English

• 1. Introduction

  The double carbon strategy retards the pace of environmental pollution and the energy crisis [1,2]. Lithium-ion batteries (LIBs) have captured most of the electronics market due to their high energy density and durable cycle life [3-5]. However, the scarcity of lithium resources and the flammability of the electrolyte lead to the high cost and low safety. It promotes the research focus towards aqueous metal ion batteries (Na, K, Ca, Zn, Al and Mg) [6-12]. Multivalent metal-ion batteries are attractive owing to their multiple electron transfer reactions. Among them, aqueous zinc-ion batteries (AZIBs) consist of zinc metal anodes, aqueous electrolytes and limited cathode materials. The former possesses the abundant resources, a theoretical capacity of 820 mAh/g, and a redox potential of −0.76 eV (vs. standard hydrogen electrode) [13-16]. Nevertheless, AZIBs are still plagued by the inability to match suitable cathode materials [17-19].

  To date, various electrodes have been explored, such as vanadium-based materials, manganese-based compounds, Prussian blue derivatives, organics and other transition metal compounds [20-26]. They are all capable of achieving reversible Zn ion storage after long-term cycles. Thereinto, organic composites are the emerging electrode materials in recent years. They are in the early stage of development. The exploitation of organic cathodes with excellent capacity and high voltage platform is the primary consideration. It is necessary to further study their structure and mechanism. Vanadium-based materials are featured by multiple V oxidation states and diverse crystal structures. The large interlayer distance facilitates rapidly the embedding and de-embedding of Zn ions [27]. However, commercial electrode materials cannot meet the requirements due to their large particle radius and small specific surface area. In order to bridge the gap between AZIBs and practical applications, it is crucial to enhance the electrochemical performance of batteries. Many optimization strategies have been proposed based on the modification of V-based compounds. For instance, Chen et al. [28] prepared a porous V₂O₅ nanofibers with an open layered structure. The assembled batteries deliver a capacity of 319 mAh/g at 0.02 A/g. After 500 cycles, they still maintain a capacity retention of 81%. Wu's group [29] designed ultrathin and amorphous V₂O₅ grown directly on graphene (A-V₂O₅/G). This unique structure facilitates the shortening of the diffusion path of zinc ions and improves the conductivity of the electrode. Zn/A-V₂O₅/G battery can retain 80% of initial capacity after 3500 cycles. This structural design effectively increases the cycle life of the battery, which can be attributed to the accelerated electrochemical kinetics.

  In addition, defect engineering is also considered as a feasible strategy to tune the electronic properties of materials, mainly including vacancies and doping (Fig. 1). The former is an intrinsic defect caused by atoms or ions in the structure forming vacancy defects in the original lattice position due to thermal vibrations. The latter is the impurity atoms or ions embedded in the lattice in the form of interstitial or replacement, which is a non-intrinsic defect [30]. The introduction of defects can effectively promote ion diffusion kinetics and improve electronic conductivity. Therefore, it is widely employed in the modification of electrode materials. Herein, we first summary recent advances in V-based electrode with different crystal structures. Then, we discuss the classification of defect engineering and focused on their effects on the electrochemical performance of vanadium-based materials through various strategies. Finally, we present the current challenges and future developments.

  Figure 1

  

  Figure 1.  A summary of defect engineering strategies for improving electrochemical performance of V-based electrode materials.

  DownLoad: Full-Size Img PowerPoint

  2. Defect engineering on V-based materials

  2.1 Classification of V-based materials

  Among many cathode materials, V-based compounds have captured much attention due to their low cost, and variety of crystal structures [31]. The valence state of vanadium ranges from +2 to +5. This rich oxidation state allows for multiple electron transfer and high theoretical capacity [32-34]. The crystal structure of vanadium oxides is determined by the coordination of V-O polyhedra and the oxidation state of V. From tetrahedron to square pyramids and triangular bipyramids, to distorted or regular octahedron, the varied structures provide multiple pathways for the transfer of zinc ions [35]. Fig. 2 shows the crystal structure of typical vanadium-based oxides. Based on the changes of valence, they can be categorized into two types: layered and tunnel structures. Among them, V₂O₅ materials are built by the deformed VO₅ square pyramid through the sharing of edges and corners to form a two-dimensional layered structure (Fig. 2a). The interlayer spacing is about 4.37 Å, which is favorable for the insertion of metal ions. For instance, Kundu et al. designed V₂O₅ materials with divalent Zn ions and H₂O intercalation (Zn_0.25V₂O₅·nH₂O) as cathodes. The assembled cells deliver a capacity of 220 mAh/g at 15 C [36]. Alshareef's group prepared porous Mg_0.34V₂O₅·0·84H₂O nanobelts materials. The large radius of the intercalation of hydrated Mg²⁺ (~4.3 Å) leads to an increase in the interlayer spacing to 13.4 Å. This facilitates the rapid insertion and extraction of Zn²⁺. As a result, the prepared electrode achieves a capacity of 264 mAh/g at a current density of 1 A/g in a potential window of 0.1–1.8 V [37]. The intercalation of metal ions can not only stabilize the host structure but also enlarge the interlayer distance. This favors the increase of active sites and also weakens the strong interactions of zinc ion embedding.

  Figure 2

  

  Figure 2.  The crystal structures of V-based oxides: (a) V₂O₅; (b) V₂O₃; (c) VO₂(B); (d) V₆O₁₃; (e) V₃O₇·H₂O; (f) V₂O₅·nH₂O.

  DownLoad: Full-Size Img PowerPoint

  As shown in Figs. 2b and c, VO₂ and V₂O₃ materials are tunnel structures composed of VO₆ octahedra sharing edges and corners. The former possesses a sufficient tunnel space (3.18 Å) than the latter (2.87 Å). In previous work [38], we reported VO_x@C microspheres as cathodes. Thereinto, VO₂@C electrodes show a stable cycling life after 1000 cycles and high rate capability. As a comparison, VO₂ and V₂O₃ electrode possess inferior specific capacity and cycle performance. It can be explained by the fact that the large tunneling space of VO₂ is more conducive to zinc ions. V₆O₁₃ materials with open structure contain V⁵⁺/V⁴⁺ mixed valence. Their crystal structure consists of alternating single and double [VO₆] octahedral layers (Fig. 2d). Liang's group [39] prepared V₆O₁₃ cathode, which delivers a capacity of 206 mAh/g at 10 A/g after 3000 cycles. In addition, the zinc vanadate phase (Zn_0.25V₂O₅·H₂O) appears during the embedding of zinc ions and recovers to the original phase when the Zn ions are extracted. The occurrence of this phase transition leads to the insertion of much Zn²⁺ into the host structure. Thus, Zn/V₆O₁₃ batteries possess a high Zn ion storage capacity.

  V₃O₇·H₂O (H₂V₃O₈) is a layered structure composed of VO₆ octahedron and VO₅ trigonal bipyramids. The V₃O₈ layers are linked together by hydrogen bonds, which can easily intercalate Zn ions (Fig. 2e). Compared with the above-mentioned materials, the presence of hydrogen bonds in V₃O₇·H₂O can provide excellent structural stability during repeated cycling. In addition, V⁵⁺ and V⁴⁺ co-exist in a 2:1 ratio in the structure, resulting in the high electronic conductivity. This suggests that it possesses more active redox sites. He and collaborators [40] reported the assembly of Zn cells using layered H₂V₃O₈ nanowires as cathodes and Zn anodes with a Zn(CF₃SO₃)₂ aqueous electrolyte. Benefiting from the large interlayer spacing, they can maintain an initial capacity of 94.3% after 1000 cycles. To further improve the cycle life, Pang et al. [41] designed a graphene sheet-wrapped H₂V₃O₈ nanowire electrode. The composite materials own a high specific surface area, which is beneficial to increase the contact area between the electrode and the electrolyte. At high current density (20 C), the electrode can run stably for 2000 cycles.

