-of-the-art water-splitting technologies utilize noble metal-based electrocatalysts, including platinum (Pt) [21] and ruthenium dioxide (RuO 2 )/iridium dioxide (IrO 2 ), which show remarkable activities towards HER and OER, respectively, at low overpotentials [22]. However, the large-scale commercial use of noble-based electrocatalysts has been restricted due to their prohibitive high cost, scarcity, and longterm instability [21,23]. Therefore, significant research efforts have been directed towards developing robust, highly active, cost-effective, and stable electrocatalysts based on earthabundant elements for water splitting (OER and HER).
Perovskite oxides, a class of transition metal oxides, have emerged as promising electrocatalysts for alkaline OER due to their unique structural, electronic, ionic, and electrocatalytic characteristics [24][25][26]. The general chemical formula for perovskite oxides is ABO 3 , where A is typically occupied by cation with 12-fold coordination and B is occupied by a cation with 6-fold coordination with oxygen anions [27][28][29][30][31][32]. Other perovskite oxides with more complex structures include layered perovskites (A n + 1 B n O 3n + 1 ), A-site ordered double perovskite oxides (AA′B 2 O 6 ), and B-site ordered double perovskite oxides (A 2 BB′O 6 ) [33]. Compared with other electrocatalytic materials, perovskite oxides are inexpensive because they are based on earth-abundant elements, easy to synthesize, and environmentally benign [27,33,34]. Moreover, depending on the type of cations occupying the A and B lattice sites, a plethora of possible perovskite oxides with various stoichiometries can be generated with modulable crystal structures, electrocatalytic activities, electronic, and ionic properties [35]. Yet, despite their promise, perovskite oxides still require further enhancements to outperform noble-based metal catalysts due to their relatively low electronic conductivity.
Several experimental and theoretical studies demonstrated that the catalytic activity of perovskite oxides can be intrinsically modulated through the inductive alteration of oxygen nonstoichiometry to generate oxygen-deficient structures for a myriad of applications [35][36][37][38][39]. Table 1 summarizes various electrocatalysts made of oxygen-defected perovskite oxides that were reported in the literature for OER. Oxygen defects can bring about substantial electrocatalytic performance improvements by (1) tuning the electronic structure and charge transfer, (2) promoting the exsolution of secondary active surface phases, and/or (3) providing moderate adsorption/ desorption behavior of reaction intermediates during water splitting. When the A and B positions are replaced, perovskite oxides maintain their structural stability through undergoing crystal lattice deformations caused by A-site and B-site ionic radii mismatch along a specific direction to construct crystallographic structures (e.g., tetragonal, orthogonal, or trigonal). Thus, oxygen vacancies can be generated on perovskite oxides to a certain extent without rendering a collapsed structure [33].
Reportedly, oxygen vacancies promote the e g -filling status of the B-cation to alter the electron configuration of the metal cation with a high-spin-state electron occupying the e g orbital [40]. Compared with the π-bonding t 2g orbital, the σ-bonding e g orbital strongly overlaps with the oxygen-containing adsorbates, which facilitates charge transfer between the transition metal cation and the reaction adsorbates (M-OH, M-O, M-OOH, H 2 O), hence accelerating the water splitting kinetics [62]. Generally, optimal OER performance could be obtained by perovskite oxides with an e g occupancy close to unity (~1.00) [1]. Besides e g filling, oxygen defects can upshift the oxygen p-band center relative to the Fermi level to promote hybridization and  [56] high covalency of the O p orbitals and transition metal d orbitals [1,63]. The O p-band should be neither too close nor too far relative to the Fermi level [64]. Perovskites with an O p-band very near the Fermi level undergo surface degradation and leaching of the A-site elements and tend to become amorphous on the surface under OER conditions, thus providing poor durability. On the other hand, when the O p-band is too far from the Fermi level, the perovskites remain crystalline and provide prolonged stability however at very low current densities. At high current densities, the B-site cations, typically recognized as OER active sites, are leached [64][65][66]. The O p-band position can be optimized via tuning the concentration of oxygen defects on the perovskite surface. The aforementioned configuration is generally reported to substantially increase the intrinsic OER activity by lowering the charge-transfer gap between the reaction adsorbates and the metal active site, contributing to higher conductivity [1,64,67]. Furthermore, in some cases, oxygen-deficient perovskite oxides tend to have higher structural distortion compared with their pristine counterparts. Specifically, it was reported that layered perovskite oxide NdBaMn 2 O 5.5 (prepared via reductive annealing under hydrogen) exhibited a much higher distorted structure compared with pristine Nd 0.5 Ba 0.5 MnO 3-δ due to the Jahn-Teller effect and the ordering of the electronic orbitals [1]. A similar finding was reported on an oxygen-deficient Ca 2 Mn 2 O 5 perovskite (treated via hydrogen gas) where the Jahn-Teller effect resulted in a more distorted structure and larger cell volume for this oxygen defected perovskite structure than of the simple two unit stacked cells of CaMnO 3 [40]. This distortion arising upon removing lattice oxygen atoms from the aforementioned perovskite structures promotes the adsorption of key OER reaction recipes, H 2 O and OH − , into the oxygen vacant sites [1,33,40].
To this end, extensive efforts for inducing oxygen defects on perovskite oxides as a new class of highly active catalysts for alkaline electrochemical water splitting have been extensively reported in the literature. In this review, synthesis strategies reported to generate oxygen vacancies in a myriad of perovskite oxides and their effect on surface morphology, crystal structure, surface chemistry, and hence electrocatalytic OER activity, as well as commonly used characterization techniques to detect oxygen vacancies, are discussed. A detailed insight is provided on the role of oxygen vacancies on modulating the electronic structure, adsorption/dissociation energies of reaction intermediates, and their consequent effect on OER activities. Finally, future suggestions are discussed to propose new directions that can aid researchers towards the rational development of novel high performance and stable materials for OER.

Synthesis methods
As previously discussed, oxygen defects can effectively enhance the electrocatalytic OER activity of perovskite oxides  [61] through modulating the surface morphology, electronic structure, and thus their electrocatalytic properties. Various methods have been reported in the literature to preferentially tune the degree of oxygen site defects in the perovskite lattice via in situ or post-synthesis treatments. This section will provide a brief summary of synthesis approaches that have been commonly adopted to induce oxygen vacancies in perovskite oxides. These methods mainly involve gaseous hydrogen reduction, thermal annealing, and elemental doping, whilst very little work has also been reported using other methods, such a plasma treatment, solid-state reduction, and wet-chemical reduction. The degree of which the synthesis method and the process parameters affect the surface morphology, crystallinity, and electrocatalytic OER performance was highlighted.

