Probing Mechanistic Insights into Highly Efficient Lithium Storage of C60 Fullerene Enabled via Three‐Electron‐Redox Chemistry

Abstract Renewable organic cathodes with abundant elements show promise for sustainable rechargeable batteries. Herein, for the first time, utilizing C60 fullerene as organic cathode for room‐temperature lithium‐ion battery is reported. The C60 cathode shows robust electrochemical performance preferably in ether‐based electrolyte. It delivers discharge capacity up to 120 mAh g−1 and specific energy exceeding 200 Wh kg−1 with high initial Coulombic efficiency of 91%. The as‐fabricated battery holds a capacity of 90 mAh g−1 after 50 cycles and showcases remarkable rate performance with 77 mAh g−1 retained at 500 mA g−1. Noteworthily, three couples of unusual flat voltage plateaus recur at ≈2.4, 1.7, and 1.5 V, respectively. Diffusion‐dominated three‐electron‐redox reactions are revealed by cyclic voltammogram and plateau capacities. Intriguingly, it is for the first time unveiled by in situ X‐ray diffraction (XRD) that the C60 cathode underwent three reversible phase transitions during lithiation/delithiation process, except for the initial discharge when irreversible polymerization in between C60 nanoclusters existed as suggested by the characteristic irreversible peak shifts in both in situ XRD pattern and in situ Raman spectra. Cs‐corrected transmission electron microscope corroborated these phase evolutions. Importantly, delithiation potentials derived from density‐functional‐theory simulation based on proposed phase structures qualitatively consists with experimental ones.


Introduction
Li-ion batteries (LIBs) have become prevailing mobile power sources and play indispensable roles in revolutionizing modern society owing to their high energy density merit, with applications spanning consuming electronics, lightweight smart devices, electrical transportation vehicles and stationary energy storage systems. [1][2][3][4][5][6][7][8] However, one of the challenges impeding the advancement of LIBs is the unsustainability of current commercial cathode materials, including LiMn 2 O 4 , LiFePO 4 , and Li(Ni, Co, Mn)O 2 , on account of limited reserves of lithium and transition metals, the eco-malignity of cobalt, high cost, problematic recyclability and adverse environmental impacts. [9,10] In recent years, the metal-free organic (MFO) materials composed of abundant elements (C, H, O, N, S) have emerged as novel cathode materials for rechargeable batteries due to their renewability, structural diversity and componential tunability over the aforementioned conventional cathode materials. [11][12][13][14][15][16][17] These MFO cathode materials mainly fall into three types: n-type, p-type, and bipolar depending on the accessible charge-state of the electroactive sites within. [12,18] In the charging process, the p-type materials, such as polyphenylamine, coronene, and its analogues, can be oxidized accompanied by anion (such as PF 6 − and ClO 4 − ) intercalation for dual-ion batteries (DIBs). [19,20] In the discharging process, n-type materials such as cyclohexanehexone, calix [4]quinone, calix [6]quinone and polydopamine can be reduced to anions concurring with Li-ion intercalation for LIB. [21][22][23][24] Noteworthily, some n-type MFO cathode materials for LIBs are molecular crystals with multi-carbonyls and they share a common trait of multi-electron-redox chemistry caused by the reactions of multicarbonyls with lithium ions, which renders them higher capacity than those p-type ones with less electron transfer for DIBs. Intriguingly, fullerenes, C 60 being the most common form, discovered by Kroto et al. in 1985 as an unusual form of carbon allotrope with a Buckyball cage-like molecular structure comprising twenty pentagonal and twelve hexagonal fused rings of single or double bonded carbon atoms, are known as bipolar molecular crystals and peculiarly display multi-electron-redox behavior. [25][26][27][28][29] Although fullerenes have been studied as electrode materials for rechargeable batteries including redox flow batteries, little work has been reported of their use as cathode material for LIB. [30][31][32][33] Previously reported DIB and magnesiumion battery (MIB) with C 60 fullerene as cathode material delivered reversible capacity below 50 mAh g −1 and exhibited less than ideal cycling stability. [13,34,35] Moreover, the role and battery chemistry of multi-electron-redox in these fullerene batteries remain elusive. [36] In this work, using C 60 as a prototype of fullerenes, we have successfully fabricated the proof-of-concept rechargeable LIB with C 60 fullerene serving as cathode material that can operate in room temperature and revealed the underlying mechanisms through a series of in situ/ex situ characterizations along with DFT computation. The C 60 cathode exhibits prominent performance for LIB with high initial Coulombic efficiency (CE) and a capacity over twice as those of the fullerenes reported for DIB and MIB, which is also superior among organic cathode materials without carbonyls including most p-type organic cathode materials for DIB and even comparable to some n-type materials for LIB. [11,19,21,35,37] Our work could render further insight into the fullerene battery chemistry and can be enlightening for their applications in rechargeable batteries and beyond.