  In Fig. 2f, the intercalation of water molecules between V₂O₅ layers plays a crucial role in expanding and supporting the layered framework of V₂O₅-based materials. Yang's group [42] prepared V₂O₅·nH₂O/graphene (VOG) via a liquid phase approach. The results show that the electrostatic interaction between Zn²⁺ and V₂O₅ framework is weakened after water solvation, which effectively increases the diffusion rate of Zn²⁺. Thus, H₂O acts as a charge shield for the intercalated metal ions during cycling, reducing their effective charge. Liang and co-workers [43] inserted Li⁺ into the V₂O₅·nH₂O interlayer, widening the (001) plane spacing from 12.1 Å to 13.77 Å. Zn/Li_xV₂O₅·nH₂O (LVO) batteries present highly reversible rate performance and maintain a capacity of 192 mAh/g after 1000 cycles (10 A/g).

  A variety of vanadium-based compounds formed with V-O layers as the main structure have been explored for AZIBs, but the unmodified electrodes still face many challenges in terms of electrochemical performance. In Fig. 3, the cell possesses a slow kinetic process due to the inherent poor conductivity of the V-base material as well as the strong electrostatic interactions when the carrier Zn²⁺ is embedded. In addition, the dissolution of the cathode promotes the formation of unfavorable by-products. These adverse effects are the crucial reasons for the decrease in the actual capacity of the electrode. For this reason, researchers have turned their attention to the modulation of materials structure.

  Figure 3

  

  Figure 3.  The main issues of V-based electrode materials.

  DownLoad: Full-Size Img PowerPoint

  2.2 Effect of defects engineering on zinc ion storage capacity

  2.2.1   Classification of defects

  In the past decades, there has been the common strategies to improve electrochemical activity and electrical conductivity by introducing structural defects in target materials [44]. Defect engineering can change the surface chemistry, electronic structure or coordination mode of materials, which is widely used in various fields such as catalysis and energy storage [45,46]. Defects are of various types including vacancies (anions and cations), and heteroatom doping. In the field of AZIBs, these defects endow V-based materials with new capabilities in electronic, magnetic, and optical properties [47]. We will specifically discuss the effect of different defects on the energy storage performance of the cells in the following sections.

  2.2.2   Anion vacancy

  Oxygen vacancies (V_o) is a structural defect formed by the escape of an oxygen ion from the lattice. Their presence shortens the shuttle path of ions and causes an increase in the conductivity and diffusion coefficient of the material. Therefore, the fabrication of V_o plays an important role in the improvement of electrochemical performances such as specific capacity, energy density, and cycling stability of battery [48]. Cao's group [49] designed VO₂ materials with V_o and found that oxygen vacancies can enlarge the tunneling space of VO₂ electrode. Further, density functional theory (DFT) calculations confirm that the VO_1.75 electrode owns a narrow band gap. It suggests a low binding energy of valence electrons and enhanced charge transport. Fig. 4a also presents a lower diffusion energy barrier than the VO₂ electrode when the zinc ions are embedded into the structure. This indicates that the electrode with V_o possesses a rapid electrochemical kinetic process (Fig. 4b).

  Figure 4

  

  Figure 4.  DFT calculation of electrodes with V_o. (a) Zn ion diffusion energy barriers; (b) Zinc ions diffusion pathways along the b tunnel in VO₂ and VO_1.75 electrode. Reproduced with permission [49]. Copyright 2020, American Chemical Society. (c, d) Schematic of Zn²⁺ insertion/extraction for perfect and oxygen deficient vanadium oxide (O_d-VO), respectively. Reproduced with permission [50]. Copyright 2019, Wiley-VCH. (e) Calculated formation energy of two electrodes. (f) DOS of V₂O₅-O defects. Reproduced with permission [52]. Copyright 2021, Elsevier Ltd.

  DownLoad: Full-Size Img PowerPoint

  In fact, the batteries show inferior cycling stability when repeatedly cycled, especially at high current densities. Many efforts have been made to solve this issue. For instance, Liao et al. [50] prepared oxygen-deficient V₆O₁₃ cathodes by a redox self-assembly method. In Figs. 4c and d, the partial absence of electronegative oxygen in the V₆O₁₃ lattice can effectively improve the Zn²⁺ diffusion rate as well as the reversibility of charge and discharge. When the oxygen atoms are extracted, there are excess electrons to form defective sites, which contribute to the formation of delocalized electron clouds to increase the discharge capacity [51]. Also, the defect-free structure shows a higher Gibbs free energy of desorption than the defective electrode. This indicates that Zn ions are difficult to desorb, resulting in reduced cycling stability. As a result, the modified electrode materials deliver an initial capacity of 401 mAh/g at 0.2 A/g and a stable cycle of 2000 cycles at high current density (2 A/g). Qin and coworkers [52] introduced V_o into the main structure of V₂O₅ in order to overcome its slow dynamics. Based on DFT calculations, the defect optimizes the internal electronic structure of the electrode, providing a bandgap of 0.45 eV and lowering the Zn²⁺ diffusion energy barrier (0.72 eV) and generation energy (55.04 eV) in Figs. 4e and f. The cells can present a specific capacity of 427.3 mAh/g at 0.1 A/g and obtain a capacity retention of 92.1% after 5000 cycles.

  The Gibbs free energy of zinc ion adsorption/desorption is an important parameter to assess the reversibility and kinetic process of zinc ion. In previous reports [53], the electrochemical kinetics of potassium vanadate cathodes were successfully optimized by combining oxygen vacancies with a carbon coating strategy. The synthesized oxygen-deficient potassium vanadate/amorphous carbon nanoribbons (C-KVO|O_d) possess low Zn²⁺ adsorption Gibbs free energy and energy barrier. It suggests a highly reversible Zn²⁺ adsorption/desorption process. Amorphous carbon facilitates the rapid transfer of electrons. Thus, this unique structure both improves the conductivity of the electrode and provides more active sites for Zn²⁺ storage. Benefiting from this synergistic effect, the C-KVO|O_d cathode presents a capacity of 385 mAh/g at 0.2 A/g and maintains a high capacity (160 mAh/g) at 20 A/g.

  The creation of V_o in metal oxides can be achieved in several ways: (1) heat treatment in an inert atmosphere; (2) using a reducing agent to partially reduce the metal ions in the metal oxide during the reaction to generate V_o; (3) materials treated with plasma are in an electronically excited state with high energies, which is beneficial for the appearance of V_o; (4) carbonization of organic-containing reaction precursors. Note that oxygen vacancies can be formed in an oxygen barrier and high temperature environment; and (5) the lattice distortion caused by hetero-doping forms V_o [54]. The first three routes are commonly used in the preparation of electrodes for rechargeable metal ions batteries [50,52,55].