Reduction
Many studies report the incorporation of oxygen vacancies in perovskite oxides by the facile but very effective hydrogen reduction method due to the high reproducibility of the hydrogen gas [68,69]. This method can generate oxygen defects either at mild or elevated temperatures [70]. Typically, under a suitable reduction atmosphere, namely H 2 , due to the high reducibility of the H 2 gas, the B-site metal cations of the perovskite oxide are exsolved to form metallic nanoparticles distributed on the surface of the as-prepared pristine perovskite oxides. Consequently, the reduced perovskite oxide will exhibit an enhanced electronic conductivity due to the high conductivity of the metallic particles, which in turn enhances the OER kinetics [44]. Moreover, since oxygen defects can be generated at relatively mild/low-temperature conditions, this avoids sintering or coalescence of the perovskite oxide during the treatment process. This also provides easier control of the reaction kinetics during the synthesis process [40]. However, under excessive reduction of annealing conditions, aggregation of the perovskite oxide nanostructures could occur, leading to a collapsed structure and degraded OER activity [51]. In a representative work by Kim et al., a single crystalphase oxygen-defected Ca 2 Mn 2 O 5 perovskite was synthesized using a low-temperature reduction approach. Ca 2 Mn 2 O 5 was prepared through annealing pristine CaMnO 3 (prepared via a sol−gel process) under 5% H 2 /Ar atmosphere at 350°C for 3 h [40]. Due to the mild reduction conditions used, no sintering or agglomeration was observed post-annealing. Moreover, Mn 4+ ions in CaMnO 3 were reduced to Mn 3+ which could easily bond with OH − . Reduction annealing has also resulted in crystal structural transformations, where a single crystal phase orthorhombic Ca 2 Mn 2 O 5 coordinated with square pyramid subunits between oxygen and manganese was formed, compared with CaMnO 3 , which had six-coordinated octahedral subunits connected by six oxygen atoms at the corner sites (Fig. 1a) . The unit cell structure of the oxygen-deficient Ca 2 Mn 2 O 5 resulted in the formulation of a molecular level porosity at its internal structure on the oxygen-vacancy sites beyond its apparent structural porosity, which facilitated the adsorption of OH − . The aforementioned modifications ultimately contributed towards enhancing the OER kinetics. OER activity measurements indicated that the onset potential in an alkaline 0.1M KOH solution for defective Ca 2 Mn 2 O 5 perovskite was 1.5 V (vs RHE), compared with its pristine counterpart CaMnO 3 (1.6 V).
Moreover, an oxygen-deficient Sr 2 Fe 1.3 Ni 0.2 Mo 0.5 O 6 − δ double perovskite was reported by Zhu et al. with enhanced OER activity, delivering a current density of 10 mA cm −2 at 360 mV compared with its pristine counterpart (404 mV) in an alkaline 0.1M KOH solution [44]. The defected perovskite was synthesized via annealing pristine Sr 2 Fe 1.3 Ni 0.2 Mo 0.5 O 6 − δ under different atmospheres (Ar, 5% H 2 /Ar and H 2 ) at 700°C for 3 h. The optimum reduction conditions, showing the highest OER activity, were under 5% H 2 /Ar as shown in Fig. 2b. During the annealing process, the metal cations were reduced resulting in mixed-valence states (Mo +5 , Mo +6 , Ni +3 , Ni +2 , Fe +2 , Fe +3 , and Fe +4 ). Moreover, the presence of metallic Fe 0 and Ni 0 was detected which improved the electronic conductivity of the catalyst due to the high conductivity of the metallic particles. Post-reduction, the as-synthesized pristine Sr 2 Fe 1.3 Ni 0.2 Mo 0.5 O 6 − δ perovskite tetrahedral lattice structure expanded as a consequence of the partial reduction of B-site cations. Furthermore, due to the high reducibility of the hydrogen gas, phase decomposition of the parent pristine perovskite occurred resulting in the exsolution of new Fe-Ni a l l o y a n d S r 4 Fig. 2c and d. As reported, the enhanced OER activity enhancement in reduced Sr 2 Fe 1.3 Ni 0.2 Mo 0.5 O 6 − δ is directly related to the aforementioned modifications related to the formation of new active phases and more exposed active sites.
Besides gaseous hydrogen reduction, oxygen defects were also created via solid-state reduction of (Sr 1 − x Ba x )FeO 2 perovskite using solid reagents that can thermally release hydrogen (CaH 2 , NaH) and wet-chemical reduction with H 2 O 2 aqueous solution on La 0.8 Sr 0.2 CoO 3 − δ (LSC) [37].

Doping
The substitution of A and/or B site atoms using low valency dopants (e.g., La, Sr, Mg, Ba, Ca) is an effective approach to creating oxygen vacancies. Upon removing a cation atom from the perovskite crystal structure, a negative charge is created resulting in an unbalanced atmosphere. To maintain charge neutrality, an oxygen vacancy is formed by releasing an oxygen atom from the perovskite lattice [33]. The concentration of oxygen vacancies is highly dependent on the degree of substitution and the type of elemental dopant used, which directly affects the formation energy of the oxygen vacancies. Typically, low formation energy results in a higher degree of oxygen defects. Sr and Ca are the most favorable and commonly used alkaline-earth metals to create oxygen vacancies in ABO 3 -type perovskite oxides [3,70]. She  /O − ratio indicates the formation of highly oxidative oxygen species and is a direct measure of surface oxygen vacancies. Moreover, Fe with different oxidation states (Fe 4+ , Fe 3+ , Fe 2+ ) was detected on the surface and increased with increasing Sr +2 content. Structural analysis revealed that the substitution of La 3+ by Sr 2+ promoted the lattice structure to change from an orthorhombic structure to a cubic structure. However, in the case where the Sr +2 dopant fraction was 1.0, a tetragonal lattice was adopted instead of a cubic lattice. Amongst the five samples, La 0.2 Sr 0.8 FeO 3 − δ (LSF-0.8) exhibited the highest activity towards OER in a 0.1M KOH alkaline media, where the overpotential at 10 mA cm −2 current density was 370 mV compared with undoped La FeO 3 − δ (510 mV) (Fig. 2a). The cubic structure and the presence of abundant oxygen vacancies both contributed towards enhancing the OER performance [41]. Kim   On the other hand, Cu doping resulted in the transformation of the orthorhombic NdBa 0.75 Ca 0.25 Co 2 O 5 + d structure to a tetrahedral structure due to the large difference between the ionic radii and the electronic structure of Cu and Co. Based on morphological analysis, the agglomerated NdBa 0.75 Ca 0.25 Co 2 O 5 + d morphology was precluded upon doping as shown in the SEM images in Fig. 2b-f. Moreover, the metallic substitutions resulted in the generation of porous structures where NBCCFe exhibited the highest exposed surface area (2.8 m 2 g −1 ) compared with NBCC (1.9 m 2 g −1 ), NBCCCu (1.8 m2 g −1 ), NBCCNi (1.9 m 2 g −1 ), and NBCCMn (2.2 m 2 g −1 ).
