A chemically self-charging aqueous zinc-ion battery

Self-charging power systems integrating energy harvesting technologies and batteries are attracting extensive attention in energy technologies. However, the conventional integrated systems are highly dependent on the availability of the energy sources and generally possess complicated configuration. Herein, we develop chemically self-charging aqueous zinc-ion batteries with a simplified two-electrode configuration based on CaV6O16·3H2O electrode. Such system possesses the capability of energy harvesting, conversion and storage simultaneously. It can be chemically self-recharged by the spontaneous redox reaction between the discharged cathode and oxygen from the ambient environment. Chemically self-recharged zinc-ion batteries display an initial open-circuit voltage of about 1.05 V and a considerable discharge capacity of about 239 mAh g−1, indicating the excellent self-rechargeability. Impressively, such chemically self-charging zinc-ion batteries can also work well at chemical or/and galvanostatic charging hybrid modes. This work not only provides a route to design chemically self-charging energy storage, but also broadens the horizons of aqueous zinc-ion batteries.

R echargeable batteries are widely used in many fields, such as electric devices and grid-scale energy storage systems [1][2][3][4] . In general, the commercial batteries are often charged by electrical grid. However, in the harsh environment or remote area, the electrical grid is unavailable, which limits the recharging and reuse of batteries. In order to solve this issue, various energy harvesting technologies, such as photovoltaic devices [5][6][7][8][9][10][11] , piezoelectric nanogenerators 12,13 , triboelectric nanogenerators 14,15 , and thermoelectrics [16][17][18] , were integrated with batteries into selfcharging power systems. However, these systems are highly dependent on the energy resources, which are not always available in some environment or during a certain period of time. Furthermore, the configurations of these integrated systems are usually complicated and many extra components (e.g., photoelectrodes or temperature-sensitive redox couples) are required in comparison with the traditional batteries with two-electrode configuration. Therefore, self-charging power systems that possess simplified configuration and are available in various environments must be considered.
Chemical energy stored in molecules is an available energy source and can be converted into electrical energy through redox reaction [19][20][21][22] . In this regard, chemical energy of oxygen that is an abundant resource in air is attracting much more attention in the energy conversion and storage devices, such as metal-air batteries. Furthermore, the metal-air batteries can be further integrated with other energy storage devices and charge them 23,24 . However, in such integrated devices, the metal-air components cannot always compensate the energy consumption of energy storage devices, and they have to be recharged by external power supply to recover when both the metal-air and energy storage components are exhausted 23 . Therefore, they cannot meet the demand in some case, where the batteries are required to be charged directly by the successive chemical energy conversion of oxygen on their cathodes. Recently, a variety of vanadium-based compounds have been developed to serve as the cathode materials of aqueous zinc-ion batteries (ZIBs) due to their open-framework crystal structure and multiple oxidation states of vanadium [25][26][27][28][29][30] . During the discharge process, the insertion of Zn 2+ ions and reduction of vanadium occur simultaneously in vanadium-based ZIBs. Furthermore, it is noted that vanadium-based compounds are also active redox materials and can be oxidized by oxygen in low valence state. Therefore, the discharged vanadium-based cathodes would be oxidized by oxygen in the ambient environment, like a charge process. As a result, self-charging ZIBs that simultaneously possess energy conversion and storage functions would be achieved.
Inspired by this, we develop a chemically self-charging aqueous ZIBs system, in which the chemical energy harvesting, conversion, and storage are integrated in a single CaV 6 O 16 ·3H 2 O (CaVO) cathode. Such system possesses a similar two-electrode configuration with the conventional ZIBs. It can harvest energy from ambient environment through spontaneous redox reaction, and then convert chemical energy into electrical energy and store them in ZIBs. Therefore, the resultant ZIBs can be self recharged by directly exposing CaVO cathodes to air without any external power supply. This design would provide a promising research direction for the next-generation self-powered systems.