  Recently, a strategy is developed to introduce V_o via an in-situ polymerization process using conductive polymer. For example, Bin et al. [56] designed a layered NH₄V₃O₈ electrode with poly(3,4-ethylenedioxythiophene) (PEDOT) intercalation (PEDOT-NVO) to increase the interlayer spacing from 7.8 Å to 10.8 Å. The formation of oxygen vacancies is attributed to the polymerization of EDOT monomers and the reduction of V₃O₈ layers. Electron paramagnetic resonance (EPR) confirms the appearance of oxygen vacancies. Zn/ PEDOT-NVO cells show an activation capacity of 345.5 mAh/g at 0.2 A/g and maintain a discharge capacity of 160.6 mAh/g after 5000 cycles (10 A/g, Figs. 5a and b). Moreover, their energy density can reach 353.1 Wh/kg at a power density of 50 W/kg (based on the mass of the cathode). In Fig. 5c, the absence of side reactions during the reaction process further reveals the zinc ion embedding/extracting mechanism. It corresponds to their long cycle life. Therefore, this is an effective strategy to introduce oxygen vacancies through the embedding of conducting polymers. A similar electrode design is used by Xiong's group [57] to enhance the zinc storage capacity of vanadium dioxide. They fabricated the oxygen-free hydrate VO₂ with polypyrrole (PPy) coating (O_d-HVO@PPy) by simple one-step hydrothermal route. The polymer coating alleviates cathodic dissolution and enhances electron transfer. Moreover, the oxygen vacancies contribute to the reversible adsorption of Zn ions on the electrode surface. The incorporation of structured water can effectively regulate the electrostatic interactions of Zn²⁺ [58]. Abided by the proton and Zn ion co-embedding mechanism, the cell provides superior rate performance and cycling stability after 1000 cycles (a capacity of 159 mAh/g at 10 A/g), as shown in Figs. 5d and e.

  Figure 5

  

  Figure 5.  The electrochemical performances of the electrode with V_o. (a) Cycling performance of the two cathodes at 0.2 A/g. (b) The long-term cycle capability. (c) The Zn²⁺ storage mechanism of Zn/PEDOT-NVO batteries. Reproduced with permission [56]. Copyright 2020, Elsevier Inc. (d) Rate capability at varying current densities. (e) Long life cycling performance. Reproduced with permission [57]. Copyright 2021, Wiley-VCH GmbH.

  DownLoad: Full-Size Img PowerPoint

  In order to improve the conductivity of the electrode, besides introducing V_o, it is also a potential route to combine with high conductivity materials. Huang et al. [59] constructed a three-dimensional (3D) sponge-like hydrated VO₂ and graphene composite (O_d-HVO/rG) with abundant oxygen defects. The electrode presents a high specific capacity (428.6 mAh/g at 0.1 A/g), fast electrochemical kinetics, and long cycle life (197.5 mAh/g after 2000 cycles). Most electrodes are based on structural chemical defects to optimize electrochemical performance. Chen et al. [60] reported vanadium oxide electrodes with both physical and chemical defect structures to improve the storage performance of zinc ions. They synthesized vanadium oxide nanofibers (VCN) with a 3D porous structure by electrospinning. Polyacrylonitrile (PAN) as a raw material produces V_o and a large number of pores during the pyrolysis process. This abundant pore structure is favoring to increase the specific surface of the sample, while oxygen vacancies bring more active sites. Based on this dual effect, the specific capacity of the battery is effectively enhanced. The host structure of the 3D network can provide more diffusion paths for Zn ions, it facilitates rapid transfer of zinc ions.

  2.2.3   Cation vacancy

  The induction of defects creates more active sites than the limited diffusion of the original material. This can be used to accommodate additional reversible ion intercalation. Cation vacancies have also attracted some attention in multivalent metal secondary batteries because they can weaken electrostatic interactions during ion intercalation [61]. The construction of cationic defects requires an increase in the surface energy of the material due to the high defect formation energy of cations. Therefore, the synthetic strategy is of particular importance. Currently, several approaches are commonly employed to introduce cationic vacancies into transition metal chalcogenides (TMCs) including different valence cation replacement, anion substitution, electrochemical charging process and pH-controlled methods [62-65]. In AZIBs, the strategies are mostly used in the modification of Mn-based compounds [66,67]. In particular, spinel structured electrodes with strong lattice charge repulsion are unable to store Zn. For instance, Chen and co-workers designed a cation-deficient ZnMn₂O₄ cathode material. The introduction of Mn vacancies accelerates their electrochemical kinetics. The battery presents a superior rate performance and stable cycle capability of 500 cycles [68]. Therefore, the introduction of cationic vacancies is also an effective approach to improve the energy storage capacity. For vanadium-based compounds, there are still challenges in the exploration of cationic vacancy-modified electrodes.

  Chou et al. [64] demonstrated in situ lattice distortion of V₂O₃ induced by the charging process. The prepared V-defect-rich V₂O₃ material is used as a cathode for Zn²⁺ storage. Fig. 6a shows that the energy required for zinc intercalation decreasing (from −0.28 eV to −0.72 eV) as the number of vacancies increase. It indicates that the abundant vanadium vacancies in V₂O₃ favor the Zn²⁺insertion. In situ XRD further confirmed the structural changes of the electrodes during the first charge and subsequent cycling. The shift of the crystal planes is related to the insertion and extraction of zinc ions. Fig. 6b demonstrates the formation of lattice defects and zinc ion storage sites during charge/discharge. The in situ electrochemical lattice conversion strategy enables the electrode to achieve a capacity of 154.3 mAh/g at high current density (51.2 A/g).

  Figure 6

  

  Figure 6.  The electrochemical performances of electrodes with cationic vacancies. (a) DFT calculated intercalation energies for zinc ions in V₂O₃ with different vacancies. (b) Schematic of the initial charging process for V₂O₃ and the subsequent Zn²⁺ storage process. Reproduced with permission [64]. Copyright 2021, Wiley-VCH. (c) Schematic of Zn²⁺ diffusion in the ZNV with NH₄⁺ vacancies in the interlayers. (d) Low-temperature cycling performance at 2 A/g. Reproduced with permission [70]. Copyright 2021, Elsevier B.V.

  DownLoad: Full-Size Img PowerPoint

  Protective measures of cation pre-insertion into the host material can ensure the structural stability of the electrode during long-term cycling [69]. Notably, it is also possible to introduce cationic vacancies indirectly during the synthesis. He et al. [70] designed the Zn_0.3(NH₄)_0.3V₄O₁₀·0·91H₂O (ZNV) cathode with abundant cation vacancies. DFT calculations show that the pre-intercalation of Zn²⁺ leads to the formation of four different defects in the structure including NH⁴⁺, V₁, V₂ and Zn²⁺/V^5+/4+ cationic vacancies, as presented in Fig. 6c. The Zn²⁺ diffusion barrier of defective ZNV electrodes is significantly lower than that of non-defective ones. This suggests that the existence of defects is conducive to the rapid diffusion of zinc ions between layers. Thereinto, the NH⁴⁺ vacancies can obtain the energy barrier of 0.862 eV than other defects. The results show that ZNV electrodes deliver a discharge capacity of 461.1 mAh/g (0.1 A/g). And there is almost no decay after 2000 cycles at 2 A/g. In addition, stable cycling performance and long cycle life (3500 cycles) are still obtained under extreme temperature conditions (0, −15 and 30 ℃, Fig. 6d). Thus, the cation vacancies caused by Zn²⁺ pre-intercalation are essential to improve the migration rate of Zn²⁺ in the electrolyte and to assure a superior reaction kinetics of ZNV in a wide temperature range.

