Fe(3)O(4)-graphene composites with three-dimensional laminated structures have been synthesised by a simple in situ hydrothermal method. From field-emission and transmission electron microscopy results, the Fe(3)O(4) nanoparticles, around 3-15 nm in size, are highly encapsulated in a graphene nanosheet matrix. The reversible Li-cycling properties of Fe(3)O(4)-graphene have been evaluated by galvanostatic discharge-charge cycling, cyclic voltammetry and impedance spectroscopy. Results show that the Fe(3)O(4)-graphene nanocomposite with a graphene content of 38.0 wt % exhibits a stable capacity of about 650 mAh g(-1) with no noticeable fading for up to 100 cycles in the voltage range of 0.0-3.0 V. The superior performance of Fe(3)O(4)-graphene is clearly established by comparison of the results with those from bare Fe(3)O(4). The graphene nanosheets in the composite materials could act not only as lithium storage active materials, but also as an electronically conductive matrix to improve the electrochemical performance of Fe(3)O(4).
photocopying process took nearly a century from 1843 until the early 1940s, while the detailed crystal structure of PB was first confirmed as cubic by Ludi and co-workers in 1977, which is now widely accepted. [6] Remarkably, the past four decades have witnessed the exploration of PB in more and more new and totally different, but very promising application areas, reaching from rechargeable batteries [7] to catalysis [8] and biosensors, [9] from optically switchable films in electrochromic devices (smart windows) [10] to a helpful nanomaterial for cancer therapy. [11] Due to their excellent redox activity, low cost, and highly reversible phase transitions during the insertion/extraction process of certain cations, PB and PBAs have also been widely investigated as promising active materials for energy storage devices, especially for commercial sodium-ion batteries (SIBs) beyond other batteries system (potassium-ion batteries, [12,13] lithium-ion batteries (LIBs), [14] lithium-sulfur batteries (LI-S), [15] lithium-air batteries, [16] zinc-air batteries, [17] solid-state batteries, [18] etc.) in large-scale stationary energy storage systems in the near future. [19,20] The chemical formulas of PBAs could be represented asHere, A represents a single alkali metal or alkaline earth metal, or a mixture of these metals, while M 1 and M 2 typically are transition metals bonded by CN − bonds to form a 3D open structure with the capability to host element(s) A inside the crystal structure. □ represents the vacancy that is caused by the loss of an M 2 (CN) 6 group and the occupation by coordination water and interstitial water, the species and ionic radii of which are shown in Figure 2a. [21] With the different species and various ratios of A/M 1 /M 2 , the number of family members could reach more than 100, sharing different crystal phases, including monoclinic, [22,23] rhombohedral, [24,25] cubic, [26,27] tetragonal, [28] hexagonal, [29] etc. According to the amount of redox-active sites for battery application, PB and PBAs could be divided into dual-electron transfer type (DE-PBAs: M 1 and M 2 = Mn, Fe, Co) and single-electron transfer type (SE-PBAs: M 1 = Zn, Ni and M 2 = Fe, Co, Mn) with theoretical specific capacity of 170 and 85 mAh g −1 , respectively. [21] Taking the high average voltage and capacity of the DE-PBAs into consideration, they are promising and competitive, even to the level of LiFePO 4 (a well-known cathode material for the LIBs), for high energy density devices (≈450 Wh kg −1 on the material level). On the other hand, the negligible structural distortion and high conductivity of SE-PBAs make them desirable choices for fast-charging and long-life devices. [20,30] Prussian blue analogues (PBAs) have attracted wide attention for their application in the energy storage and conversion field due to their low cost, facile synthesis, and appreciable electrochemical performance. At the present stage, most research on PBAs is focused on their material-level optimization, whereas their properties in practical b...
Dou, S. (2015). Facile method to synthesize Na-enriched Na 1+x FeFe(CN) 6 frameworks as cathode with superior electrochemical performance for sodium-ion batteries. Chemistry of Materials, 27 (6), 1997Materials, 27 (6), -2003 Facile method to synthesize Na-enriched Na1+xFeFe(CN)6 frameworks as cathode with superior electrochemical performance for sodium-ion batteries AbstractDifferent Na-enriched Na 1+x FeFe(CN) 6 samples can be synthesized by a facile one-step method, utilizing Na 4 Fe(CN) 6 as the precursor in a different concentration of NaCl solution. As-prepared samples were characterized by a combination of synchrotron X-ray powder diffraction (S-XRD), Mössbauer spectroscopy, Raman spectroscopy, magnetic measurements, thermogravimetric analysis, X-ray photoelectron spectroscopy, and inductively coupled plasma analysis. The electrochemical results show that the Na 1.56 Fe[Fe(CN) 6 ]·3.1H 2 O (PB-5) sample shows a high specific capacity of more than 100 mAh g -1 and excellent capacity retention of 97% over 400 cycles. The details structural evolution during Na-ion insertion/ extraction processes were also investigated via in situ synchrotron XRD. Phase transition can be observed during the initial charge and discharge process. The simple synthesis method, superior cycling stability, and cost-effectiveness make the Na-enriched Na 1+x Fe[Fe(CN) 6 ] a promising cathode for sodium-ion batteries.Keywords method, batteries, facile, cathode, sodium, electrochemical, superior, frameworks, 6, cn, xfefe, na1, enriched, na, synthesize, ion, performance Disciplines Engineering | Physical Sciences and Mathematics Publication DetailsLi, W., Chou, S., Wang, J., Kang, Y., Wang, J., Liu, Y., Gu, Q., Liu, H. & Dou, S. (2015). Facile method to synthesize Na-enriched Na 1+x FeFe(CN) 6 frameworks as cathode with superior electrochemical performance for sodium-ion batteries.