Results and Discussions
The pristine C 60 in our study is brownish powder that was used as received without further treatment. Its morphology at microscale is characteristic of bulk secondary particles closely stacked from submicro-sized flakes as revealed by Scanning electron microscopy (SEM) in Figure S1, Supporting Information. As shown in the X-ray diffraction (XRD) pattern in Figure S2, Supporting Information, three major peaks located at ≈10.8°, 17.7°, and 20.8°are ascribed to (111), (220), and (311) crystal planes in face-centered cubic (FCC) structure belonging to the Fm3 space group, indicative of single crystalline trait of C 60 and consistent with previously reported work. [30] The distinct lattice fringes and their spacings in the high-resolution TEM image, along with the FFT pattern in the upper right inset, correspond well to the XRD results, as shown in Figure 1. Besides, C 60 nanoclusters were also distinguished as shown in the upper left inset.  The pure electrochemistry of C 60 fullerene has been well established since its discovery. [27] However, little attention has been concentrated on its electrochemical behavior in batteries and the knowledge pertaining to battery chemistry remains limited. [30,35,36,38,39] Therefore, a main objective of this work is to investigate the electrochemical behavior of C 60 as LIB cathode material. The schematic architecture of C 60 LIB and its operating principle was illustrated in Figure 2. We began by studying the dependence of electrochemical behavior in half cells. Figure 3a exhibit typical galvanic discharge-charge (GDC) Figure 3. Electrochemical behavior and performance of C 60 as cathode material in half cells measured at room temperature: a) the GDC voltage profiles for different electrolytes at 1 C current rate, inset are corresponding dQ/dV curves, here V stands for voltage, b) voltage profiles of initial 2 GDC cycles for EL-3 electrolyte, c) differential capacitance curves derived from voltage profiles of (b), d) rate capability of C 60 cathode at various current rates, e) discharge voltage profiles for the third cycles at various current rates, f) cycling performance of C 60 cathode in varied electrolytes, here C.E. denotes Coulombic efficiency.
voltage profiles at 1 C (refers to 100 mA g −1 ) of current rate after 2 cycles at 0.2 C in three different electrolytes. For EL-1, the electrolyte of 1 M LiPF 6 dissolved in mixed solvent of ethylene carbonate, diethyl carbonate, and dimethyl carbonate (1:1:1 in volume), the discharge-charge voltage profiles of C 60 displays no voltage plateaus, similar to previous work. [30] Both the CE (here defined as the ratio of charge capacity to discharge counterpart) of 33.5% and reversible capacity of less than 20 mAh g −1 are very low. This could be rationalized by the deterioration of C 60 from the irreversible parasitic reactions with electrolyte in the first several cycles, which contributes to the interfacial capacitance. Further details are provided in Figure S3a, Supporting Information. On the contrary, multiple distinct voltage plateaus are observed in discharge-charge voltage profiles for EL-2, the electrolyte of 1 M LiClO 4 in the mixture of dimethyl ether (DME) and dioxolane (DOL) (1:1 in volume) or EL-3, the electrolyte of 1 M LiTFSI in DME and DOL (1:1 in volume). The three major voltage plateaus are presented altogether for both the discharge and charge process, including the high plateaus at ≈2.5 V, the middle plateaus between 1.6 and 2.1 V, and the low plateaus near 1.5 V. The GDC CE of C 60 for EL-2 and EL-3 are 128.8%, and 98.7%, respectively. The much higher CE near 100% and much higher discharge capacity of ≈107 mAh g −1 demonstrates excellent electrochemical reversibility and redox activity of the C 60 cathode at such voltage range at 1 C for the EL-3 electrolyte, whereas the abnormally high CE for EL-2 may result from shuttle effect of dissolved active materials, presumably driven by side chemical and/or electrochemical reactions of the lithiated C 60 with ClO 4 − . [40,41] Underlying redox difference is reflected in corresponding dQ/dV curves in the inset of Figure 3a, where no redox peaks are observed and the curves are almost flat for EL-1 while the redox peaks are quite strong for EL-2 and EL-3. Further, half cells with the C 60 cathode were tested in 0.1 M LiPF 6 in DME. Surprisingly, we find that the voltage profiles also exhibit distinct plateaus as displayed in Figure S3b, Supporting Information. As observed in the CV curves in Figure S3c, Supporting Information, below 1.2 V extra reduction emerges and there are no more redox peaks for C 60 cathode after the first two cycles, due to the irreversible strong reduction peak ≈0.7 V where irreversible intense parasitic interfacial reactions could occur with the collapse of C 60 structure. And this leads to the eventual loss of redox activity for C 60 . All the above results manifest that, apart from the voltage range, the electrochemical redox behavior of C 60 as cathode is strongly dependent on the electrolyte, with more influence from the solvent than from the solvate. More specifically, the DME-based electrolyte rather than the carbonate-based electrolyte is preferable for the redox of the C 60 cathode in LIB.