In contrast to thermal annealing/calcination, doping via hydrothermal synthesis requires low processing temperatures (normally below 300°C). This allows for precise control of the particle size, shape, and crystallinity of perovskite oxide via tuning the synthesis process conditions. Moreover, due to the mild temperature conditions used via this synthesis route, agglomerated free powders can be produced. Thus, electrocatalysts with high specific area and unique favorable morphologies towards OER can be generated [3,71].

Thermal treatment
Calcination/thermal annealing under low oxygen partial pressures or vacuum at elevated temperatures is a fairly simple and direct approach to produce non-stoichiometric perovskite oxides [72]. However, catalysts produced using this method can contain agglomerated large particles of various sizes and morphologies, as well as phase impurities [3]. Moreover, the high calcination temperatures associated with this synthesis route can result in sintering of the perovskite oxide catalyst which may result in a poor microstructure, reduction in surface area and coarsening of the catalyst powders, hence low electrochemical OER performance [73]. Therefore, the catalyst powder post-calcination is typically refined or ball-milled to separate the particle aggregate and obtain a catalyst powder with enhanced particle size distribution [52]. Miao et al. studied the role of oxygen vacancy concentration in enhancing the electrocatalytic OER activity of PrBaCo 2 O 6 − δ perovskite. Two oxygen-deficient perovskites with different oxygen vacancy concentrations (δ) of 0.25 (PrBaCo 2 O 5.75 ) and 0.5 (PrBaCo 2 O 5.5 ) were synthesized. The catalysts were produced by sintering PrBaCo 2 O 6 − δ powders (produced via a sol-gel method) in air at 1000°C for 10 h followed by annealing in pure N 2 at 250 and 600°C for 30 min to obtain PrBaCo 2 O 5.7 5 and PrBaCo 2 O 5. 5 . Interestingly, higher oxygen vacancies (δ = 0.5) have detrimentally affected the intrinsic OER activity of the cobalt oxide-based perovskite. PrBaCo 2 O 5.75 depicted faster OER kinetics in 1M KOH alkaline media with a low overpotential of 360 mV to achieve a current density of 10 mA cm −2 as compared with PrBaCo 2 O 5.5 (420 mV). As the oxygen vacancy introduced, both PrBaCo 2 O 5.75 and PrBaCo 2 O 5.5 displayed similar particle morphologies as shown in Fig. 3a and b. However, at (δ = 0.5), as the oxygen atoms were dislodged from the octahedral Co 4+ O 6 in PrO 1-δ layers, a pyramidal Co 3+ O 5 was formed, resulting in an alternative arrangement of pyramidal Co 3+ O 5 and octahedral Co 3+ O 6 within the PrO 1 − δ layers (Fig. 3c). Consequently, this ordered structure reduced the cobalt oxidation states and caused a spin-state transition from high-spin to low-spin states for the cobalt ions, which both significantly increase charge resistance hence hampering the OER kinetics [38].
In another work by Chen et al., an oxygen-deficient BaTiO 3 − x perovskite denoted as (BTO-1300VAC) was synthesized using a sol-gel method followed by vacuum thermal treatment at 1300°C for 2 h [49]. For comparison purposes, BTO-950AIR was produced via calcinating pristine BaTiO 3 in air at 950°C for 2 h. Moreover, benchmark IrO 2 nanoparticles (denoted as Ir-550) were synthesized via a sol-gel method followed by calcination in oxygen at 550°C for 2 h to directly compare its OER activity with the as-synthesized oxygen-deficient perovskite. The measured surface areas of BTO-1300VAC and IrO 2 were 24.7 and 21.1 m 2 g −1 , respectively. Post-annealing, small agglomerations of the BaTiO 3 − x particles were observed due to the high-temperature conditions used in the calcination process (Fig. 3d). On the other hand, BTO-950AIR formulated highly agglomerated particles due to the bonding reaction in air at 950°C (Fig. 3e). Moreover, in contrast to BTO-950AIR and BaTiO 3 which exhibited pure tetrahedral phases (t-BaTiO 3 ), mixture of tetragonal and hexagonal BaTiO 3 (h-BaTiO 3 ) phases was exsolved upon annealing. Results of electrochemical OER measurements in 0.1 NaOH electrolyte solution showed that the BTO-1300VAC sample generates larger current density than Ir-550 at relatively low potential (< 1.6 V). However, the measured current density for Ir-550 at high potentials (> 1.6 V) rapidly increases and exceeds that for BTO-1300VAC. This was attributed to the higher conductivity and active site density of IrO 2 over perovskite oxides. BTO-950AIR showed a very low electrocatalytic OER activity with an onset of around 1.8 V.

Characterization techniques for oxygen vacancies
As will be discussed in detail in Section 4, the presence of oxygen vacancies results in notable changes in the performance of a perovskite electrocatalyst. Such enhancements in electrocatalytic activities emerge from both structural and electronic modulations to the material. For instance, the omission of several surface and sub-surface oxygen vacancies can lead to structural instabilities and phase changes-as will be discussed later. Crystallographic techniques, such as XRD, can indirectly probe the presence of oxygen vacancies in structurally complex perovskites upon slight phase expansions or compressions that result in a more stable configuration. Furthermore, it has been found that amongst the main changes that perovskites undergo upon the induction of oxygen vacancies, modulation in electronic and magnetic properties as a result of metallic-oxygen species near the surface and charge neutrality effects, respectively, are witnessed. This section will briefly overview some of the most prominent and advanced characterization techniques employed in literature to effectively identify the presence of oxygen-deficient perovskites. It is worth noting that the techniques discussed have been utilized for the characterization of oxygen vacancies in a myriad of transition metal oxides (TMOs); however, this section will solely review relevant endeavors in identifying oxygen-deficient perovskites.
