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structure and the high density of phase/grain boundaries. Figure 10A schematically shows Nanomaterials 2021, 11, 810 the increased grain boundaries and magnesium ions transport channels on the atomic scale that is possible to obtain after the first cycle in a dual-phase bismuth–tin electrode. Two different alloys were tested, i.e., Bi6Sn4 and Bi4Sn6, synthesized by chemical dealloy- ing of rapidly solidified Mg90Bi6Sn4 (at %) and Mg90Bi4Sn6 (at %) precursor ribbons in a 2 14 of 29 Figure 10. (A) The increased grain boundaries on the atomic scale after the first cycle and the en- Figure 10. (A) The increased grain boundaries on the atomic scale after the first cycle and the wt % tartaric acid solution at ambient temperature. Scanning electron microscopy (SEM) images of the two alloys are shown in Figure 10B,C. Their theoretical specific capacities were 623 and 525 mAh g−1, respectively. hanced magnesium ions transport; SEM images of (B) NP-Bi6Sn4 and (C) NP-Bi4Sn6; (D) CV curves enhanced magnesium ions transport; SEM images of (B) NP-Bi6Sn4 and (C) NP-Bi4Sn6; (D) CV curves for NP-bismuth and alloy electrodes at a scan rate of 0.05 mV s−1 and for NP-tin at 0.01 mV s−1 for for NP-bismuth and alloy electrodes at a scan rate of 0.05 mV s−1 and for NP-tin at 0.01 mV s−1 the first cycle; (E) Discharge/charge profiles for NP-bismuth and alloy electrodes acquired at 50 forthe−1firstcycle;(E)Discharge/c−h1argeprofilesforNP-bismuthandalloyelectrodesacquiredat mA g and for NP-tin at 20 mA g . Adapted with permission from [170]. Copyright Elsevier B.V., 50 mA g−1 and for NP-tin at 20 mA g−1. Adapted with permission from [170]. Copyright Elsevier 2018. B.V., 2018. MIB performances with these alloys were studied in an all-phenyl-complex 0.4 M MIB performances with these alloys were studied in an all-phenyl-complex 0.4 M electrolyte. Cells were composed of a magnesium foil and the alloy as electrodes, and electrolyte. Cells were composed of a magnesium foil and the alloy as electrodes, and comparison with NP-bismuth and NP-tin electrodes was also carried out. Figure 10D shows the resulting CV traces, at the scan rate of 0.05 mV s−1 for NP-bismuth and alloy electrodes, and at 0.01 mV s−1 for NP-tin within the voltage range of 0–0.6 V vs. Mg2+/Mg. It is possible to observe a larger peak area for the NP-Bi4Sn6 electrode than that for the NP-Bi6Sn4 one, suggesting a higher specific capacity. For the two alloys, a two-step reversible magnesiation and de-magnesiation reaction occurred, associated to two couples of redox peaks. This was attributed to the biphasic nature of the alloys. The relatively small redox peaks of the NP-tin electrode were explained by its low reactivity and inferior kinetics. Galvanostatic discharge/charge profiles of the NP-bismuth and alloy electrodes (at a current density of 50 mA g−1) and of NP-tin sample (at 20 mA g−1) within the voltage range of 0–0.8 V vs. Mg2+/Mg (Figure 10E) showed that NP-Bi6Sn4 and NP-Bi4Sn6 electrodes managed to deliver high values of discharge specific capacities equal to 434 and 482 mAh g−1, respectively. These values were much higher than those of NP-bismuth and NP-tin, i.e., 330 mAh g−1 at 50 mA g−1 for NP-bismuth and only 31 mAh g−1 evenPDF Image | Overview on Anodes for Magnesium Batteries
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