Abstract:The synergistic effect of surface carbon coating and CNT compositing on mesoporous hard carbon was investigated. The sample showed excellent cyclic and rate performances, suggesting a highly efficient and easy scale-up approach to elevate hard carbons as anodes for SIBs.
“…The observed first broad reduction peak at around 0.217 V was associated to the electrolyte decomposition reaction and the formation of a solid electrolyte interface (SEI), which disappeared in the subsequent cycles, confirming an irreversible process. The similar irreversible cathodic peak is observed in the cyclic voltammograms of the HC anode. , A predominant reduction peak was observed at 0.014 V, corroborating the Na + ion intercalation of the micropore filling mechanism , in the derived mesoporous HC anode (Figure a). Subsequently, a predominant anodic peak was observed at 0.185 V, corresponding to the Na + ion deintercalation from the MHCSs.…”
Section: Resultssupporting
confidence: 76%
“…The similar irreversible cathodic peak is observed in the cyclic voltammograms of the HC anode. 61,62 A predominant reduction peak was observed at 0.014 V, corroborating the Na + ion intercalation of the micropore filling mechanism 28,48 in the derived mesoporous HC anode (Figure 4a). Subsequently, a predominant anodic peak was observed at 0.185 V, corresponding to the Na + ion deintercalation from the MHCSs.…”
Advanced wave-shape non-graphitizable carbon sheets are derived, comprising mesoporous weaved turbostratic micropore enabled stable Na + ion storage. The non-graphitizable amorphous characteristics are determined from the obtained two broad diffraction peaks at 22.7°and 43.8°. The observed D-band at 1325 cm −1 and G-band at 1586 cm −1 confirm the disordered graphitic structure, attributed to the measured specific surface area of 54 m 2 g −1 . Mesoporous weaved wave-shape carbon sheet architecture is confirmed by surface morphological studies, showing lattice fringes of disordered graphitic structures and dispersed ring patterns for the non-crystalline characteristics. The predominant stable redox peak at 0.014 V/0.185 V and the broader rectangular shape between 0.9 and 0.15 V depict the adsorption−micropore filling mechanism. The mesoporous hard carbon sheet delivers discharge−charge capacities of 450/311 mAh g −1 (1st cycle) and 263/267 mAh g −1 (250th cycle) at 25 mA g −1 , exhibiting a superior anode for sodium-ion batteries. Besides, in situ multimode calorimetry results disclose that the micropore filling Na + ion storage shows a higher released total heat energy of 721 J g −1 than the adsorption (471 J g −1 ). Ultimately, differential scanning calorimetry analysis of micropore filling Na + ion storage (discharged state at 0.01 V) has revealed a predominant exothermic peak at 156 °C with the highest released total heat energy of 2183 J g −1 compared to adsorption (553 J g −1 ) and deintercalation (85 J g −1 ), indicating that micropore filling status is more unsafe than the adsorption and deintercalation for SIBs.
“…The observed first broad reduction peak at around 0.217 V was associated to the electrolyte decomposition reaction and the formation of a solid electrolyte interface (SEI), which disappeared in the subsequent cycles, confirming an irreversible process. The similar irreversible cathodic peak is observed in the cyclic voltammograms of the HC anode. , A predominant reduction peak was observed at 0.014 V, corroborating the Na + ion intercalation of the micropore filling mechanism , in the derived mesoporous HC anode (Figure a). Subsequently, a predominant anodic peak was observed at 0.185 V, corresponding to the Na + ion deintercalation from the MHCSs.…”
Section: Resultssupporting
confidence: 76%
“…The similar irreversible cathodic peak is observed in the cyclic voltammograms of the HC anode. 61,62 A predominant reduction peak was observed at 0.014 V, corroborating the Na + ion intercalation of the micropore filling mechanism 28,48 in the derived mesoporous HC anode (Figure 4a). Subsequently, a predominant anodic peak was observed at 0.185 V, corresponding to the Na + ion deintercalation from the MHCSs.…”
Advanced wave-shape non-graphitizable carbon sheets are derived, comprising mesoporous weaved turbostratic micropore enabled stable Na + ion storage. The non-graphitizable amorphous characteristics are determined from the obtained two broad diffraction peaks at 22.7°and 43.8°. The observed D-band at 1325 cm −1 and G-band at 1586 cm −1 confirm the disordered graphitic structure, attributed to the measured specific surface area of 54 m 2 g −1 . Mesoporous weaved wave-shape carbon sheet architecture is confirmed by surface morphological studies, showing lattice fringes of disordered graphitic structures and dispersed ring patterns for the non-crystalline characteristics. The predominant stable redox peak at 0.014 V/0.185 V and the broader rectangular shape between 0.9 and 0.15 V depict the adsorption−micropore filling mechanism. The mesoporous hard carbon sheet delivers discharge−charge capacities of 450/311 mAh g −1 (1st cycle) and 263/267 mAh g −1 (250th cycle) at 25 mA g −1 , exhibiting a superior anode for sodium-ion batteries. Besides, in situ multimode calorimetry results disclose that the micropore filling Na + ion storage shows a higher released total heat energy of 721 J g −1 than the adsorption (471 J g −1 ). Ultimately, differential scanning calorimetry analysis of micropore filling Na + ion storage (discharged state at 0.01 V) has revealed a predominant exothermic peak at 156 °C with the highest released total heat energy of 2183 J g −1 compared to adsorption (553 J g −1 ) and deintercalation (85 J g −1 ), indicating that micropore filling status is more unsafe than the adsorption and deintercalation for SIBs.
“…As mentioned before, hard carbon is adopted to provide high reversible specific capacity and the interior CNTs make contributions to high conductivity. [9] As discussed above, CNTs@C-180 are chosen to be annealed for further characterization and electrochemical tests. It is also worth noticing that the reference HCSs are distributed in a uniform size of ~200 nm (Figure S3).…”
Section: Resultsmentioning
confidence: 99%
“…Speaking of batteries, numerous advanced and latemodel techniques are necessary to be developed to meliorate energy storage to keep abreast with the development of the new era. [8][9][10] Lithium-ion batteries (LIBs) have dominated the power sources of portable electronic devices and electric vehicles for many years. [9,11] LIBs advantage over other counterparts on account of their high energy density, long cycle life, and low maintenance cost.…”
Section: Introductionmentioning
confidence: 99%
“…[8][9][10] Lithium-ion batteries (LIBs) have dominated the power sources of portable electronic devices and electric vehicles for many years. [9,11] LIBs advantage over other counterparts on account of their high energy density, long cycle life, and low maintenance cost. [12][13][14][15] While merely improving LIBs technology is unable to solve the deficiency and maldistribution of lithium resources, which impedes their large-scale application.…”
Although being advantageous, the sodium‐ion storage capability of hard carbon would be better if its electrical conductivity could be improved. Herein, 3D hard carbon‐coated carbon nanotubes (CNTs@C) with interconnected conductive networks are fabricated by inducing hard carbon uniformly growth on CNTs. Compared with the isolated hard carbon spheres, the interconnected wire shape of CNTs@C reduces the ion transfer distance and increases the conductivity of hard carbon. By optimizing the thickness of the hard carbon layer and annealing temperature, the optimized CNTs@C displays a reversible specific capacity of 275.9 mAh g−1 at 0.1 A g−1 as anode material for SIBs. Furthermore, the material shows remarkable rate capability (102.8 mAh g−1 at 5 A g−1) and long‐life cycling performance (∼100% capacity retention after 1000 cycles at 5 A g−1). The results of this study provide an effective route for designing novel carbon‐based composite materials as anodes for SIBs.
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