The ordering of oxygen vacancies has been investigated in TMOs due to the observed influence that vacancy ordering has on magnetic and transport properties. Advanced microscopy using high resolution transmission electron microscopy (HRTEM) and scanning transmission electron microscopy (STEM) can be utilized to directly probe evident surface structural distortions as a result of surface lattice realignment upon the induction of oxygen vacancies. Klie et al. reported the use of high-angle annular dark-field (HAADF) STEM technique to convey patterned ordering of oxygen-deficient La 0.5 Sr 0.5 CoO 3-ẟ (LSCO) on SrTiO 3 (STO) and LaAlO 3 (LAO) substrates in the [74] orientation [75]. Oxygen vacancies were indirectly found to be ordered in LCO thin films grown on a (001) oriented STO substrate, whereby the contrast is resulting from oxygen vacancy ordering [76]. This is presented in Fig. 4a. Furthermore, Fig. 4b shows enlarged La-La distances as a result of the induced oxygen vacancy planes.
The induction of oxygen vacancies in pristine Pr 0.5 Ba 0.5 MnO 3 − ẟ (PBM) by direct annealing in H 2 was reported by Ciucci et al., and clear changes to the crystalline phase of the reduced H-PBM are conveyed through XRD comparison between both samples [46]. Phase transition from the cubic structure with randomly distributed Pr/Ba sites to the ordered one can be depicted from Fig. 4c and d, respectively. Reduction of the pristine perovskite can also result in a lowering of transition metal ions to a lower valence states and the decomposition of the original coupled material into its constituent oxide and metals. However, the latter of this can be ruled out in the case of H-PBM based on XRD patterns not showing phases of the standalone components of the perovskite. XRD technique is one of a few characterization methods that was reported in several studies to determine the presence oxygen vacancies in perovskites [77,78]. Upon reduction-and consequent introduction of oxygen vacancies-peak shifts to lower angles infer an increase in out-of-plane lattice parameter (c) and cell volume. This is attributed to atomic underbonding orbitals located in nonbinding orbitals of transition metals due to the presence of large number of electrons upon oxygen vacancy formation [70].
Neutron powder diffraction (NPD) is another effective approach for depicting oxygen vacancies in perovskites. The neutrons utilized in NPD technique have higher penetration depth than the penetration depth of X-rays, which allows for bulk characterization and a higher sensitivity towards oxygen atoms. This proves effective for studying oxygen-deficient perovskites [79][80][81][82]. For instance, Chen et al. employed the  Rietveld method in NPD to exemplify potential active sites in oxygen-deficient BaTiO 3 [49]. It was also used to study the oxygen atom site occupancies in structural models as free variables in the refined spectra. It was thus determined that tetragonal phases did not promote vacancy formation; however, the oxygen site occupancies in hexagonal BaTiO 3 phase refined to 0.92(3)-representing BaTiO 2.76 . Such detailed phase analysis is essential for oxygen vacancy engineering, since as will be discussed later, not all phases have the same enthalpic favorability towards vacancy formation and represent different binding energies towards reaction intermediates.
X-ray photoelectron spectroscopy (XPS) is perhaps the most employed characterization method for indirectly determining the presence of oxygen vacancies in the surface of oxide-based materials. XPS works by determining the surface electronic and chemical states of a material through effectively measuring the contrast in outermost layer electrons and their atomic cores' binding energies. A reduced material with oxygen vacancies tends to always have surface oxygen vacancies since reduction initially attacks surface lattice oxygen, and consequently through the deconvolution of the O 1s spectra of a reduced material, the determination of vacant sites can be inferred. Due to charge neutrality restrictions, neighboring cationic metallic sites to the oxygen vacancy site lower their valence oxidation states. Yang et al. fabricated Sr 2 Fe 1.3 Ni 0.2 Mo 0.5 O 6 − ẟ (SFNM) with oxygen vacancies through calcination in argon (Ar), 5% H 2 /Ar, and H 2 atmospheres [44]. The resultant samples were denoted SFNM-Ar, SNFM-5%, and SNFM-H 2 , respectively. XPS results presented in Fig. 5 show the different degrees of oxygen vacancies the materials possess, which was directly correlated to the order in OER performance. The deconvoluted peaks of the Ni 2p, Fe 2p, and Mo 3d spectra in the modified SFNM samples of Fig. 5a-c show a clear lowering of oxidation states upon reduction in H 2 and 5% H 2 /Ar atmospheres. This is in order to cope with surface charge electroneutrality conditions for more thermodynamic surface-stable reduced structure. Furthermore, the reduction of B-site ions (Ni, Fe, and Mo) to a lower oxidation state leads to a decrease in the binding energy of the lattice oxygen, whilst the oxygen vacancies greatly enhance the binding energy of the lattice oxygen. Figure 5d shows two main deconvoluted peaks for the O 1s spectra of different SFNM samples. Essentially, a peak at 529 eV corresponds to lattice oxygens, and the second peak at a binding energy of 531 eV corresponds to adsorbed oxygen species (i.e., O 2 − , O − ), which is an indirect identifier of oxygen The presence of oxygen vacancies in a perovskite leads to the trapping of unpaired electrons, which can be detected through electron paramagnetic resonance (EPR). EPR as a characterization technique can shed light on both bulk and surface unpaired electrons. However, a disadvantage in using EPR as a sole method to determine the presence of oxygen vacancies lies in the fact that it innately is unable to differentiate between oxygen vacancies and other types of defects that can lead to the same unpairing effect of electrons. Eichel performed a thorough investigation of several transition metaldoped perovskites through the analysis of high-frequency EPR [83]. The presence of oxygen deficiencies in all the studies materials was confirmed by g-parameters close to 2.00. For instance, Mn-doped Bi 0.5 Na 0.5 TiO 3 EPR analysis found a gparameter of 2.0015. Numerous findings of g-parameters approaching 2.00 for oxygen-deficient perovskites and transition metal oxides (TMOs) co-confirmed with other oxygen vacancy characterization techniques have been reported in recent years [84][85][86]. Acquiring information pertaining to molecular vibrations and rotations via Raman spectroscopy is another tool continued to be adopted for identifying oxygendeficient materials and perovskites in general [87][88][89][90].
Changes in lattice molecular vibrational nodes due to novel bond configurations give rise to Raman shifts. Oxygen vacancies can thus result in observed Raman shifts or the creation of new peaks. Moreover, anionic vacancies tend to modify band structures-as can be seen from DFT band structure calculations of oxygen-deficient materials. Such band structure changes can lead to potential alternate paths for excited electron generation and recombination-which occurs from lightdirected electron excitation during photoluminescence (PL) readings [85,91]. Peak position and intensity of the PL spectra show easily identifiable changes upon such electronic modulations from oxygen vacancies [92].