Results
Preparation and characterization of CaVO nanoribbons. The CaVO nanoribbons were synthesized via a one-step hydrothermal method 31 . They display a size of several hundred micrometers in length and 200-500 nm in width (Fig. 1a, d). Their crystalline phase was further understood by X-ray diffraction (XRD) and the corresponding Rietveld refinement, as shown in Fig. 1b. The results show that the diffraction peaks can be well indexed to the monoclinic CaVO phase with space group of A2/m (JCPDS 33-317) and lattice parameters of a = 12.2533 Å, b = 3.5149 Å, c = 18.3874 Å, α = γ = 90.0°, and β = 118.642°. Thermogravimetric analysis (TGA) also confirms that three molecular waters exist in a formula unit ( Supplementary Fig. 1, Supplementary Note 1). Furthermore, it is noted that the XRD pattern exhibits multiple (00l) reflections and the intensity of (002) reflection is extremely strong. It suggests that CaVO nanoribbons possess a typical layered structure, which is constructed by the stacking of V 6 O 16 framework and the hydrated Ca atoms act as "pillars" between the V 6 O 16 layers to stabilize the layered structure ( Fig. 1c) 32,33 . In addition, the lattice fringes with d-spacing of 0.205 nm is observed in the high-resolution transmission electron microscopy (HRTEM) image, corresponding to the (008) plane of CaVO (Fig. 1e), which is in good agreement with the XRD result. Moreover, the transmission electron microscopy (TEM) elemental mapping images clearly show that Ca, V, and O element are homogeneously distributed in CaVO nanoribbons (Fig. 1f).
Electrochemical performance of Zn/CaVO batteries. The favorable morphological features, open framework and expanded interlayer spacing (0.819 nm) would contribute to the fast kinetics of Zn 2+ ions insertion/extraction in CaVO (refs. 26,[34][35][36], thereby enhancing their electrochemical performance. The electrochemical performance of CaVO nanoribbons was investigated in coin cells. In their cyclic voltammetry (CV) curves, there are two pairs of reduction/oxidation peaks at 0.75/0.95 and 0.47/0.66 V (Fig. 2a). They can be ascribed to a two-step redox reaction associated with Zn 2+ ion insertion/extraction (corresponding analysis see the following energy storage mechanism section), corresponding to the valence change of vanadium from V 5+ to V 4+ and V 4+ to V 3+ , respectively 26,37,38 . Furthermore, the CV curves display similar shape after first cycle, suggesting the high reversibility of the charge/discharge process of Zn/CaVO batteries, which is further confirmed by the reversible galvanostatic charge/discharge (GCD) profiles (Fig. 2b). Besides, Zn/CaVO batteries deliver a high initial discharge capacity of 300 mA h g −1 at 0.1 A g −1 and an average operating voltage of~0.7 V versus Zn 2+ /Zn, corresponding to an insertion of~3.6 Zn per unit formula of CaVO. Impressively, even the current density is up to 30 A g −1 , a capacity of 62 mAh g −1 is still achieved (Fig. 2c). When the current density recovers from 30 to 0.2 A g −1 after 70 cycles, the capacity is able to recover to the initial capacity of 290 mAh g −1 . Such excellent rate capability of Zn/CaVO batteries significantly depends on their electrochemical kinetics, as suggested by CV measurements at different scan rates (see Supplementary Fig. 2 and detailed calculation in Supplementary Note 2). The high surface-controlled capacity contributions result in the fast Zn 2+ ion diffusion, enabling the high rate capability as well as outstanding cycling stability [39][40][41][42] . The capacity of Zn/ CaVO batteries is still 263 mAh g −1 after 100 cycles at 0.5 A g −1 (Supplementary Fig. 3). Impressively, even after 10,000 cycles at a high current density of 10 A g −1 , there is no degradation in their capacity, remaining stable at~170 mA h g −1 (Fig. 2d). During initial 200 cycles, the capacity is gradually increased, which is attributed to the activation of CaVO at a high current density of 10 A g −1 (refs. 43,44 ).
Energy storage mechanism of Zn/CaVO batteries. The fast reaction kinetics and excellent electrochemical performance depend on the energy storage mechanism of Zn/CaVO batteries. To further understand the energy storage mechanism of Zn/ CaVO system, various measurements, including in situ/ex situ XRD, ex situ TEM, X-ray photoelectron spectrometry (XPS) and  c Rate capability at various current densities. d Cycling performance at 10 A g −1 . e In situ XRD patterns of (002) reflection and corresponding GCD curves at 0.2 A g −1 during the first cycle. f XPS spectra of Zn 2p at initial, fully discharged, and charged states. g V K-edge XANES curves at initial, fully discharged, and charged states with reference to the standard V 2 O 3 , VO 2 , and V 2 O 5 .