Exploitation of clean renewable energy (solar, wind, and water) has inspired plentiful scientific researches on the development of large-scale energy storage systems (ESS), which possess cost-efficient and environmental-benign. Recently, in spite of the fact that more research achievement have been obtained in sodium-ion batteries and lithium ion batteries with organic electrolyte, some issues arising from organic electrolyte (detrimental effect on the environment, moisturesensitive, potential safety hazards induced by low flash point) have obstructed their practical application in ESS. Aqueous batteries are considered as an attractive candidate for ESS, due to its safety and a low environmental impact. Especially, aqueous zinc-ion batteries (AZIBs) stand out from the various aqueous batteries and have attracted more attention from researchers, owing to unique merits of zinc metal anode, including low redox potential (−0.76 V vs standard hydrogen electrode), chemical stability in water, and the abundant resources of zinc. [1-3] The choice of cathode candidates is crucial for AZIBs, and they can be classified into two types, conversion-type (NiO, Co 3 O 4 , etc.) [4] and intercalation-type (V 2 O 5 , MnO 2 , Prussian blue analogues, etc.), [5,6] based on their Zn-ion storage mechanism. The intercalation-type cathode is promising due to the utilization of neutral or slightly acidic electrolyte (ZnSO 4), in comparison with the conversion-type cathodes which utilize alkaline electrolyte, alleviating the dendritic zinc formation and reducing the environmental impact. V 2 O 5 , which has a layered structure, is considered as an ideal intercalation cathode candidate for Zn 2+ storage due to large capacity. However, V 2 O 5 application is hindered by its low conductivity, strong interaction with Zn 2+ and cathode dissolution, giving rise to the sluggish kinetics and capacity degradation. To solve these issues, the cathode host should have an appropriate crystal structure with large diffusion channels, weak electrostatic interaction with Zn 2+ , and high rate capability for Zn-ion storage. Yan et al. reported that electrostatic interactions with the V 2 O 5 framework can be weakened by Zn 2+ solvation in structural H 2 O in V 2 O 5 •nH 2 O. [7] Alkali metal ions (e.g., Li + , Aqueous zinc-ion batteries (ZIBs) have triggered a great deal of scientific research and become a promising alternative for large-scale energy storage applications, owing to the unique merits of high volumetric energy density, abundance of zinc resources, eco-friendliness, and safety. The pace of progress of ZIB development, however, is hindered by their poor reversibility and sluggish kinetics, derived from the dissolution of active materials in aqueous electrolytes and the strong electrostatic interactions between Zn 2+ and the cathode lattice. Herein, a vanadium oxide (V 2 O 5-x)/ polyaniline (PANI-V) superlattice structure is demonstrated as a model of superlattice structural engineering to overcome these weaknesses. In this superlattice, the PAN...
Sodium-ion batteries (SIBs) have been attracting intensive attention at present as the most promising alternative to lithium-ion batteries in large-scale electric storage applications, due to the low-cost and natural abundance of sodium. Elemental phosphorus (P) is very promising anode material for SIBs, with the highest theoretical capacity of 2596 mAh g −1 . Recently, there have been many efforts devoted to phosphorus anode materials for SIBs. As pure red phosphorus can not react with Na reversibly, many attempts to prepare composite materials containing phosphorus have been reported. Here, we report the facile preparation of a red phosphorus/N-doped carbon nanofiber composite (P/NCF) that can deliver a reversible capacity of 731 mAh g -1 in sodium-ion batteries (SIBs), with capacity retention of 57.3 % over 55 cycles. Our results suggest that it would be a promising anode candidate for SIBs with a high capacity and low cost.
An exfoliated MoS2-C composite (E-MoS2-C) was prepared via simple chemical exfoliation and a hydrothermal method. The obtained E-MoS2-C was tested as an anode material for sodium ion batteries. High capacity (~400 mA h g(-1)) at 0.25 C (100 mA g(-1)) was maintained over prolonged cycling life (100 cycles). Outstanding rate capability was also achieved with a capacity of 290 mA h g(-1) at 5 C.
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