Furthermore, the electrochemical properties were evaluated for the C 60 cathode in half cells with the electrolyte of EL-3. As Figure 3b shows, in the initial cycle at 0.2 C, the C 60 serving as cathode material can deliver capacity as high as 121.2 mAh g −1 corresponding to an energy density above 200 Wh kg −1 with remarkable CE of 90.8%, which are superior to many other MFO cathode materials for LIBs including polydopamine, cyclohexanehexone, and 2,2′-bis-p-benzoquinone derivatives. [21,23,37] The charge voltage profiles of the first two GDC cycles are almost overlapped, showcasing prominent oxidation stability. It is noted that the initial charge capacity of 110.0 mAh g −1 approximates the theoretical value of 111.7 mAh g −1 calculated based on three-electron transfer, which suggests that the charging process of C 60 is a three-electron oxidation reaction. In the first cycle, the discharge voltage profile displays distinct ladder-like voltage plateaus at 2.33, 1.68, and 1.40 V, respectively, apart from the extra minor plateau at 1.77 V. While the charge counterpart www.advancedsciencenews.com www.advancedscience.com displays only three yet more elegantly flat plateaus at 2.50, 1.82, and 1.48 V that corresponds to three-stage oxidation of the lithiated C 60 . The three-stage voltage plateaus and their values are similar to those reported ones and the similar plateau capacity close to 37 mAh g −1 equivalent to one electron transfer for each plateau, particularly for the charging process, further supports the electron-by-electron three-electron-oxidation within the C 60 fullerene during charging. [36] Corresponding redox peaks are shown in Figure 3c. However, the discharge voltage plateau corresponding to the reduction peak near 1.8 V is smaller in the second cycle, which implies that the initial discharge underwent an irreversible reduction reaction and this, combined with interfacial pseudocapacitance, accounts for the irreversible capacity in the initial cycle and the relatively higher initial discharge capacity.
The rate capability of the C 60 cathode was ascertained at various current rates at room temperature, as shown in Figure 3d,e. The average discharge capacities at 0.2, 0.5, 1, 2, and 5 C are 120.4, 103.6, 95.6, 88.6, and 76.7 mAh g −1 , respectively. The capacity retention at 5 C is 63.7% relative to 0.2 C and the rate retention capability is equivalent to or even higher than previously reported MFO materials. [21,23,24] A comparison in electrochemical performance for various MFO materials provided in Table S1 and Figure S8, Supporting Information, shows that the performance the C60 cathode is superior compared with other MFO cathodes without carbonyls. The relatively large interstitials in between the C 60 clusters and the global electron delocalization in the C 60 clusters synergistically favor charge transfer and intermolecular lithium ion diffusion and contribute to the superior rate capability. [35,[42][43][44] To examine the cycling stability of the C 60 cathode, GDC tests were performed at 0.2 C current rate for initial 2 cycles followed by 1 C current rate for another 50 cycles. As Figure 3f shows, the reversible capacity that the C 60 cathode delivered in EL-3 electrolyte maintained at 91.9 mAh g −1 with a capacity retention rate of 83.9% after 50 cycles, along with an average discharge capacity of 99.1 mAh g −1 . Even after 100 cycles, a capacity above 70 mAh g −1 was retained, as shown in Figure S9, Supporting Information. In contrast, the discharge capacity for EL-2 faded quickly in the initial 20 cycles and then remained at low level ≈66 mAh g −1 with a final capacity decay by 33.8%. The case for EL-1 has a rather low capacity of only 7.2 mAh g −1 retained and 7.4% retention rate after 50 cycles. This manifests that the cycling stability of the C 60 cathode is also closely related to the electrolyte used, and the EL-3 electrolyte can better support the relatively stable GDC cycling of the C 60 cathode than the other two. The capacity fading for EL-3 during cycling is related to the partial dissolution of lithiated active materials similar to other organic MFO materials. [12] And the dissolving extent in DME for active materials in electrodes at varied states of charge during chargedischarge process was compared through UV-Vis spectroscopy, as shown in Figures S11 and S12, Supporting Information.