  The quantitative analysis of defects is crucial to identify metal vacancies and V_o in the materials. The Rietveld refinement of XRD technique is often employed to quantify the defect concentrations. However, the presence of V_o is generally difficult to be captured by XRD pattern due to the small atomic radius. Therefore, Rietveld refinement of neutron powder diffraction (NPD) is more suitable for light and small elements. Zhu and collaborators [71] combined two techniques to quantify V-deficient V₂O₃ (V_d-V₂O₃) electrodes with 5.7% V_d clusters. The XANES (X-ray absorption near edge structure) spectra of V K-edge detected defects in the V₂O₃ sample, as shown in Fig. 7a (Site A). The pre-edge peak intensity of the material is significantly enhanced compared to the defect-free sample. It indicates that the structure of V_d-V₂O₃ is distorted around the V atoms, which can be attributed to the absence of surrounding atoms. As shown in Fig. 7b, the insertion of Zn²⁺ into V_d-V₂O₃ structure shows different Gibbs free energies. Zn ions occupy vanadium vacancies, which can release −1.34 eV heat under strong electrostatic interaction. It reinforces the stability of the host structure. However, the extraction of Zn²⁺ becomes difficult undergoing this strong interaction. Part of the Zn²⁺ is riveted on the vanadium vacancies, resulting in the residue of Zn. It can be observed the expansion and contraction of the V_d-V₂O₃ lattice with the intercalation and de-intercalation of Zn²⁺ in the ex situ XRD patterns (Fig. 7c). The 5.7% V_d clusters accelerate the diffusion of Zn ions. The battery can be repeatedly charged and discharged 30,000 times with the capacity retention of 81%.

  Figure 7

  

  Figure 7.  The kinetics process and the cycling performance. (a) The XANES spectra of V K-edge. (b) The Gibbs free energy. (c) Ex situ XRD patterns of V_d-V₂O₃ electrodes at different cut-off voltages during the charge and discharge process. Reproduced with permission [71]. Copyright 2021, Springer Nature. (d) Cycling stability of the electrodes at 5 A/g. Reproduced with permission [79]. Copyright 2022, Elsevier B.V.

  DownLoad: Full-Size Img PowerPoint

  2.2.4   Heterogeneous doping

  Typical heteroatom doping includes metallic and non-metallic doping. For the former, metals such as Li, Na, K, Al, and Co are used for interlayer doping [43,57,72,73]. Mai's group [74] reported Na⁺ intercalation between V₂O₅ layers as cathode. The Zn/Na_0.33V₂O₅ battery obtains a stable structure and keeps a capacity of 93% for 1000 cycles. Other alkali metals with larger atomic radii have also been explored, which are hindered in terms of specific capacity despite improved structural stability [75,76].

  For electrode materials, the limited ion diffusion path is one of the main factors leading to their performance degradation. During the reaction, the diffusion of carriers is hampered, which causes severe structural deformation and irreversible reactions. Therefore, the pre-intercalated metal ions can act as "pillars" and expand the interlayer space of vanadium oxide. This type of intercalation not only increases the stability of the crystal structure, but also optimizes electrical conductivity of electrode. It contributes to the stable intercalation of Zn ions and enhances its energy storage capacity.

  Cationic doping can generally be divided into substitutional and interstitial doping. Jo et al. [72] prepared a hollandite-type VO_1.52(OH)_0.77 material with tunnel structure and introduced Al element in the host structure. They found that Al³⁺ ions replace part of the V ions, which can be represented by V_1-xAl_xO_1.52(OH)_0.77 (x = 0, 0.05, and 0.09). Since the radius of Al³⁺ (0.535 Å) is smaller than that of V ions (V³⁺ = 0.64 Å, and V⁴⁺ = 0.58 Å) [77], the linear decrease of lattice parameters is consistent with Vegard's law. Compared with VO_1.52(OH)_0.77, the doping of Al stabilizes the electrode structure, which is beneficial to the enhancement of the cycle performance. Wang's group [78] reported the doping of Al in layered V₁₀O₂₄ materials to maintain the stability of the crystal structure. Pure V₁₀O₂₄ electrode possesses a high initial specific capacity, but their capacity declines rapidly with increasing number of cycles. As a comparison, Al-doped V₁₀O₂₄ electrode achieves a positive influence in the electrochemical performance. Specifically, they can charge and discharge stably up to 3000 cycles and maintain 98% of the capacity.

  Similarly, Jiang and collaborators [79] developed a high-temperature quenching approach to introduce Al ions into the V₂O₅ interlayer and form abundant V_o on the electrode surface. Benefiting from the participation of these defects, the optimized electrode material shows a long cycle life (5000 cycles) and excellent rate capability (Fig. 7d). The influence of Al doping on the electronic properties of the host material is further evaluated by DFT calculations. From Fig. 8a, it can be shown that Al is suitable to replace the vertex position from the energy point of view. Furthermore, the addition of Al and the formation of V_o reduces the diffusion barriers of Zn (0.36 eV drops to 0.09 eV). It indicates that doping can accelerate the reaction kinetics of the electrode. The density of states in Fig. 8b further confirms that the conductivity of the electrode material is effectively improved. The presence of oxygen vacancies induces changes in electrochemical activity and local rearrangement of the electronic structure, which promotes the accumulation of charge carriers [80].

  Figure 8

  

  Figure 8.  DFT calculation and the cycle capability of electrode with ion doping. (a) Energy barriers for diffusion paths in two electrodes. (b) DOS of the two samples. Reproduced with permission [79]. Copyright 2022, Elsevier B.V. (c) Lattice parameters and (d) the zinc-ion diffusion coefficient of samples. Reproduced with permission [81]. Copyright 2021, Elsevier B.V. (e) Cycle performance at a current rate of 4 A/g. Reproduced with permission [83]. Copyright 2020, Wiley-VCH.

  DownLoad: Full-Size Img PowerPoint

  The doping of metal ions can effectively change the geometrical structure of the material, including the adjustment of layer spacing and rearrangement. Therefore, it can positively affect the electrical conductivity, ion diffusion rate, and structural stability of the material. Yoo et al. [81] prepared Fe-doped V₂O₅ nanorods samples by electrospun polyacrylonitrile (PAN) fibers template and annealing at high temperature. To investigate the effect of the amount of Fe doping on V₂O₅, they synthesized various Fe-V₂O₅ materials. The successful doping of Fe ions can be confirmed by the change of lattice parameters. From Fig. 8c, all lattice parameters of V₂O₅ material gradually expand with increasing amount of Fe source. This may be attributed to the formation of FeO₆ octahedra between the V₂O₅ layers. Additional active sites are provided for the storage of Zn ions. The occupation of V⁵⁺ sites by Fe³⁺ also generates oxygen vacancies, causing an increase in electrode conductivity. Among them, 5Fe-V₂O₅ sample possesses a high Zn ion diffusion coefficient (Fig. 8d), which may be due to the narrowing of the bandgap. Therefore, the optimized electrode can deliver a capacity of 422 mAh/g at 0.5 A/g and maintain a capacity retention of 85% after 160 cycles at 1.3 A/g.

  The layers in V₂O₅·H₂O are connected by hydrogen bonds. This is similar to the structure of the H₂V₃O₈ material, as shown in Figs. 2e and f. Previous studies [36,37] have confirmed that the introduction of metal ions between the V₂O₅ layers can lead to improved cycling stability. Inspired by this, the researchers began to develop the doping of the V₃O₈ layer. Compared with monovalent cations (Na⁺, Li⁺), the introduction of polyvalent ones results in strong ionic bonds. It can suppress lattice distortion during cycling [82].

