Incarceration of Iodine in a Pyrene-Based Metal-Organic Framework

A pyrene-based metal-organic framework (MOF) SION-8 captured iodine (I-2) vapor with a capacity of 460 and 250 mg g(MOF)(-1) at room temperature and 75 degrees C, respectively. Single-crystal X-ray diffraction analysis and van-der-Waals-corrected density functional theory calculations confirmed the presence of I-2 molecules within the pores of SION-8 and their interaction with the pyrene-based ligands. The I-2-pyrene interactions in the I-2-loaded SION-8 led to a 10(4)-fold increase of its electrical conductivity compared to the bare SION-8. Upon adsorption, >= 95 % of I-2 molecules were incarcerated and could not be washed out, signifying the potential of SION-8 towards the permanent capture of radioactive I-2 at room temperature

Hydrogen storage and electrochemical properties of LaNi5-xCux hydride-forming alloys

LaNi5-type alloys are commercial materials for the negative electrode in Ni-MH rechargeable batteries. Partial substitution of La by mischmetal (Mm) and of Ni by elements like Co, Al, and Mn significantly improve the cycle stability and high-rate discharge capacity of the electrodes. The partial substitution of Ni by Cu was studied previously for several selected ternary alloys with a special focus on crystal structure change upon substitution and gas phase hydrogen absorption. We present in this paper the results of the study of the electrochemical activation, discharge kinetics, equilibrium charge/discharge, and cycle life of electrodes made from four different LaNi5-xCux (x = 0.1, 0.5, 0.9, 1) alloys in order to provide full insights into utilization of these alloys. (C) 2018 Elsevier B.V. All rights reserved

Description of the capacity degradation mechanism in LaNi5-based alloy electrodes

The mechanism of the capacity degradation of LaNi5-based alloy electrodes was investigated with a special focus on the influence of the alloy and surface composition, as well as the unique structure obtained by gas atomisation. The electrochemical properties, especially the cycle life curve (i.e. the capacity as a function of the cycle number of LaNi4.5Al0.5, LaNi2.5Co2.4Al0.1, (La + Mm) Ni3.5Co0.7Al0.35Mn0.4Zr0.05, and MmNi(4.3)Al(0.2)Mn(0.5) alloy electrodes), was analysed and modelled. The capacity degradation upon cycling is determined by the chemical state of the alloy elements and the solubility of their oxides. The cycle life curves for the alloy electrodes without Co exhibited a rapid activation (3-4 cycles to reach maximum capacity), as well as rapid degradation (130-180 cycles for 50% maximum discharge capacity). LaNi2.5Co2.4Al0.1 and (La + Mm) Ni3.5Co0.7Al0.35Mn0.4Zr0.05 alloy electrodes activated after 7-10 cycles and showed very stable discharge behaviour (more than 400 cycles). The Co-containing alloy electrodes primarily lose the cycle stability because of mechanical decrepitation, whereas the alloys without Co suffer from selective dissolution of the unstable elements in the potential window, which was shown by our model of alloy degradation and confirmed by means of SEM, WDX, and ICP-OES data. (C) 2014 Elsevier B.V. All rights reserved

MOESM1 of Characteristics and properties of nano-LiCoO2 synthesized by pre-organized single source precursors: Li-ion diffusivity, electrochemistry and biological assessment

Additional file1: Text 1. Synthesis of bimetallic compounds. Table S1. Crystal data. Text 2. Single crystal structure descriptions. Text 3. Argentometric titration. Table S2. Idealistic oxidation reactions of two types of compounds, precursors 1, 5 with 2:1 and precursors 8, 9 with 1:1 stoichiometric ratio between Li+ and Co2+. Table S3. Results of the argentometric titration of chloride and ICP-measurements for lithium. Table S4. ICP analysis for Li+ and Co3+ of LiCoO2 obtained from different precursors. Figure S6. XRD study of commercial LCO, and nano-LCO obtained from LiOtBu before annealing and after annealing at 600°C and 700°C. Figure S7. XRD of LiCoO2 from 9-LiOPh calcined at 450°C before washing. The red line corresponds to HT-LCO and the blue lines are Li2CO3. Table S5. The combustion temperature and the thermal measurement conditions of the compounds 1, 8-12. Table S6. TGA weight loss in percentage [%] with associated steps of compounds 1, 8-12. Equation S1-S5. Determination of the particle and crystallite sizes. Figure S8. Morphologies of LiCoO2 prepared with different precursors at 450°C. Figure S9. (a) Cyclic voltammograms of the 15 nm LCO prepared from the compound 12 at different sweep rates. (b) The maximum anodic and cathodic current peaks of LiCoO2 electrode versus the square root of sweep rate. Table S7. Li+ diffusion coefficients determined for HT-LCO obtained from different precursors. Figure S10. Nyquist plot for LiCoO2 electrodes from LiOtBu with fit: filled markers – experimental points, open markers – fit points with error bars a) and corresponding equivalent circuit model b) with fitting report c). Figure S11. Nyquist plot obtained for LiCoO2 electrodes from LiOPh with fit: filled markers – experimental points, open markers – fit points with error bars a) and corresponding equivalent circuit model b) with fitting report c)