The aforementioned analyses show a varying degree of accuracy and reliability in identifying oxygen vacancies in perovskites, and oxygen-deficient TMOs generally. Nevertheless, based on the most prominently utilized and accepted techniques, XPS and STM are generally used to detect surface chemistry changes and physical imaging of oxygen vacancies, respectively. Although the creation of surface oxygen vacancies is more important than bulk vacancies in photocatalytic and electrocatalytic applications, some applications may find bulk vacancies important. For the latter applications, both XPS and STM may not be very useful since they characteristically capture the first few layers of a material's surface. It is generally a common practice to perform at least two characterization techniques for an accepted claim of oxygen vacancies. Moreover, phase characterization techniques, such as XRD, are only useful for identifying oxygen deficiencies when the target material is crystalline in nature. Therefore, factoring for the fact that every technique exhibits some form of limitation, it is considered best practice to use multiple characterization techniques on the same material to undoubtedly prove the presence of oxygen vacancies.

Advantageous intrinsic effects of oxygen vacancies in perovskites
Induction of oxygen vacancies in perovskites has been reported to advantageously enhance the physicochemical properties directly related to lower overpotentials for electrochemical OER through water splitting. Literature shows a clear sparked increase in interest towards oxygen-deficient perovskitesnot only due to an apparent improvement in performance. Oxygen vacancies in perovskites are amongst the easiest anionic or Schottky defects to be induced and reasonably controlled due to their low formation energies. Other types of defects, such as interstitial or Frenkel defects, tend to be more challenging to control. Furthermore, due to a growing interest in oxygen-deficient metal oxides, both experimental and computational studies have been devoted to mechanistically investigate how oxygen vacancies alleviate an initially high OER overpotential for a pristine sample. Quintessentially for perovskites, three main areas were found to be modulated upon induction of oxygen vacancies-namely, changes in the relaxed configuration structure, improvements in bulk charge transport, and favorable inflection of the electronic structure.
In their recent work, Tavassol et al. synthesized an oxygendeficient Sr 2 − x Ca x Fe 2 O 6 − ẟ perovskite for tunable surface reactivity towards OER [93]. This was undertaken by changing the A-site composition (A = Sr 2 − x Ca x ) and the oxygen vacancy content (ẟ). Figure 6a shows a clear direct proportionality between the degree of oxygen vacancy (ẟ) and the reduction in OER overpotential. Similar findings have been reported with other oxygen-deficient perovskites. For instance, Fig. 6b also shows a direct correlation between the most oxygen-deficient La 1 − x Sr x CoO 3 − ẟ and the highest OER activity for the optimum material SrCo 2.7 [42].
Researchers have utilized so-called "activity descriptors" for predicting the intrinsic behavior of transition metal oxides (TMOs) and their activity towards OER. Essentially, two main descriptors that are related to oxygen vacancies have been frequently investigated to merit their utilization; they are the e g occupancy and the difference between the metal dband center and the oxygen p-band center (ΔE d − p ) [94,95]. Both these descriptors can be thought of as modulators of electronic structure. In their recent and very thorough work, Kim et al. primarily focused on investigating the relationship between oxygen vacancies, ΔE d − p , and apparent overpotential for Sm 0.5 Sr 0.5 CoO 3 − ẟ (SSC) [96]. The authors were motivated by the fact that previous studies solely focused on the effect of ẟ on catalytic activity without much consideration of the electronic structure of cobalt in SSC. They performed a detailed study using X-ray absorption spectroscopy (XAS) characterization for recording changes to the oxidation state of Co upon different degrees of oxygen vacancies (ẟ) were induced, and density functional theory (DFT) calculations to reveal more accurate reaction pathways. Early TMs (i.e., V, Mn, and Cr) show higher M d compared with the  [97]. Thus, OER performance can be increased by increasing M d which in effect decreases the ΔE d − p . This relationship is displayed in Fig. 7a. The ẟ value was varied between 0 and 0.2 (with 0.1 increments), and the content of oxygen vacancies in the oxygen-deficient SSC samples was determined using iodometric titrations. DFT analyses confirmed that OER activity was improved upon vacancy introduction due to lifting the metal d-band centers (M d ) and reducing (ΔE d − p ). Figure 7b shows that the OER onset potential was found to decrease from 1.62 to 1.54 V (vs RHE) at 1 mA/cm 2 with an increase in oxygen vacancy content (ẟ). Furthermore, a DFT investigation pertaining to the placement of the oxygen vacancies was performed, whereby as can be seen from Fig. 7c, the overpotential is lowest when the anionic vacancy is in the first layer. This is since ΔE d − p is lowest when oxygen vacancies are induced in the top layer. The reaction coordinate diagram in Fig. 7d shows how the placement of oxygen vacancy in the topmost layer lowers the thermodynamic barrier for each intermediate step-namely, the rate-determining step (RDS). Similar findings of increased OER activity corresponding to a decrease in ΔE d − p have been reported over the years [98,99].  [96] with permission from the American Chemical Society, Copyrights 2020 Suntivich et al. described the e g occupancy descriptor to strongly affect the rate-determining step (RDS) in OER [62]. The authors reported that Ba 0.5 Sr 0.5 Co 0.8 Fe 0.2 O 3 − ẟ (BSCF) yielded an order of magnitude more prominent intrinsic activity than benchmark IrO 2 for OER in alkaline 0.1M KOH media. The formulation of this optimized material was undertaken by systematically examining ten different transition metal oxides (TMOs). A notable finding of an apparent volcano-plot pattern emerged relating the occupancy of the e g orbitals (i.e., dz 2 , dx 2 -y 2 ) in surface TM cations and occupancy of the 3d electrons. The peak of the volcano plot shows that an e g occupancy close to unity, reflecting high covalency between TM-Oxygen bonds, corresponds to optimum OER activity. This is presented in Fig. 8a, whereby the performance of BSCF is close to the apex of the volcano plot. Suntivich argues that in the case where the e g occupancy is less than unity, the formation of the peroxide ion from preceding oxyhydroxide would be the RDS. In contrary, if the e g occupancy is greater than unity, the formation of O-O bonds in the OOH* OER intermediate would be the RDS. The relevance of this comes in the finding that introduction of oxygen vacancies in perovskites actually brings the e g occupancy close to unity. For instance, Wu et al. found that oxygen-deficient CaMnO 3 perovskite samples showed activity enhancements up to a certain point-e g filling approaching 1 [36]. They also related this enhancement to a dual improvement in intrinsic conductivity of the material. The optimum Yb-doped and oxygen-deficient Yb 0.1 Ca 0.9 MnO 3 sample showed 100 times higher activity than the original undoped and un-reduced CaMnO 3 sample. This was attributed to optimal Mn e g filling state as high as 0.81 and better conductivity. Similarly, the activity of Mg-doped oxygen-deficient LaNiO 3 (LNO) (d) Relationship between OER and HER activity, both of which are defined as the potential to deliver a current density of 0.5 mA/cm 2 of oxide. The error bar is the standard deviation calculated from three separate experiments. The dashed volcano line is displayed only for reference. Reproduced from Ref. [1] with permission from the American Chemical Society, Copyright 2018 nanofibers fabricated through electrospinning was shown to outperform the pristine LNO counterpart [60]. Typically, Ni 2+ presence in LNO leads to an e g occupancy greater than unity. However, STXM-XANES analysis of the Mg-doped LNO (LNMO) sample showed an increase in the Ni 3+ state, whereby an increased Ni 3+ /Ni 2+ ratio could lead to an e g occupancy approaching unity and enhancing OER activity. Moreover, Ciucci et al. reported the HER activity of oxygen-deficient NbBaMn 2 O 6 − ẟ (NMB) fabricated via direct hydrogen reduction treatment [1]. The optimum oxygen-deficient NbBaMn 2 O 5.5 (NMB 5.5 ) achieved a better overall water splitting stable activity at large potentials (> 1.75 V) compared with benchmark IrO 2 and RuO 2 catalysts. Figure 8b-d shows NMB 5.5 yielding the most favorable alkaline HER and OER activity compared with other NMB fabricated perovskites, ascribed to near unity e g occupancy, along with favorable ΔE d − p levels and structural distortions.