  Adding divalent cations to the V₃O₈ layer is also one of the directions to stabilize cycling and prolong lifetime. Liu's group [83] added Mn ions to the NaV₈O₂₀ material to improve its conductivity. With the combined effect of monovalent and divalent ions, (Na_0.33, Mn_0.65)V₈O₂₀·nH₂O materials maintain a stable cycle for 1000 cycles with a capacity loss of 1%. To study the role of Mn ions, they replaced new transition metal materials, such as Fe, Co, Ni, Ca, for comparison. The results show that the capacity retention of other electrodes is significantly lower than that of the Mn-optimized samples (Fig. 8e). This is mainly ascribed to the inhibition of electrode dissolution by the incorporation of Mn ions. Zhu et al. [84] reported the co-intercalation of monovalent and divalent metal cations into the V₃O₈ structure to form NaCa_0.6V₆O₁₆·3H₂O (NaCaVO) samples. The battery can deliver a capacity of 231 mAh/g after 2000 cycles. From Fig. 9a, the zinc ion diffusion path is further investigated by the quasi-empirical bond-valence (BV) approach. The embedded Zn²⁺ diffuses mainly in a zigzag shape along the b-axis. Structural water plays a crucial role in NaCaVO samples. The spacing of the V₃O₈ layers of the NaCaVO sample without crystal water is reduced from 8.1 Å to 6.7 Å (Fig. 9b). First, zinc ions possess low energy barriers at multiple diffusion paths. Then, sufficient interlayer space is favorable to the improvement of the storage capacity of Zn²⁺. Then, structural water can reduce the Gibbs free energy of Zn absorption (−2.02 eV), which acts as a buffer against the strong electrostatic interaction of Zn ion (Fig. 9c). The Zn/NaCaVO battery can last for 10,000 cycles and retain a specific capacity of 125 mAh/g. This is the result of Na⁺ and Ca²⁺ co-stabilizing the structure.

  Figure 9

  

  Figure 9.  The kinetic process of dual ion-doped V-based electrodes. (a) Migration path of Zn²⁺ in NaCaVO along the b-axis. (b) The crystal structure of NaCaVO and NaCaVO with no structural water electrodes after Zn-ions intercalation. (c) Zn²⁺ adsorption and diffusion models from surface to bulk. Reproduced with permission [84]. Copyright 2019, Wiley-VCH. (d) The crystal structure of iron ion and alkylammonium cation co-intercalated vanadium oxide. (e) Schematic of the energy storage mechanism. Reproduced with permission [85]. Copyright 2022, Elsevier B.V.

  DownLoad: Full-Size Img PowerPoint

  Considering the design of electrodes can combine the two roles of expanding the layer spacing and stabilizing the layer structure. Luo's group [85] explored the co-insertion of metal ions (iron ion) and organic molecules (alkylammonium cation) into layered vanadium oxide (FeVO-X) as cathodes. Among them, the intercalation of metal ions can generate strong electrostatic attraction between VO_x layers, which stabilizes the interlayer structure. The organic molecules can act as a role in expanding the interlayer spacing. It is favorable to increase the storage sites of Zn²⁺. The optimal interlayer spacing can be obtained by adjusting the length (X) of the alkyl chain in the alkylammonium cation. As shown in Fig. 9d, FeVO-12 samples possess an interlayer spacing of 19.26 Å. The assembled batteries deliver a specific capacity of 408 mAh/g at 0.1 A/g and can be charged and discharged stably up to 1000 times at 10 A/g. In addition, the charge storage mechanism of this electrode is further confirmed through ex situ XRD patterns and XPS spectra (Fig. 9e). The above double metal ion co-doping strategies can effectively optimize the electrode material structure from the following aspects. First, the enhancement of the electrical conductivity facilitates the rapid transfer of charges. Second, the widening of the layer spacing is beneficial in providing abundant Zn ion transport paths. Finally, the stable V-O layer prevents the main structure of the electrode from collapsing during repeated cycles.

  Anion doping (such as N, P, S, C and Br) is also an efficient approach to further enhance the electrochemical performance of V-based materials. In previous reports, it has been revealed that the non-metallic heteroatoms can boost the ion transfer ability and promote the wettability of electrodes and electrolytes [86]. The replacement of highly electronegative oxygen with low electronegative elements such as N, S and C can reduce the diffusion barriers of Zn²⁺ in the structure. For instance, Wang et al. [87] synthesized the sandwich-like sulfur-doped V₂O₅/reduced graphene oxide/sulfur-doped V₂O₅ (S-V₂O₅/rGO) core-shell structure via a hydrothermal and calcination strategy. The results show that the Zn//S-V₂O₅/rGO battery delivers a specific capacity of 467 mAh/g at 0.4 A/g. And they can still obtain a capacity of 442 mAh/g at 2 A/g, demonstrating their excellent rate capability. This S-doped structure is beneficial to improve the electrical conductivity of the composites and promote the rapid transfer of Zn²⁺ and electrons. In addition, the design of the sandwich structure can provide abundant transport channels for Zn ions. Ge et al. [88] controlled the directional growth of the LiV₃O₈ material by doping with different amounts of bromine ions to form small rod-like particles (LVOB). The doping of Br ions presents some influence on the morphology of the samples. The ion doping behavior inhibits the directional growth and eventually leads to irregular change. In addition, their growth is accompanied by the evolution of defects, thus expanding the energy distribution for rapid redox reactions [89]. During the reaction, the charge imbalance causes the generation of oxygen defects. Notably, it is very critical to tune the appropriate content of doping elements for the enhanced zinc storage capacity. The introduction of excess Br ions reduces the stability and electrochemical activity of the cell. After 500 cycles, the optimized LVOB-2 electrode can maintain a capacity of 207 mAh/g, demonstrating its durable cycling stability. As a result, the excellent electrochemical performance is attributed to heteroatom doping and the generation of oxygen defects. So far, there are few literatures on anion doping with V-based compounds as host materials. This also provides a direction for further exploration.

  3. Summary and outlook

  In summary, vanadium-based electrodes perform unsatisfactorily in electrochemical performance for AZIBs due to their narrow operating voltage, electrode dissolution, sluggish electrochemical kinetics, and low electrical conductivity. Defect-rich materials can alter the atomic structure and charge distribution of the sample. The advantages of defect engineering in electrode materials can be described as follows (Fig. 10): First, the defects induce more active sites, effectively improving the specific capacity of the battery. Secondly, they can weaken the strong electrostatic interaction when zinc ions are embedded and promote the rapid charge transfer. Finally, the main structure can be stabilized to ensure the cycle life of the battery.

  Figure 10

  

  Figure 10.  The advantages of defect engineering and future goals for electrode materials.

  DownLoad: Full-Size Img PowerPoint

  In Table 1, we summary the electrochemical performance of the vanadium-based electrode materials. It can be observed that the electrochemical stability and cycle life are greatly improved. The optimum electrode can maintain stable charge and discharge after 10,000 cycles. Therefore, the defect engineering strategy is an efficient and feasible way to solve the above problems. However, it is worth noting that these modifications cannot broaden the working voltage of the battery. Among various strategies to modify cathode materials, the modulation of electron cloud density can improve the electrochemical stability of organic sulfide compounds. A high voltage window of 1.7 V is achieved, which is superior to most V- and Mn-based compounds. Nevertheless, the electrochemical performance of the cathodes still fails to meet the market requirements. Hence, the development and exploration of electrode materials still face a large number of challenges.