The electrode kinetics of C 60 cathode were studied by galvanostatic intermittent titration test (GITT), cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) as presented in Figure 4. The apparent diffusion coefficient of lithium ion, D Li + , in the C 60 cathode was measured by GITT at 0.2 C at the third cycle, as shown in Figure 4a The average D Li + for discharge process is 1.71 × 10 −13 cm 2 s −1 similar to the value of 1.83 × 10 −13 cm 2 s −1 for charge process, implicating high reversibility in terms of lithium diffusion kinetics for the C 60 cathode during GDC processes and comparable lithium ion diffusion kinetics relative to other MFO materials and typical cathode materials for LIBs were shown in Table S2, Supporting Information. The CV curves at various scan rates were shown in Figure 4c. Three pairs of redox peaks are observed, consistent with the second cycle in dQ/dV curves. The changes of current with scan rate follow the power law: The value of b can be obtained by plotting log(i) as the function of log(v) according to the derivation of above equation: where v is the scan rate, a and b are tunable coefficients, with b as the slope of plots in Figure 4d. The electrochemical reaction is dictated by capacitive process at b = 1, while it indicates the capacity is dominated by solid state diffusion when b = 0.5. [45,46] The average b values for the redox peak pairs of I, II, and III are 0.749, 0.493, and 0.470, respectively, which showcases that peak pair I exhibits a mixture between the capacitive and the diffusionlimited behavior while the other two are basically controlled by diffusion. Furthermore, the EIS curves for the C 60 cathode at different charged or discharged states in the fourth cycle were obtained and are shown in Figure 4e. In the inset is the equivalent circuit for EIS fitting, in which the parameter R l represents the resistance of electrolyte and the contacts of cell parts other than the active materials, R s the solid-electrolyte-interface(SEI) resistance, R ct the charge transfer resistance, and Z w the Warburg resistance, and CPE1 and CPE2 are the constant phase elements. [47][48][49] In a GDC cycle, R s , derived from the high-frequency semicircle, mostly remains steady at ≈250 Ohm at various discharge and charged states, as shown in Figure 4f. However, the evolution of R ct value, derived from the middle-frequency semicircle, behaves more like a slight U-type curve. It declines by 18% from 660 Ohm at the OCV state to ≈560 Ohm after discharged to 2.1 V below 1st discharge plateau, and then keeps almost stable before a bold climb to ≈651 Ohm when the cell was discharged to 1.2 V of deeply lithiated state. Over subsequent charge process, the R ct value gradually increases to ≈607 Ohm at fully charged state. This indicates that the SEI is less sensitive to the lithium intercalation compared with the charge transfer for C 60 cathode in this GDC cycle. It is also shown that the charge transfer can be reversibly altered by lithium intercalation. A comparison of charge transfer resistance with other MFO cathode materials in Table S3, Supporting Information, shows that the charge transfer resistance of C 60 cathode is relatively low, suggesting decent electrode kinetics of charge transfer. Moreover, the relatively lower R ct values at lower lithiated potentials imply that the relatively higher lithiation degree favors charge transfer kinetics. Given the near-theoretical reversible capacity and the redox behavior described above, the C 60 cathode can undergo reversible three-electron redox reactions with respect to the GDC process . a) Voltage profiles acquired from GITT measurement for the 3rd GDC cycle, b) apparent diffusion coefficients D of lithium ion calculated based on (a), here the 100% SoC is defined as the lithiated state at 1.2 V, c) CV curves of C 60 cathode at various scan rates, d) logarithm plots of peak current versus scan rate, e) Nyquist plots for C 60 cathode obtained by EIS tests at various discharged/charged states for the 4th GDC cycle, the OCV data point near 3.0 V is categorized to the discharge part. Inset is corresponding equivalent circuit via which fitting curves are obtained, f) Evolution of resistance at different discharged or charged states extracted from fitting curves of (e). except for the first discharge. The reactions can be deduced as follows: For redox pair I between 2.33 and 