NATURE COMMUNICATIONS | https://doi.org/10.1038/s41467-020-16039-5 ARTICLE X-ray absorption near-edge spectroscopy (XANES) were utilized to characterize the CaVO cathodes at the selected states of charge/ discharge process. It is noted that the XRD characteristic diffraction peaks of (002) and (004) plane shift slightly toward high degree during the discharge process, corresponding to the decrease of interlayer spacing (Fig. 2e, Supplementary Figs. 4 and 5). It is ascribed to the strong electrostatic interaction between intercalated Zn 2+ ions and V 6 O 16 layers 38,45 . In contrast, the ( 206) reflection shifts slightly toward low degree, corresponding to the expansion of the interlayer spacing of ( 206) plane, which could arise from the reduction of V 5+ /V 4+ upon Zn 2+ ion insertion and the resultant increase in the V-V bond distance between the layers 43 . Furthermore, the disorder in structure caused by Zn 2+ ion insertion would result in the broadening of ( 206) and (006) reflections. Reversibly, during the subsequent charge process, these characteristic diffraction peaks gradually return to their original state with the extraction of Zn 2+ ions. This reversible change of interlayer spacing is also confirmed by the HRTEM images ( Supplementary Fig. 6). Therefore, the energy storage mechanism of Zn/CaVO batteries is the insertion/ extraction of Zn 2+ ions into/from the CaVO (Supplementary Fig. 7, Supplementary Note 3), which is similar to the case of conventional ZIBs (refs. 30,46 ). Moreover, this Zn 2+ ion insertion/ extraction mechanism is further substantiated by the XPS analysis of Zn 2p peaks (Fig. 2f). The peaks of Zn 2p are not detected in the initial CaVO cathode, whereas strong peaks are observed at the fully discharged state, corresponding to the intercalated Zn 2+ ions. In contrast, at the fully charged state, the intensity of Zn 2p peaks is significantly weakened, suggesting that most of Zn 2+ ions are extracted from the CaVO. It is also proved by TEM elemental mapping images, where Zn element is uniformly distributed in the nanoribbons at fully discharged state and then almost disappears at fully charged state ( Supplementary Fig. 8). The insertion/extraction of Zn 2+ ions is accompanied by the valence change of vanadium in CaVO, as illustrated in V K-edge XANES curves of CaVO cathodes at different charge/discharge states (Fig. 2g). Compared with the initial state, the main absorption edge slightly shifts toward lower binding energy at fully discharged state, suggesting that the average oxidation state of vanadium is reduced due to the insertion of Zn 2+ ions [47][48][49] . Subsequently, the position of absorption edge reversibly shifts back toward higher energy at fully charged state, indicating the oxidation of vanadium caused by the extraction of Zn 2+ ions from CaVO. The above insertion/extraction of Zn 2+ ions during the charge/discharge process can also be reflected by the reversible intensity change of pre-edge peak in XANES (Fig. 2g), which is sensitive to the change of the local symmetry of V atoms 50 . Based on the above results and discussion, the overall electrochemical reaction of the Zn/CaVO batteries can be described as follows: Cathode: Anode: Overall: Chemically self-charging mechanism. The CaVO cathodes exhibit excellent Zn 2+ ion storage performance, and the reduction/oxidation of vanadium occurs during the Zn 2+ ion insertion/ extraction. In the galvanostatic charging process, electrons are released from the CaZn 3.6 V 6 O 16 ·3H 2 O (CaZn 3.6 VO) cathode. As a result, vanadium in CaZn 3.6 VO is oxidized and the Zn 2+ ions are extracted from the layered structure simultaneously. In this process, the driving force of the release of electron from CaZn 3.6 VO is generally the external power supply. In addition to above-mentioned electrochemical oxidation reaction, other strategies that can realize the electron transfer from CaZn 3.6 VO would be also promising to carry out the charging process of the ZIBs based on CaZn 3.6 VO cathode. It is well known that redox reaction is an effective and straightforward approach to realize the electron transfer, which is driven by the redox potential difference (ΔE) between reactants 51,52 . In the case of CaZn 3.6 VO, the redox potential in this system can be obtained from the CV curves of Zn/CaVO batteries (Fig. 2a) 53 , in which the minimum reduction peak potential of CaVO versus Zn 2+ /Zn is 0.47 V.