  Table 1

  

  Table 1.  The electrochemical performance of the optimized vanadium-based electrode materials.

  DownLoad: CSV

  In future work, we should first explore some ways to increase the energy density of batteries. For cathode materials, the capability of large capacity and high voltage together determines the energy density. There are several thinking directions: (1) The mass loading of electrode materials. Active substance mass is closely related to specific capacity. In the current reports, the loading of cathode materials is generally lower than 2 mg, which is not matched with the excessive Zn anode. The electrodes with high loading mass are closer to practical applications. However, it may lead to a reduction of specific capacity. (2) Increasing the operating voltage of the battery. The V-based polyanionic compounds show high working voltages beyond 1.2 V but suffer from inferior specific capacity. It is possible to modify their surface structural to improve the electrochemical performance. Also, it is a feasible approach to pre-insertion of high-potential transition metal ions into electrode materials.

  Then, oxygen vacancy and cation doping are commonly used in defect engineering strategies. The optimal concentration of defects in the host structure for Zn ion storage has rarely been studied. Moreover, the variation of defects in the structure during charging and discharging needs to be further explored. In situ characterization approaches (XRD, XPS, etc.) facilitate the investigation of elemental evolution. At present, there are few studies on anion doping. Mn-based cathode materials are modified by this strategy to inhibit Mn ion dissolution accompanied by the formation of oxygen vacancies. This suggests that the introduction of anions (S, N, and F) into vanadium-based compounds is a promising direction. The changes caused by defects are mainly directed to the electronic structure and ion diffusion behavior. However, not all defects play a positive role. Researchers need to employ advanced characterization techniques to analyze the role played by defects and reduce the occurrence of negative effects.

  Finally, the construction of defects can create more active sites and accelerate electrochemical kinetic processes. This optimized electrode can be composited with other materials including graphene, carbon nanotubes, conductive polymers to further enhance the conductivity. Furthermore, the appropriate modification on the surface defects of electrode materials can effectively modulate the electron interaction, local ion concentration, and energy storage behavior. The rational design of the electrode structure is an indispensable step in the development of high-performance cathode materials.

  Declaration of competing interest

  The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

  Acknowledgment

  The work is supported by National Natural Science Foundation of China (No. 52172218).

  
  
• 1. [1]

     J.B. Goodenough, Energy Storage Mater. 1 (2015) 158–161. doi: 10.1016/j.ensm.2015.07.001

  2. [2]

     D.P. Zhao, M.Z. Dai, Y. Zhao, et al., Nano Energy 72 (2020) 104715. doi: 10.1016/j.nanoen.2020.104715

  3. [3]

     J.M. Tarascon, M. Armand, Nature 414 (2001) 359–367. doi: 10.1038/35104644

  4. [4]

     S. Ni, J. Liu, D. Chao, et al., Adv. Energy Mater. 9 (2019) 1803324. doi: 10.1002/aenm.201803324

  5. [5]

     C. Liu, X. Wu, B. Wang, Chem. Eng. J. 392 (2020) 123651. doi: 10.1016/j.cej.2019.123651

  6. [6]

     S. Chen, C. Wu, L. Shen, et al., Adv. Mater. 29 (2017) 1700431. doi: 10.1002/adma.201700431

  7. [7]

     Q. Zhang, Z. Wang, S. Zhang, et al., Electrochem. Energy Rev. 1 (2018) 625–658. doi: 10.1007/s41918-018-0023-y

  8. [8]

     Y. Liu, X. Wu, J. Energy Chem. 56 (2021) 223–237. doi: 10.1016/j.jechem.2020.08.016

  9. [9]

     J. Zhang, Z. Chang, Z. Zhang, et al., ACS Nano 15 (2021) 15594–15624. doi: 10.1021/acsnano.1c06530

  10. [10]

      M. Jiang, C. Fu, P. Meng, et al., Adv. Mater. 34 (2022) 2102026. doi: 10.1002/adma.202102026

  11. [11]

      S. Ye, L. Wang, F. Liu, et al., eScience 1 (2021) 75–82. doi: 10.1016/j.esci.2021.09.003

  12. [12]

      B. Xu, S. Qi, F. Li, et al., Chin. Chem. Lett. 31 (2020) 217–222. doi: 10.1016/j.cclet.2019.10.009

  13. [13]

      Y. Liu, Y. Liu, X. Wu, Chem. Record. (2022) e2200088.

  14. [14]

      M. Song, H. Tan, D. Chao, H.J. Fan, Adv. Funct. Mater. 28 (2018) 1802564. doi: 10.1002/adfm.201802564

  15. [15]

      H.F. Li, L.T. Ma, C.P. Han, et al., Nano Energy 62 (2019) 550–587. doi: 10.1016/j.nanoen.2019.05.059

  16. [16]

      Y. Liu, Y. Liu, Y. Yamauchi, et al., Batteries Supercaps 4 (2021) 1867–1873. doi: 10.1002/batt.202100172

  17. [17]

      B.Y. Tang, L.T. Shan, S.Q. Liang, J. Zhou, Energy Environ. Sci. 12 (2019) 3288–3304. doi: 10.1039/C9EE02526J

  18. [18]

      Y. Liu, X. Wu, Chin. Chem. Lett. 33 (2022) 1236–1244. doi: 10.1016/j.cclet.2021.08.081

  19. [19]

      L.E. Blanc, D. Kundu, L.F. Nazar, Joule 4 (2020) 771–799. doi: 10.1016/j.joule.2020.03.002

  20. [20]

      D. Selvakumaran, A. Pan, S. Liang, et al., J. Mater. Chem. A 7 (2019) 18209–18236. doi: 10.1039/C9TA05053A

  21. [21]

      H. Liang, Z. Cao, F. Ming, et al., Nano Lett. 19 (2019) 3199–3206. doi: 10.1021/acs.nanolett.9b00697

  22. [22]

      Q. Yang, F. Mo, Z. Liu, et al., Adv. Mater. 31 (2019) 1901521.

  23. [23]

      C. Luo, L. Xiao, X. Wu, CrystEngComm 24 (2022) 1387–1393. doi: 10.1039/D1CE01658J

  24. [24]

      N. Li, G. Qu, X. Zhang, et al., Chin. Chem. Lett. 33 (2022) 3272–3276. doi: 10.1016/j.cclet.2021.10.084

  25. [25]

      H. Cui, T. Wang, Z. Huang, et al., Angew. Chem. Int. Ed. 61 (2022) e202203453.

  26. [26]

      Z. Chen, H. Cui, Y. Hou, et al., Chem 8 (2022) 2204–2216. doi: 10.1016/j.chempr.2022.05.001

  27. [27]

      J. Ding, H. Gao, D. Ji, et al., J. Mater. Chem. A 9 (2021) 5258–5275. doi: 10.1039/D0TA10336E

  28. [28]

      X. Chen, L. Wang, H. Li, et al., J. Energy Chem. 38 (2019) 20–25. doi: 10.1016/j.jechem.2018.12.023

  29. [29]

      X. Wang, Y. Li, S. Wang, et al., Adv. Energy Mater. 10 (2020) 200081.

  30. [30]