2.5 V, For redox pair II between 1.65 and 1.82 V, For redox pair III between 1.40 and 1.48 V, To gain insights into the structural evolution of the C 60 cathode during the GDC processes, in situ XRD experiment was performed at 0.35 C in half cell at room temperature. The results are shown in Figure 5. During the discharge-charge process, the C 60 cathode underwent phase transitions corresponding to three dis-charge voltage plateaus. For the initial discharge, as shown in Figure 5a, the (311) peak shifts positively from ≈20.70°to ≈20.85°, indicative of an interplanar contraction for the (311) crystal plane. Slight negative shift was also observed for (111) peak, as shown in the wide-range XRD pattern in Figure S4, Supporting Information. In the meanwhile, the intensity of (311) diffraction peak decreases first and then increases to its apex when the cell was discharged to the second voltage plateau, followed by another decrease, as observed in Figure 5b. Surprisingly, one new peak 19.55°emerge during the 1st discharge voltage plateau 2.3 V, which can be ascribed to the orthorhombic phase (denoted as O1, ICSD-75 612) belonging to Pnnm space group. [50] Later when the cell was discharged to the 2nd plateau 1.6 V, another new peak appears at 19.0°and gradually intensifies, which, together with the peak near 19.5°matches monoclinic C2/m phase (denoted as M1, ICSD-55 493). [51] In the 3rd discharge plateau near 1.4 V, these peaks become weak and another peak near 21.5°appears, suggestive of another phase presumably formed of monoclinic C2/m phase (denoted as M2, ICSD-94 237). [36,52]  Most intriguingly, in the initial charge process, the (311) peak begin to intensify when the cell was charged to the second voltage plateau near 1.8 V while its peak position remains. When the cell was fully recharged to 3.0 V, another new peak appears at ≈20.55°(marked as blue arrow in Figure 5a) which is attributed to another orthorhombic Pnnm phase (denoted as O2, ICSD-94 500). [53] Noteworthily, the peak at ≈19°intensifies and subsides alternatingly during GDC, concurring with the peak near 20.8°, which further supports that the peak near 19.0°corresponds to monoclinic C2/m phase. Note that the peak originally from (311) plane of FCC cannot go back to its initial position at ≈20.7°in following GDC process. This irreversible peak shift could correlate with the irreversible short discharge voltage plateau near 1.77 V, which can be rationalized by partial polymerization between C 60 clusters via intermolecular coupling. [53,54] This peak shift also suggests that the intermolecular coupling interaction can induce the interplanar contraction which is also irreversible. The phase structures and their evolution were further verified through ex situ transmission electron microscopy (TEM) performed for samples discharged or charged to varied cut-off voltages ( Figures S5 and S10, Supporting Information). In situ Raman spectroscopy was employed to inspect the vibration evolution of the C 60 cathode during GDC process. As shown in Figure 6, the Raman spectra of the pristine C 60 electrode exhibits three peaks at 272.3, 495.6, and 1468.0 cm −1 corresponding to the intramolecular vibration modes of "squashing" Hg(1), "breathing" Ag(1), and "pentagonal-pinch" Ag(2), respectively. [55,56] The intensity of all these peaks increased during charge process of the lithium deintercalation yet decreased during discharge process of electron injection. The increased peak intensity could involve the recovered molecular symmetry with delithiation and vice versa. Moreover, the peak position also varies with the degree of lithium intercalation. For instance, the Ag(2) peak shifts toward higher frequency during charging and then shifts toward lower frequency during discharging (Figure 6b), which arises from reversible formation and decomposition of intramolecular covalent bonding induced by charge transfer. [57] The irreversible downshift gaps of ≈6 cm −1 for all these peaks in GDC process relative to their pristine positions, similar to the aforementioned irreversible XRD peak shift (Figure 5a), suggests a reduced symmetry of the molecules. [58] The peak shift of pentagonal-pinch Ag(2) was reported as a sensitive www.advancedsciencenews.com www.advancedscience.com Figure 7. a) ATR-IR spectra of C 60 cathode at various discharged/charged states acquired ex situ, b-d) magnified views of (a).