It has also been found that some activity descriptors, such as e g occupancy and ΔE d − p levels, can be impacted through modulation of lattice strains, especially in perovskites. Although most studies tend to discuss oxygen deficiencies and lattice strains in perovskites independently, Liu et al. found a symbiotic relation between the two [78]. They expressed these effects intrinsically through monitoring e g occupancies in oxygen-deficient La 0.7 Sr 0.3 CoO 3 − ẟ (LSC) thin films grown atop single crystal substrates (SrTiO 3 (STO) and LaAlO 3 (LAO), with in-plane tensile and compressive strain, respectively). Experimental results and DFT calculations illustrated that higher oxygen deficiencies in LSC/STO samples corresponded to lower OER activities, compared with LSC/ LAO with fewer vacancies and higher compression strains. This is an example of disadvantageous synergy between tensile strains in perovskites facilitating oxygen vacancies, which leads to higher e g occupancies and ΔE d − p levels in the LSC/ STO sample and results in diminished electrochemical activity. On the contrary, Petrie et al. showed that 4.2% epitaxial/ tensile strains in strontium cobaltite to enhance oxygen deficiencies at benign synthesis conditions and lead to an orderof-magnitude improvement in intrinsic OER activity [100]. Such modest tensile strains allowed unconventionally low anionic concentrations not found in the unstrained bulk cobaltite and lead to an increased Co 3+ ratio which admits the e g occupancy closer to unity.
Based on the discussion thus far, an ideal OER perovskite should have an e g value approaching unity, but also high conductivity [62]. However, most pristine oxides do not have both ideal e g occupancies and good conductivities. Wu et al. related the 100 times increase in OER activity of Yb 0.1 Ca 0.9 MnO 3 treated at 350°C (CYMO-350), compared with pristine CMO, to both the enhancement of e g occupancy and conductivity [36]. This was achieved by sequential doping and hydrogen treatment at elevated temperatures. Figure 9a, b represents the OER polarization curves and the identified e g occupancy vs. conductivity of the representative samples investigated. Similar findings have been numerously reported whereby the induction of oxygen vacancies has led to an apparent substantial increase in perovskite's conductivity. For example, Shao et al. reported a silicon-incorporated perovskite as an OER material, which showed a 12.8-fold increase in oxygen diffusivity and two orders of magnitude increase in conductivity-matching the attained 10-fold enhancement in intrinsic OER activity [48]. Previously reported pristine SrCoO 3 − ẟ (SCO) with relatively high and stable OER performance was modified with silicon. Pristine SCO showed a conductivity of 2 S cm −1 , whilst a remarkable value of 198 S cm −1 was recorded for the silicon modified oxygendeficient sample (Si-SCO). The comparative alkaline (0.1 M KOH) OER polarization curve in Fig. 9c corresponds to Tafel slope values of 76 and 66 mV dec −1 for pristine SCO and Si-SCO, respectively. This is also a good indication of improved OER kinetics since lower Tafel slopes imply significantly increased currents at only moderate increments of overpotential. Furthermore, Ciucci et al. developed a novel bifunctional perovskite catalyst towards OER and ORR, whereby Nb was substituted in the Mn site of CaMnO 3 (CMO) to yield CMNO and inducing oxygen vacancies in the structure upon hydrogen treatment (H 2 -CMNO) [45]. Hydrogen treatment was found to not only affect the phase structure of CMNO, but it also enhanced the concentration of oxygen vacancies based on XPS analysis. This has contributed to more effective electronic transport through conductivity enhancement between CMO (3.33 × 10 −3 S m −1 ) and H 2 -CMNO (2.19 × 10 −2 S m −1 ). Figure 9d shows the substantial difference in mass activity as a performance parameter between pristine CMO, CMNO, and the highly oxygen-deficient H 2 -CMNO. Other works showing OER performance exceeding that of benchmark IrO 2 have been reported over the years [101,102].
Shao et al. systematically investigated structural distortions of La 1 − x Sr x FeO 3 − ẟ (LSF) upon varying degrees of Sr-doping in LaFeO 3 − ẟ (LF) which induced proportional increases in oxygen deficiencies based on XPS analysis [41]. The content of Sr-doping was varied from x = 0, 0.2, 0.5, 0.8, and 1.0, with the alkaline (0.1 M KOH) OER performance evaluated using an RDE at 1600 rpm increasing in the order LF (LSF-0), SF (LSF-1.0), LSF-0.2, LSF-0.5, and LSF-0.8 corresponding to an increase in Sr-doping and oxygen deficiency character in the doped perovskite. Based on XRD analysis performed, structural distortions and phase configurational changes occur upon progressive doping as can be observed from Fig. 10a. Furthermore, the corresponding electrochemical impedance spectra (Nyquist plot) in Fig. 10b shows highest resistivity in the LF and SF samples having orthorhombic and tetragonal structures, respectively. Similarly, Cheng et al. correlated structural variations with Sr-doping in La 1 − x Sr x CoO 3 (LSC) [103]. The authors found a relatively abrupt phase transformation from a rhombohedral (LaCoO 3 ) to a cubic structure (La 0.2 Sr 0.8 CoO 3 ), congruent to progressive alignment of the Co-O-Co bonds and an oxidation state of Co greater than Co 3+ .