According to the Nernst equation, the calculated redox potential of CaZn 3.6 VO is −0.27 V versus standard hydrogen electrode (SHE). Theoretically, CaZn 3.6 VO can be oxidized spontaneously by the oxidants with a higher potential than −0.27 V versus SHE. Among various oxidants, O 2 is common and abundant in the air, the standard electrode potentials (E θ ) of which are~0.40 V and 1.23 V versus SHE in the neutral and acidic medium, respectively. Owing to the difference in redox potential between O 2 and CaZn 3.6 VO, the CaZn 3.6 VO tends to release electrons to be oxidized and O 2 can accept these electrons to be reduced simultaneously (Fig. 3a). Therefore, if the redox reaction between CaZn 3.6 VO and O 2 could take place, the oxidation of vanadium in CaZn 3.6 VO would be realized, and the Zn 2+ ions would be extracted from the layered structure to balance the charge at the same time. As a result, the fully discharged product CaZn 3.6 VO would recover to its charged states CaZn 3.6−x V 6 O 16 ·3H 2 O (CaZn 3.6−x VO) without any external power supply. In the Zn/ CaVO batteries, acidic 4 M Zn(CF 3 SO 3 ) 2 electrolyte was used. In an open device, O 2 could be dissolved into such electrolyte and imported to the discharged product CaZn 3.6 VO, realizing the redox reaction between CaZn 3.6 VO and O 2 . In order to validate the spontaneity of the redox reactions between CaZn 3.6 VO and O 2 in the acidic 4 M Zn(CF 3 SO 3 ) 2 electrolyte, we designed a galvanic cell 54,55 ðÀÞCaZn 3:6 VOjCaZn 3:6Àx VOjjH 2 OjO 2 jPtðþÞ As shown in Fig. 3b, the CaZn 3.6 VO electrode served as anode, which was in 4 M Zn(CF 3 SO 3 ) 2 electrolyte without the dissolved oxygen and sealed under Ar. The platinum wire was used as cathode, which was immersed in 4 M Zn(CF 3 SO 3 ) 2 solution containing dissolved oxygen. In this system, a cell voltage of 0.38 V was observed. According to the relationship between thermodynamic function and cell voltage: where, ΔG, F, and E are the free energy change, Faraday constant, and cell voltage, respectively, the free energy change is less than zero in this case, suggesting that the redox reaction between CaZn 3.6 VO and O 2 can take place spontaneously in 4 M zinc trifluoromethanesulfonate (Zn (CF 3 SO 3 ) 2 ) solution at ambient condition.
To gain insight into the process of such redox reaction, various ex situ characterizations were carried out to investigate the structure and composition evolution of CaZn 3.6 VO electrodes that were immersed in 4 M Zn (CF 3 SO 3 ) 2 to react with the dissolved oxygen for different times. With the extension of immersion time from 0 (fully discharged state) to 36 h, the V 2p peak in the XPS spectra gradually shifts toward higher binding energy (Fig. 3c), where the intensity of V 5+ peak is significantly enhanced and V 3+ peak disappears in comparison with those of initial CaZn 3.6 VO (Fig. 3d), suggesting the oxidation of vanadium in CaZn 3.6 VO during the redox reaction process. Simultaneously, to balance the charge of CaZn 3.6 VO, the intercalated Zn 2+ ions are extracted from the layered structure, resulting in the increase of the interlayer spacing of CaZn 3.6 VO, as proved by the XRD pattern. Furthermore, it is worth noting that the amount of extracted Zn 2+ ions of CaZn 3.6 VO can be effectively controlled by varying the oxidation time in this system. The (002) reflection of oxidized CaZn 3.6 VO gradually shifts toward lower degree with the extension of oxidation time (Fig. 3e, Supplementary Figs. 5 and 9, Supplementary Note 4). According to the Bragg equation (2dsinθ = nλ, n = 1, λ = 0.154 nm), the interlayer spacing of (002) plane is calculated and increases from 7.75 to 8.10 Å after oxidation for 42 h (Fig. 3f). In addition, it is noted that V 2p XPS spectra and the (002) reflection will not further shifts when the oxidation time exceeds 36 h (Fig. 3c, e), suggesting the oxidation of vanadium in CaZn 3.6 VO and the extraction of Zn 2+ ions would be finished within 36 h.