probe for the extent of C 60 polymerization. [56,58] The Ag(2) peaks during GDC locate between 1458.6 and 1460.2 cm −1 , as exhibited in the case of photo-or pressure-induced polymerized C 60 , could be attributed to the linear C 60 clusters. [54,56] Further, ex situ attenuated-total-reflection IR (ATR-IR) spectroscopy was measured to detect the vibration responses of C 60 to lithium (de)intercalation. As presented in Figure 7a, the pristine C 60 powder exhibits four major peaks located at 521.7, 572.8, 1180.2, and 1426.1 cm −1 , which were assigned to four fundamental and symmetry-allowed intramolecular vibration modes of T1u(1), T1u(2), T1u(3), and T1u(4), respectively. [59] For charged and discharged samples, new peaks emerged, implying lowered symmetry of the C 60 molecule. [54] As shown in Figure 7b, the T1u(1) and T1u(2) peaks are first depressed after discharge and then recovered after charging. In contrast, the evolutions of highfrequency vibrations are much more complicated due to the peak shift and emergence of new peaks. After discharge, the T1u(3) peak shifts from 1180 to 1188 cm −1 and becomes broadened, which implies an increased disorder among C 60 molecules, as seen in Figure 7c. Most noteworthily, new peaks appear at ≈1227 and 1129 cm −1 , with the latter associating with one splitting vibration mode of T1u(3). [60] When the cell charged back from 1.2 to 2.1 V, the T1u(3) band underwent red shift and split, exposing another new characteristic peak at 1192 cm −1 , related to intermolecular polymerization [60] With the cell recharged to 3.0 V, the splitting peaks subside yet the T1u(3) peak resumed its original position with more sharpened shape, indicate of recovered symmetry. The reversible peak shift of T1u(3) mode could arise from the reversible fluctuation in lattice constant of the lithiated C 60 . [61] As exhibited in Figure 7d, the peak shift of T1u(4) is not obvi-ous. Similarly, T1u(4) peak also broadens up to 1465 cm −1 and one splitting peak appears at ≈1339 cm −1 come into sight. [60,62] As the cell charged from 1.6 to 2.1 V and to 3.0 V, new peaks emerge sequentially at 1444, 1397, and 1460 cm −1 , consistent with those in situ IR data reported. [62,63] The reversible splitting of high-frequency T1u vibrations also manifests the structural reversibility. Although the self-polymerization between the C 60 clusters within C 60 cathode may lead to some irreversible capacity loss, it may also promote electron delocalization bridging the C 60 clusters, favoring charge transfer and hence the rate capability. [64] Based on the above analysis, it is deduced that the phase transitions of the C 60 cathode during GDC were dominated by the interactions among neighboring C 60 molecules as well as lithium intercalation. Combining in situ XRD analysis and ex situ TEM revelation with density-functional-theory (DFT) calculations (details are in Supporting Information), underlying mechanisms during charge and discharge were proposed, as illustrated in Figure 8. Different from previous DFT studies of C 60 based on single C 60 molecule in cathode applications, [65] plateau redox reactions and crystal phases of C 60 with/without lithium ions involved were considered in our study to derive the delithiation potentials. For the first discharge stage, lithium ions tend to occupy the octahedral interstitial sites in FCC lattice of the C 60 crystal for charge compensation as C 60 molecules are negatively charged along with interplanar contraction, leading to phase transition from FCC to orthorhombic Pnnm LiC 60 (O1 phase), accompanied by partial polymerization and volume contraction. As the lithium ions further migrate into O1 phase structure with C 60 accepting more electrons, lithium ions can be redistributed to occupy quasi-tetrahedral and quasi-octahedral sites, transforming the structure to monoclinic C2/m phase (M1 phase). As more lithium ions squeeze into the M1 phase structure, redistribution of lithium ions and volume expansion can occur to accommodate more lithium ions, reshaping the structure into another C2/m phase (M2 phase)). The charging process proceeds reversibly except that another orthorhombic Pnnm (O2 phase) rather than FCC phase was formed at the end of charging. A comparison between simulated plateaus of open circuit potentials based on proposed phase structures and experimental potential profile based on GITT test is shown in Figure 8b. For simulation, it was assumed that only the oxidation of the lithiated C 60 contributes to the charge capacity regardless of capacitance and partial polymerization. It is observed that the trend of simulated OCVs agrees qualitatively with that of the experimental OCVs, indicating that the proposed phase transition mechanism is energetically reasonable. The conformable positive potential deviation of ≈0.3 V in average can arise from disregarding the effect of solvation energy of Li + and TFSI − . [11,66] It is noted that the elegant flatness of the operating voltage plateaus (Figure 3b), especially for charge part, energetically betrays the fact that the phase structures of C 60 or the lithiated C 60 in the midst of each plateau are stable, with little effect from intercalating lithium ion, deducing from Nernst equation and Gibbs free energy difference between the products and the reactants for a given reaction. [11,66,67] The phase transitions abruptly occur at the end of each plateau and the characteristic of multiple plateaus also distinguishes the C 60 fullerene from most MFO multi-electron-redox cathode materials.