Density functional theory (DFT) was utilized in this work to calculate the Co-O-Co bond alignment. Figure 10c relates the structure type and Co-O-Co bond alignment to the Srdoping content. Highest conductivity (300-time increase compared to the pristine undoped LaCoO 3 sample), transition to a cubic structure, second highest oxygen vacancy content, and lowest OER overpotential corresponded to the La 0.4 Sr 0.6 CoO 3 sample. This indicates the favorability of cubic Pm-3m structures for intrinsic activity towards OER. Interestingly, Sunarso and Zhou dedicated an investigation to structural changes in LaNiO 3 − ẟ (LN) [104]. In their work, XPS analysis of oxygen deficiencies was not undertaken-however, this leaves room for doping, which introduces oxygen vacancies and enhances performance as discussed earlier. Nevertheless, in this early work by the group, a direct relationship between OER/ORR activity and LN structure was identified. LN samples that were heated at 400, 600, and 800°C yielded an apparent transition from rhombohedral (R-3c) to cubic (Pm-3m) and showed a direct correlation with respect to OER/ORR activities-see Fig. 10d. Furthermore, the elongation of the Ni-O bond in the cubic structure favors higher OER/ORR activity.
Computational analyses using varying density functional theory (DFT) approaches have proven invaluable in the investigations of surface microengineering effects including, but not limited to, effects of oxygen vacancies in perovskites. The Kohn-Sham scheme is perhaps the most utilized "basecase" method used in DFT. The derivation of the noninteracting and spin density functional respective systems are integrated within the Kohn-Sham scheme. The scheme's equation (Eq. (6)) revolves around motion calculation of interacting electrons as individual moving particles [105]. ν KS (r) represents the Kohn-Sham potential, μ i shows the one-electron orbital, and ε i represents the total energy of one orbital.
The different intermediates partaking in OER for perovskites and other material types have been heavily investigated using DFT. Ideally, OER intermediates (O*, OH*, and OOH*) should not bind too strongly to the active site of a perovskite, to facilitate for reasonable dynamics. Man et al. utilized this understanding to develop and present a universal scaling relationship between the free binding energy of OOH* and OH* in order to analyze the reaction free energy diagrams of all oxides in a general way [106]. This work gave rise to a simple and effective universal descriptor for OER reactions on oxide surfaces, including perovskites, and to an activity volcano plot. At the time, a few materials were at the apex of this activity volcano, representing a theoretical minimum overpotential, whilst remaining materials are burdened by either too weak or too strong O* intermediate binding energies. The activity descriptor (ΔG O* − ΔG OH* ) remains invaluable in all first principle design of materials, including oxygen-deficient perovskites for the OER. DFT approaches, such as DFT + U, which introduces an artificial corrective potential, are heavily used to study, fine-tune, and guide experimental work for improving OER performance in perovskites. For instance, Yao et al. employed DFT + U to investigate oxygendeficient Mg-based A 2 Mn 2 O 5 (A = Ca, Sr) [74]. They predicted Sr 2 Mn 2 O 5 to have lower OER overpotentials due to the large ionic radii of A-site elements caused by weakening the hybridization between the Mn d z2 and OH-p σ orbitals. Furthermore, Zhao et al. computed the Gibbs free energy changes for the OER using pristine PrBaCo 2 O 5 + δ (PBC, where Co as active center), PrBa 0.5 Sr 0.5 Co 1.5 Fe 0.5 O 5 + δ (PBSCF, where Co and Fe as active centers) [101].  in La 0.5 Sr 0.5 FeO 3 − ẟ eventually lowers the conductivity and leads to metal-to-semiconductor transition at low partial pressures of O 2 [108]. Density of states (DOS) calculations in Fig. 11b show how the Fermi level, initially in the middle of the hybridization band for O 2p and Fe 3d orbitals, increases. Two oxygen vacancy states appear, and as a result, the hybridized band becomes fully occupied. The excess electrons from the vacancies thus increase the Fermi level and cause the transition from metallic to semiconductor state, in this case leading to a decrease in conductivity (Fig. 11c). DFT under the general gradient approach (GGA), such as the Perdew-Burke-Ernzerhof (PBE) method, has proven to be an effective strategy for initial screening of oxygendeficient materials for electrolysis applications [109]. However, there are still opportunities for improvement by including orbital dependent potentials and hybrid functionals (i.e., HSE06, PBE0) that can provide more accurate electronics analysis (i.e., band gaps for semiconductors, band structure) compared with the basic PBE approach at the cost of high computational resources [110,111]. Incorporation of relatively recent methods, such as the GW approximation for calculating self-energy of a main body, is highly expected to curb limiting computational resources especially for large systems [112].

Disadvantageous effects of oxygen vacancies in perovskites
The previous section discussed changes in the intrinsic effects that promote an enhanced OER performance as perovskites become oxygen deficient to some degree. However, we will now focus on cases which do not fall under this general category.  [95]. OER activity was evaluated for a range of oxygen-deficient BSCF perovskites, namely heavily oxygen vacant (r-BSCF, ẟ = 0.51), pristine conventional (p-BSCF, ẟ = 0.38), and highly oxidized (o-BSCF, ẟ = 0.12) BSCF. Interestingly, overpotentials for heavily oxygen vacant and highly oxidized samples were inferior to that of the moderate and conventional sample (ẟ = 0.38). Figure 12a reports the lattice parameter (a) increases linearly with respect to the degree of oxygen vacancy (ẟ) in BSCF, indicating an increase in the ionic radii of the B-site ions (Fe, Co) which causes structural instabilities [114,115]. Figure 12b shows the relationship between ẟ and the recorded OER overpotential. Moreover, Du et al. reported excessive reduction via annealing in H 2 -reducing atmosphere led to the phase transformation of CaMnO 3 from Pnma to Pbam (CaMnO 2.5 ) [113]. The oxygendeficient and stable CaMnO 2.75 sample-showing the lower OER overpotential-was experimentally found to be the most conductive (4.68 × 10 −2 S m −2 ) compared with that of pristine CaMnO 3 (1.56 × 10 −3 S m −2 ) and CaMnO 2.5 (1.8 × 10 −3 S m −2 ).