In addition to O 2 , it is noted that H 2 O also plays an important role in the redox reaction process. In order to demonstrate this, the CaZn 3.6 VO electrodes were immersed in acetonitrile containing dissolved oxygen. In the absence of H 2 O, the oxidation of vanadium is not detected in the resultant CaZn 3.6 VO, as reflected by the V 2p XPS spectra, where V 2p region remains unchanged in comparison with that of the initial CaZn 3.6 VO ( Supplementary  Fig. 10). Furthermore, there is no shift in the XRD characteristic peak of the resultant CaZn 3.6 VO ( Supplementary Fig. 11 37,44,56,57 . Based on the above discussion, in the neutral deionized water, the redox reaction between CaZn 3.6 VO and O 2 can be summarized as below: Different from the case in neutral deionized water, in the acidic 4 M Zn(CF 3 SO 3 ) 2 electrolyte, O 2 is reduced to H 2 O in the presence of H + ions, and the CaZn 3.6 VO is oxidized along with the extraction of Zn 2+ ions. The redox reaction mechanism can be expressed by the following half-cell reactions: The continuous consumption of H + ions promotes the water dissociation, thus producing additional H + ions and OH − ions: The additional H + ions also participate in the oxygen reduction reaction (O 2 + 4 H + + 4e − → 2H 2 O). The generated OH − ions react with electrolyte ions (Zn 2+ and CF 3 SO 3 − ) and Zn 2+ ions that are extracted from the oxidation reaction of CaZn 3.6 VO to form Zn x+y (CF 3 The overall reaction can be expressed as: Self-charging performance of ZIBs. The oxidation of vanadium and extraction of Zn 2+ ions in CaZn 3.6 VO can spontaneously occur in the 4 M Zn(CF 3 SO 3 ) 2 electrolyte containing dissolved oxygen. Consequently, the fully discharged product CaZn 3.6 VO can recover to its charged states CaZn 3.6−x VO through spontaneous redox reaction, which could be considered as a chemical self-charging process (Fig. 4a). When the oxidized product CaZn 3.6−x VO electrode directly act as the cathode of ZIBs, the discharge process will take place due to the Zn 2+ ion chemical potential difference between CaZn 3.6−x VO cathode and Zn anode, where anodic Zn is dissolved to form Zn 2+ ions and then intercalate into the CaZn 3.6−x VO cathode (Fig. 4b) 51 . Simultaneously, electrons flow out of the anode to cathode through the external circuit to maintain electrical neutrality. In order to investigate the electrochemical performance of aqueous ZIBs based on CaZn 3.6−x VO cathodes, their galvanostatic discharge curves were measured. The open-circuit voltage (OCV) of the Zn/ CaZn 3.6−x VO batteries rises continually along with extending the oxidation time of CaZn 3.6 VO (Fig. 4c, d) (Fig. 4e). During the repeated chemical charging/galvanostatic discharging cycles, CaZn 3.6−x VO can be reversibly converted with CaZn 3.6 VO ( Supplementary Fig. 5). Different from CaZn 3.6−x VO, the Zn x+y (CF 3 SO 3 ) 2y (OH) 2x is progressively generated and aggregated on the electrode, which will inevitably increase electrochemical impedance and hinder the insertion of Zn 2+ ions during subsequent cycles, resulting in the capacity degradation (Fig. 4f). Importantly, after the electrochemical charging process, most Zn x+y (CF 3 SO 3 ) 2y (OH) 2x would be decomposed and disappear from the electrode (Supplementary Fig. 27, Supplementary  Note 12). Therefore, the chemical-charging ability and capacity will recover to a large extent after the electrochemical charging process. However, it is noted that there is still a capacity decay even after several chemical-recharging/galvanostatic-recharging cycling (Fig. 4f). It could be ascribed to the structural stress generated from continuous extraction/insertion of Zn 2+ ions, during the repeated chemical charging/galvanostatic discharging cycles 25,34 .