      Y. Zhang, L. Tao, C. Xie, et al., Adv. Mater. 32 (2020) 1905923. doi: 10.1002/adma.201905923

  31. [31]

      X. Chen, H. Zhang, J.H. Liu, et al., Energy Storage Mater. 50 (2022) 21–46. doi: 10.1016/j.ensm.2022.04.040

  32. [32]

      C. Luo, L. Xiao, X. Wu, Mater. Adv. 3 (2022) 604–610. doi: 10.1039/D1MA00983D

  33. [33]

      P. Ruan, S. Liang, B. Lu, et al., Angew. Chem. Int. Ed. 61 (2022) 202200598.

  34. [34]

      K. Li, Y. Liu, X. Wu, CrystEngComm 24 (2022) 5421–5427. doi: 10.1039/D2CE00741J

  35. [35]

      S. Zhang, H. Tan, X. Rui, et al., Acc. Chem. Res. 53 (2020) 1660–1671. doi: 10.1021/acs.accounts.0c00362

  36. [36]

      D. Kundu, B.D. Adams, V. Duffort, et al., Nat. Energy 1 (2016) 16119. doi: 10.1038/nenergy.2016.119

  37. [37]

      F.W. Ming, H.F. Liang, Y.J. Lei, et al., ACS Energy Lett. 3 (2018) 2602–2609. doi: 10.1021/acsenergylett.8b01423

  38. [38]

      Y. Liu, Y. Liu, X. Wu, et al., ACS Appl. Mater. Interfaces 14 (2022) 11654–11662. doi: 10.1021/acsami.2c00001

  39. [39]

      L. Shan, J. Zhou, W. Zhang, et al., Energy Technol. 7 (2019) 1900022. doi: 10.1002/ente.201900022

  40. [40]

      P. He, Y. Quan, X. Xu, et al., Small 13 (2017) 1702551. doi: 10.1002/smll.201702551

  41. [41]

      Q. Pang, C. Sun, Y. Yu, et al., Adv. Energy Mater. 8 (2018) 1800144. doi: 10.1002/aenm.201800144

  42. [42]

      M. Yan, P. He, Y. Chen, et al., Adv. Mater. 30 (2018) 1703725. doi: 10.1002/adma.201703725

  43. [43]

      Y. Yang, Y. Tang, G. Fang, et al., Energy Environ. Sci. 11 (2018) 3157–3162. doi: 10.1039/C8EE01651H

  44. [44]

      Z. Liu, L. Qin, X. Cao, et al., Prog. Mater. Sci. 125 (2022) 100911. doi: 10.1016/j.pmatsci.2021.100911

  45. [45]

      R.E. John, A. Chandran, M. Thomas, et al., Appl. Surf. Sci. 367 (2016) 43–51. doi: 10.1016/j.apsusc.2016.01.153

  46. [46]

      Z. Duan, X. Tan, Y. Sun, et al., ACS Appl. Nano Mater. 4 (2021) 10791–10798. doi: 10.1021/acsanm.1c02224

  47. [47]

      T. Xiong, Y. Zhang, W.S.V. Lee, J. Xue, Adv. Energy Mater. 10 (2020) 2001769. doi: 10.1002/aenm.202001769

  48. [48]

      Y. Wang, X. Xiao, Q. Li, et al., Small 14 (2018) 1802193. doi: 10.1002/smll.201802193

  49. [49]

      Z. Li, Y. Ren, L. Mo, et al., ACS Nano 14 (2020) 5581–5589. doi: 10.1021/acsnano.9b09963

  50. [50]

      M. Liao, J. Wang, L. Ye, et al., Angew. Chem. Int. Ed. 59 (2020) 2273–2278. doi: 10.1002/anie.201912203

  51. [51]

      G. Fang, J. Zhou, A. Pan, et al., ACS Energy Lett. 3 (2018) 2480–2501. doi: 10.1021/acsenergylett.8b01426

  52. [52]

      J. Cao, D. Zhang, Y. Yue, et al., Mater. Today Energy 21 (2021) 100824. doi: 10.1016/j.mtener.2021.100824

  53. [53]

      W. Yang, L. Dong, W. Yang, et al., Small Methods 4 (2019) 1900670.

  54. [54]

      R. Wei, Y. Lu, Y. Xu, Sci. China Chem. 64 (2021) 1826–1853. doi: 10.1007/s11426-021-1103-6

  55. [55]

      G. Zhang, T. Xiong, M. Yan, et al., Nano Energy 49 (2018) 555–563. doi: 10.1016/j.nanoen.2018.04.075

  56. [56]

      D. Bin, W. Huo, Y. Yuan, et al., Chem 6 (2020) 968–984. doi: 10.1016/j.chempr.2020.02.001

  57. [57]

      Z. Zhang, B. Xi, X. Wang, et al., Adv. Funct. Mater. 31 (2021) 2103070. doi: 10.1002/adfm.202103070

  58. [58]

      Y. Liu, X. Wu, Nano Energy 86 (2021) 106124. doi: 10.1016/j.nanoen.2021.106124

  59. [59]

      S. Huang, S. He, H. Qin, et al., ACS Appl. Mater. Interfaces 13 (2021) 44379–44388. doi: 10.1021/acsami.1c12653

  60. [60]

      Z. Chen, J. Hu, S. Liu, et al., Chem. Eng. J. 404 (2021) 126536. doi: 10.1016/j.cej.2020.126536

  61. [61]

      J. Ma, T. Koketsu, B.J. Morgan, et al., Chem. Commun. 54 (2018) 10080–10083. doi: 10.1039/C8CC04136A

  62. [62]

      T. Koketsu, J. Ma, B.J. Morgan, et al., Nat. Mater. 16 (2017) 1142–1148. doi: 10.1038/nmat4976

  63. [63]

      W. Li, D. Corradini, M. Body, et al., Chem. Mater. 27 (2015) 5014–5019. doi: 10.1021/acs.chemmater.5b01407

  64. [64]

      J. Ding, H. Zheng, H. Gao, et al., Adv. Energy Mater. 11 (2021) 2100973. doi: 10.1002/aenm.202100973

  65. [65]

      P. Gao, P. Metz, T. Hey, et al., Nat. Commun. 8 (2017) 14559. doi: 10.1038/ncomms14559

  66. [66]

      C. Zhu, G. Fang, S. Liang, et al., Energy Storage Mater. 24 (2020) 394–401. doi: 10.1016/j.ensm.2019.07.030

  67. [67]

      Y. Zhang, S. Deng, M. Luo, et al., Small 15 (2019) 1905452. doi: 10.1002/smll.201905452

  68. [68]

      N. Zhang, F. Cheng, Y. Liu, et al., J. Am. Chem. Soc. 138 (2016) 12894–12901. doi: 10.1021/jacs.6b05958

  69. [69]

      X. Wang, B. Xi, X. Ma, et al., Nano Lett. 20 (2020) 2899–2906. doi: 10.1021/acs.nanolett.0c00732

  70. [70]

      T. He, S. Weng, Y. Ye, et al., Energy Storage Mater. 38 (2021) 389–396. doi: 10.1016/j.ensm.2021.03.025

  71. [71]

      K. Zhu, S. Wei, H. Shou, et al., Nat. Commun. 12 (2021) 6878. doi: 10.1038/s41467-021-27203-w

  72. [72]

      J.H. Jo, Y.K. Sun, S.T. Myung, J. Mater. Chem. A 5 (2017) 8367–8375. doi: 10.1039/C7TA01765K