Conclusion
In summary, we used C 60 fullerene as organic cathode for rechargeable LIB operating at room temperature. Robust electrochemical redox reactivity, much higher reversible capacity and decent cycling stability were achieved in ether-based electrolyte relative to the carbonate-based one. The C 60 cathode exhibited superior electrochemical performance compared with other MFO cathodes without carbonyls, due presumably to intrinsic electron delocalization within C 60 and beneficial lithium penetration in between C 60 nanoclusters. Unusually, three pairs of voltage plateaus occurred sequentially at ≈2.4, 1.7, and 1.5 V in discharge-charge voltage profiles, correlating with three-electronredox chemistry demonstrated by the near-theoretical specific total and plateau capacities. The presence of phase transitions during discharge/charge process was revealed for the first time by in situ XRD. As evidenced by the irreversible shift of (311) peak from the in situ XRD and the evolution of the peak at 1460 cm −1 in in situ Raman spectra, partially irreversible polymerization may be responsible for the largely irreversible minor plateau near 1.8 V. The phase evolution and irreversible structural transition was also verified by ex situ TEM.
Based on the in situ XRD and ex situ TEM analyses, three reversible lithiation-induced phase transitions between M1, M2, O1, and O2 phase were proposed. This was also energetically corroborated by DFT calculations. It is noteworthy that fullerenes play an important role in modulating the open-circuit voltage of solar cells and organic molecules such as poly(3-hexylthiophene-2,5-diyl) and tetrakislawsone have been used as cathodes for photo-rechargeable Zn-ion and LIBs. [68][69][70][71] Therefore, this work will not only enrich the studies of multi-electron-redox organic electrode materials for rechargeable batteries, but also shed light on the research of fullerene battery chemistry, providing new understandings beyond conventional rechargeable batteries to inspire the research of novel batteries including the emerging solarrechargeable batteries.

Experimental Section
Electrode Fabrication: Commercial C 60 powder (MREDA TECHNOL-OGY, >99.50%) was used without further processing. The C 60 powder and acetylene black were ground together in a mortar, followed by mixing them with the suspension of polyvinylidene fluoride (PVdF) as binder in N-methyl-2-pyrrolidone. The mass ratio of C 60 , acetylene black, and PVdF was controlled at 60:20:20 ratio. Next, the slurry was cast uniformly onto conductive-carbon-coated aluminum foil as current collector and dried at 60°C for 10 h inside a vacuum oven. The dried coated aluminum foil was punched into electrode discs of 8 mm in diameter, where the mass loading of the electrode material is ≈0.83-1.33 mg cm −2 . Other details are presented in Supporting Information.
Electrochemical Measurements: GDC tests were carried out at room temperature on the battery tester (NEWARE). CV tests were carried out at various scan rates at room temperature using an electrochemical workstation (CHI 660E). EIS measurements were conducted by applying a perturbation voltage of 5 mV in the frequency range from 100 kHz to 0.01 Hz using the same electrochemical workstation. Other details are included in Supporting Information.
Materials Characterization: The morphology image of pristine C 60 was obtained by a field emission SEM (TESCAN MIRA3, accelerating voltage: 15 kV). Powder XRD data for pristine C 60 were collected on Bruker Advance D8 system with Cu K radiation ( = 1.5418 Å). TEM images were acquired using Cs-corrected Environmental TEM operated at 80 kV. Other characterization details are provided in Supporting Information.
Computational Method: All calculations were conducted by using the Vienna ab initio simulation package code, based on the DFT method. Details can be found in Supporting Information.

Supporting Information
Supporting Information is available from the Wiley Online Library or from the author.