In the cases of BSCF and CaMnO 2 perovskites discussed previously, a certain degree of vacancies is favorable, but this is not necessary the case for the wide variety of perovskite oxides. For instance, Hirai et al. showed that the OER activity of layered perovskite Sr 2 VFeAsO 3 − ẟ was substantially improved above lattice oxygen vacancy content of ẟ = 0.5, Relative electrical conductivity (s/sd¼0, red triangle) and relative hole concentration (p/pd¼0, blue square) as a function of oxygen non-stoichiometry, with values at stoichiometric state (d¼ 0) as reference state. Blue dotted line, trend of the hole concentration. Electrical conductivity is obtained from the experimental data [107], and hole concentration is estimated by integrating the unoccupied state density of the hybridized band. Reproduced from Ref. [108] with permission from The Royal Chemical Society, Copyrights 2020 manifesting near 300 mV reduction in overpotential and 80 times higher specific activity at 1.7 V vs. RHE [116]. Chronoamperometric (CA) tests revealed that formation of oxygen vacancies in Sr 2 VFeAsO 3 − ẟ does not cause structural instabilities. DFT calculations for ẟ > 0.5 show that the oxygen vacant sites become available and promote OHadsorbates through more favorable O-O bond formation, which further lowers enthalpic limitations for the OER.
DFT calculations were employed in order to generate a density of states (DOS) plot shown in Fig. 12c and indicate the creation of new electronic states near the Fermi level, which are known to enhance conductivity and allow favorable binding energies with OER intermediates. Furthermore, the same DOS plot predicts a 1.56 eV bandgap for the pristine perovskite sample, indicating the expected semiconductor behavior. The creation of states in only spin-up near the Fermi level in the DOS of CaMnO 2.75 and an apparent gap for the spin-down states indicate a highly spin polarized system exhibiting metallicity, which enhances conductivity. Miao et al. explored the role of oxygen vacancies in the OER of double perovskite PrBaCo 2 O 6-ẟ [38]. Confirming previous reports of the disadvantageous effects excessive oxygen vacancies can cause for OER performance of perovskites, the authors found that intrinsic activity decreases for this cobalt perovskite. Oxygen vacancies were found to form an ordered alignment of PrO 1 − ẟ layers with an alternative configuration of pyramidal Co 3+ O 5 and octahedral Co 3+ O 6 , resulting in spin state transition of Co 3+ ions in the tetrahedral formation from high-spin (HS: t 4 2g e 2 g ) to low-spin (LS: t 5 2g e 0 g ) states. This transition follows a reduction in the e g occupancy away from ideal unity and a decrease in the conductivity. Furthermore, an apparent weakening in the Co-O bond covalency results in higher instabilities and reduction in the alkaline (1 M KOH) OER performance. Deficiencies in the Co-O bond covalency in ABO 3 -type oxides caused by lattice distortions can severely limit electrochemical performance [117]. Figure 12d shows that as the oxygen vacancy content (ẟ) increases from 0.25 to 0.50, both the overpotential at 10 mA cm −2 increases from 360 to 420 mV and a corresponding increase in the Tafel slopes from 70 to 80 mV dec −1 , respectively.

Conclusion and future outlook
This review gives an executive, yet thorough, examination in the development of oxygen-deficient perovskites. A discussion pertaining to the major contributing factors of performance enhancements through electronic modulation has been undertaken. Attaining e g occupancy close to unity, minimizing ΔE d− p , enhancing conductivity, and microengineering the surface for optimum and moderate binding energies for the OER intermediates (O, OH, OOH) via the induction of an oxygen-deficient perovskite surface has been presented. The importance of careful tuning of oxygen vacancies in order to prevent structural instabilities was discussed.
Further research is needed in order to enhance the stability of perovskites generally, which are known to undergo amorphization during OER operations through the leaching of A/B-site cations, as is the case with BSCF materials [118]. On that note, propagated investigation of highly oxygen-deficient layered perovskites is encouraged, due to their innate stabilities at high ẟ values and oxygen vacancy oriented OER mechanism. The apparent lower stabilities exhibited in perovskites for longterm OER operation compared with Ni-and Fe-based materials are hindering some interest in them. However, this presents a great area of potential development for these materials. Furthermore, the relatively costly and multi-process steps involved in the fabrication and fine-tuning of oxygen vacancies in oxygen-deficient perovskites presently bottlenecks their potential utilization for large scale applications. Development of more environmentally benign and one-step syntheses for perovskites is expected to revolutionize development and applications of these electrocatalysts. The modification of perovskites through other types of defects and/or heterojunction with novel supports, such as conductive MXenes, may prove fruitful in enhancing their electrocatalytic performance.
The utilization of computational techniques, such as DFT, to accurately screen and predict favorable and highly active perovskite surfaces is of invaluable importance. DFT employment to further explore and understand the reaction mechanisms on perovskite surface during OER will lead to more rationally designed materials with more surface functionalities and properties. However, consideration should be taken when purely relying on DFT analysis for predicting performance of TMO electrocatalysts. Currently, functionals and pseudopotentials within conventional DFT can predict well the performance of 3d metals, but they do not work well for certain 4d and 5d TMOs (e.g., Ca 1 − x Sr x RuO 3 , SrIrO 3 ) [119,120]. In such systems, direct observation of the electronic structure (bulk-sensitive photoelectron spectroscopy) are conducted to understand their electronic structure. Furthermore, implementation of machine learning (ML) approaches for quick prediction and selection of effective catalytic surfaces has been on the rise [121]. For instance, Li et al. have recently presented an adaptive ML framework for OER perovskites, which navigated through numerous potential double perovskites (AA'B 2 O 6 ) and identified feasible surfaces for fabrication [80,113]. Appropriating ML techniques to identify the most prominent activity descriptors on surface-modulated perovskites will surely lead to a high-throughput propagation of nextgeneration perovskite electrocatalysts.
We believe that it is of paramount importance to rationalize the design of perovskites, and electrocatalytic materials in general, for an effective and feasible integration of such materials as viable industrial electrocatalysts in water splitting. Tuning activity descriptors relevant to the performance of oxygen-deficient perovskite electro-anodes, coupled with recent synthesis techniques for surface-modulated structures, offer potential for further improvement of catalytic activity. Bridging the gap between DFT, ML, and experimental work has been highlighted due to the immense potential it brings towards efficient and systematic approach for discovery of highly active and stable catalysts. Funding Open Access funding provided by the Qatar National Library.

Compliance with ethical standards
Conflict of interest The authors declare that there is no conflict of interest involved in this submission.
Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons licence, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons licence, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons licence and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this licence, visit http://creativecommons.org/licenses/by/4.0/.