  73. [73]

      J. Ji, H. Wan, B. Zhang, et al., Adv. Energy Mater. 11 (2020) 2003203.

  74. [74]

      P. He, G. Zhang, X. Liao, et al., Adv. Energy Mater. 8 (2018) 1702463. doi: 10.1002/aenm.201702463

  75. [75]

      B. Tang, G. Fang, J. Zhou, et al., Nano Energy 51 (2018) 579–587. doi: 10.1016/j.nanoen.2018.07.014

  76. [76]

      P. He, M. Yan, X. Liao, et al., Energy Storage Mater. 29 (2020) 113–120. doi: 10.1016/j.ensm.2020.04.005

  77. [77]

      N.B. Mahadi, J.S. Park, J.H. Park, et al., J. Power Sources 326 (2016) 522–532. doi: 10.1016/j.jpowsour.2016.07.026

  78. [78]

      Q. Li, T.Y. Wei, K.X. Ma, et al., ACS Appl. Mater. Interfaces 11 (2019) 20888–20894. doi: 10.1021/acsami.9b05362

  79. [79]

      H. Jiang, W. Gong, Y. Zhang, et al., J. Energy Chem. 70 (2022) 52–58. doi: 10.1016/j.jechem.2022.02.030

  80. [80]

      P. Ge, L. Zhang, W. Zhao, et al., Adv. Funct. Mater. 30 (2020) 1910599. doi: 10.1002/adfm.201910599

  81. [81]

      G. Yoo, B.R. Koo, H.R. An, et al., J. Ind. Eng. Chem. 99 (2021) 344–351. doi: 10.1016/j.jiec.2021.04.041

  82. [82]

      Q. Wei, Z. Jiang, S. Tan, et al., ACS Appl. Mater. Interfaces 7 (2015) 18211–18217. doi: 10.1021/acsami.5b06154

  83. [83]

      M. Du, C. Liu, F. Zhang, et al., Adv. Sci. 7 (2020) 2000083. doi: 10.1002/advs.202000083

  84. [84]

      K. Zhu, T. Wu, K. Huang, Adv. Energy Mater. 9 (2019) 1901968. doi: 10.1002/aenm.201901968

  85. [85]

      Y. Tong, S. Su, X. Li, et al., J. Power Sources 528 (2022) 231226. doi: 10.1016/j.jpowsour.2022.231226

  86. [86]

      L. Huang, Y. Xiang, M. Luo, et al., Carbon 185 (2021) 1–8. doi: 10.1016/j.carbon.2021.09.019

  87. [87]

      X. Wang, Y. Zhang, J. Zheng, et al., Appl. Surf. Sci. 568 (2021) 150919. doi: 10.1016/j.apsusc.2021.150919

  88. [88]

      P. Ge, S. Yuan, W. Zhao, et al., ACS Appl. Energy Mater. 4 (2021) 10783–10798. doi: 10.1021/acsaem.1c01754

  89. [89]

      A. Eftekhari, M. Mohamedi, Mater. Today Energy 6 (2017) 211–229. doi: 10.1016/j.mtener.2017.10.009

• 

  Figure 1  A summary of defect engineering strategies for improving electrochemical performance of V-based electrode materials.

  下载: 全尺寸图片 幻灯片
  

  Figure 2  The crystal structures of V-based oxides: (a) V₂O₅; (b) V₂O₃; (c) VO₂(B); (d) V₆O₁₃; (e) V₃O₇·H₂O; (f) V₂O₅·nH₂O.

  下载: 全尺寸图片 幻灯片
  

  Figure 3  The main issues of V-based electrode materials.

  下载: 全尺寸图片 幻灯片
  

  Figure 4  DFT calculation of electrodes with V_o. (a) Zn ion diffusion energy barriers; (b) Zinc ions diffusion pathways along the b tunnel in VO₂ and VO_1.75 electrode. Reproduced with permission [49]. Copyright 2020, American Chemical Society. (c, d) Schematic of Zn²⁺ insertion/extraction for perfect and oxygen deficient vanadium oxide (O_d-VO), respectively. Reproduced with permission [50]. Copyright 2019, Wiley-VCH. (e) Calculated formation energy of two electrodes. (f) DOS of V₂O₅-O defects. Reproduced with permission [52]. Copyright 2021, Elsevier Ltd.

  下载: 全尺寸图片 幻灯片
  

  Figure 5  The electrochemical performances of the electrode with V_o. (a) Cycling performance of the two cathodes at 0.2 A/g. (b) The long-term cycle capability. (c) The Zn²⁺ storage mechanism of Zn/PEDOT-NVO batteries. Reproduced with permission [56]. Copyright 2020, Elsevier Inc. (d) Rate capability at varying current densities. (e) Long life cycling performance. Reproduced with permission [57]. Copyright 2021, Wiley-VCH GmbH.

  下载: 全尺寸图片 幻灯片
  

  Figure 6  The electrochemical performances of electrodes with cationic vacancies. (a) DFT calculated intercalation energies for zinc ions in V₂O₃ with different vacancies. (b) Schematic of the initial charging process for V₂O₃ and the subsequent Zn²⁺ storage process. Reproduced with permission [64]. Copyright 2021, Wiley-VCH. (c) Schematic of Zn²⁺ diffusion in the ZNV with NH₄⁺ vacancies in the interlayers. (d) Low-temperature cycling performance at 2 A/g. Reproduced with permission [70]. Copyright 2021, Elsevier B.V.

  下载: 全尺寸图片 幻灯片
  

  Figure 7  The kinetics process and the cycling performance. (a) The XANES spectra of V K-edge. (b) The Gibbs free energy. (c) Ex situ XRD patterns of V_d-V₂O₃ electrodes at different cut-off voltages during the charge and discharge process. Reproduced with permission [71]. Copyright 2021, Springer Nature. (d) Cycling stability of the electrodes at 5 A/g. Reproduced with permission [79]. Copyright 2022, Elsevier B.V.

  下载: 全尺寸图片 幻灯片
  

  Figure 8  DFT calculation and the cycle capability of electrode with ion doping. (a) Energy barriers for diffusion paths in two electrodes. (b) DOS of the two samples. Reproduced with permission [79]. Copyright 2022, Elsevier B.V. (c) Lattice parameters and (d) the zinc-ion diffusion coefficient of samples. Reproduced with permission [81]. Copyright 2021, Elsevier B.V. (e) Cycle performance at a current rate of 4 A/g. Reproduced with permission [83]. Copyright 2020, Wiley-VCH.

  下载: 全尺寸图片 幻灯片
  

  Figure 9  The kinetic process of dual ion-doped V-based electrodes. (a) Migration path of Zn²⁺ in NaCaVO along the b-axis. (b) The crystal structure of NaCaVO and NaCaVO with no structural water electrodes after Zn-ions intercalation. (c) Zn²⁺ adsorption and diffusion models from surface to bulk. Reproduced with permission [84]. Copyright 2019, Wiley-VCH. (d) The crystal structure of iron ion and alkylammonium cation co-intercalated vanadium oxide. (e) Schematic of the energy storage mechanism. Reproduced with permission [85]. Copyright 2022, Elsevier B.V.

  下载: 全尺寸图片 幻灯片
  

  Figure 10  The advantages of defect engineering and future goals for electrode materials.

  下载: 全尺寸图片 幻灯片

  Table 1.  The electrochemical performance of the optimized vanadium-based electrode materials.

  下载: 导出CSV
•