According to the redox reaction mechanism, O 2 and H 2 O are essential in the chemical charging process. Considering that water-based electrolyte was utilized in aqueous ZIBs and the Zn anode was stable in ambient air 58-60 , we designed "open" cointype aqueous ZIBs, where the cathode caps were predrilled with holes to import O 2 into electrolyte and then reacted with CaZn 3.6 VO to realize the chemical charging process in situ. In such chemically self-charging ZIBs, the CaVO cathode simultaneously serves as an electrode for energy conversion and storage. After the batteries were fully discharged, the gas diffusion window was opened to ensure that O 2 could continuously diffuse into electrolyte and react with CaZn 3.6 VO cathode. These "open" coin-type ZIBs still exhibit superior self-rechargeability, as reflected by the repeated chemical charging/galvanostatic discharging cycles (Fig. 5a). Furthermore, the chemical charging/ galvanostatic discharging process is also reversible. In addition, such chemically self-charging ZIBs can work at multiple charge/ discharge modes. When they are chemically charged, the OCV slowly reaches~0.77 V (Fig. 5b, Supplementary Fig. 28). After the batteries are exhausted, they can be chemically recharged again. Impressively, when the external power supply is available, the batteries can be galvanostatically recharged from self-charged state (0.77 V) to the fully charged state (1.5 V). Furthermore, it is worth mentioning that the operation of chemical charging process has almost no effect on the subsequent galvanostatic charging/discharging process. Similar GCD behavior is observed after several chemical charging cycles (Fig. 5b, Supplementary  Fig. 29), indicating the excellent reusability of these chemically self-charging ZIBs. To demonstrate the feasibility of the resultant chemically self-charging ZIBs via a simple visual cue, two "open" coin-type batteries were connected in series to power a timer. After the batteries were exhausted and then exposed to the air, they could be chemically recharged to light up the liquid crystal display from the timer (Fig. 5c), suggesting their availability as chemically self-charging energy storage devices.

Discussion
The recharging and reuse of commercial batteries is often limited in the harsh environment or remote area, where electrical grid is unavailable. Therefore, self-charging power systems that integrate energy harvesting devices and batteries together must be considered. The rational design of self-charging power systems mainly depends on the fabrication of innovative electrodes and the construction of simplified device configurations. In our case, the favorable nanoribbon morphology, open framework and expanded interlayer spacing endow CaVO with the fast kinetics of Zn 2+ ion insertion/extraction in the layered structure. As a result, Zn/CaVO batteries exhibit a high initial discharge capacity (300 mAh g −1 at 0.1 A g −1 ), excellent rate performance (62 mAh g −1 at 30 A g −1 ) and outstanding cycling stability (100% capacity retention after 10,000 cycles). Owing to the redox potential difference between the fully discharged product CaZn 3.6 VO and O 2 , the redox reaction between them will occur, where CaZn 3.6 VO releases electrons to be oxidized and O 2 accepts these electrons to be reduced simultaneously. Meanwhile, the Zn 2+ ions are extracted from CaZn 3.6 VO to balance the charge. As a result, the oxidation of vanadium and extraction of the Zn 2+ ions take place in CaZn 3.6 VO during above redox process at ambient condition. Clearly, the fully discharged product CaZn 3.6 VO recovers to its charged states in such redox process instead of external power. Therefore, Zn/CaZn 3.6−x VO system can harvest chemical energy from the ambient environment and convert it to electrical energy stored in batteries through the chemical charging process. They can be self-charged to~1.05 V without any external power supply and deliver a considerable discharge capacity of 239 mAh g −1 . Furthermore, the chemical charging/galvanostatic discharging process is also reversible in such open battery design. More importantly, chemically self-charging ZIBs are compatible with different chemical or/and galvanostatic charging hybrid modes. Chemically self-charging ability ensures that Zn/CaVO batteries are available at various conditions. It is different from the conventional ZIBs and zinc-air batteries, which are only charged by external power supply. In the case of rechargeable zinc-air battery 61 , O 2 is an oxidant and reduced to OH − ions via a reduction reaction at the air electrode during the discharge process. The generated OH − ions then migrate to the zinc electrode, forming insoluble zinc oxide (ZnO) at supersaturated Zn (OH) 2-4 concentrations. In its charge process, the OH − ions are oxidized to generate O 2 , which is driven by external power supply. However, in our case, during the discharge process, Zn 2+ ions insert into the CaVO, which is a characteristic behavior. In this process, O 2 does not participate in the reaction. During the self-charging process, the discharge product CaZn 3.6 VO will be oxidized by O 2 due to the difference in redox potential between O 2 and CaZn 3.6 VO, replacing the electric energy to make the oxidization of discharged product and realizing the self-charging. However, during the chemical charging process, the Zn 2+ ions will not be redeposited on the Zn anode and the formation of byproduct Zn x+y (CF 3 SO 3 ) 2y (OH) 2x will consume Zn 2+ ions from the anode irreversibly, limiting the long-term chemical charging/galvanostatic discharging cycling. Significantly, the Zn x+y (CF 3 SO 3 ) 2y (OH) 2x can be decomposed by a electrochemical charging process and Zn 2+ ions could be also redeposited on the Zn anode. This work paves the way for the potential application of ZIBs in self-charging systems, and the chemical charging strategy provides a promising research direction for the selfpowered systems.
Preparation of CaVO nanoribbons. CaVO nanoribbons were fabricated by a simple hydrothermal method. A total of 117 mg of NH 4 VO 3 was added into 30 mL deionized water and stirred at 80°C for 20 min to obtain a clear yellowish solution. Meanwhile, 666 mg of CaCl 2 and 100 mg SDS were dissolved in another 30 mL deionized water, and stirred at 60°C for 10 min to achieve a transparent solution. Subsequently, the CaCl 2 /SDS solution was added into NH 4 VO 3 solution under stirring. Finally, the above mixture solution was transferred into a 100 mL Teflonlined autoclave and heated at 160°C for 10 h. After cooling to room temperature, the brownish-red precipitates were washed with deionized water and freeze-dried.
Electrochemical measurement. Electrochemical performance of CaVO nanoribbons was measured in CR2032 coin cells. The cathode was prepared by mixing the CaVO nanoribbons, SWCNTs, and PVDF in a weight ratio of 7:2:1 by NMP. Then, the slurry was coated on stainless-steel meshes and dried at 60°C for 12 h under vacuum. The mass loading of CaVO in the cathode is~1 mg cm −2 . Commercial glass fiber and zinc foil with a thickness of 30 μm were employed as the separator and anode, respectively. Aqueous 4 M Zn (CF 3 SO 3 ) 2 solution was used as electrolyte since the high-concentration electrolyte would not only alter the solvation and transporting behaviors of cations/anions to enhance stability and kinetics, but also reduce the water activity and water-induced side reactions 48,62-64 . They were assembled into CR2032 coin cells by a traditional method. The GCD tests were performed on a battery test system (LAND CT2001A) with a voltage window of 0.3-1.5 V. CV were measured using an electrochemical workstation (CHI660E) in a voltage window from 0.3 to 1.5 V.
To understand the mechanism of redox reaction between CaZn 3.6 VO and O 2 , the Zn/CaVO batteries were discharged to 0.3 V at a current density of 0.1 A g −1 . Subsequently, the fully discharged cathodes (CaZn 3.6 VO) were washed by deionized water and then immersed in 4 M Zn(CF 3 SO 3 ) 2 solution or water for different times to react with the dissolved oxygen. After that, the treated CaZn 3.6-x VO cathodes were assembled into coin cells again for the electrochemical performance measurement. In the in situ chemical charging process, the cathode cap was predrilled with a hole to import oxygen. The cell was first sealed with a Kapton membrane, which was subsequently wiped off to enable O 2 to pass through the hole. Furthermore, to avoid the excessive volatilization of water from the electrolyte, the chemical charging process was carried out under a high humidity condition (>60%). After self-charging, the cell was sealed again. The specific capacities were calculated based on the mass of the active material CaVO of cathodes.
Characterization. The morphologies of CaVO nanoribbons and cathodes were characterized via field-emission scanning electron microscopy (SEM, JEOL JSM7500F, 5 kV and Phenom XL, 15 kV). The SEM-energy dispersive spectroscopy (EDS) of the samples are collected with Phenom XL at an acceleration voltage of 15 kV. The microstructure was characterized by TEM (FEI Talos F200X and FEI Talos F200X G2) equipped with EDS mapping at an acceleration voltage of 200 kV. The crystalline structure of samples was determined by XRD (Rigaku SmartLab) with Cu Kα radiation (λ = 0.15405 nm). TGA (Netzsch STA 449 F3 Jupiter analyzer) was carried out in an Ar flow from room temperature to 600°C at a heating rate of 10°C min −1 . In situ XRD experiments were performed using home-made cells that were designed with Be window for X-ray penetration. XPS (PerkinElmer PHI 1600 ESCA) was used to characterize the composition and surface oxidation state of the electrodes. V K-edge XANES spectra were collected at the beamline 14W1 in Shanghai Synchrotron Radiation Facility. The solid state 1 H nuclear magnetic resonance ( 1 H NMR) was taken from a 400 MHz superconducting NMR spectrometer (AVANCE ||| 400).

Data availability
The authors declare that all the relevant data are available within the paper and its Supplementary Information file or from the corresponding author upon reasonable request.