Although the lithium-metal anode has the advantages of both high gravimetric and volumetric capacities (3862 Ah kg −1 and 2085 Ah L −1 ) [13] and is already successfully used in primary batteries, it is still plagued by a series of issues that limit its successful operation in rechargeable applications, when organic solvent based electrolytes are used. [14] One of them is the nature of the lithium-metal dissolution and redeposition in the discharge and charge process together with the composition of the solid electrolyte interphase (SEI) [15,16] that is formed immediately after electrolyte addition and continues to form, grow and alter during cycling, [17] which limits the rechargeability in these battery systems and decreases their safety. [15,18,19] The SEI, though not being a homo geneous single phase, varies in composition and thickness and these differences lead to inhomogeneous and thus locally different current densities during the discharge and charge process, which can ultimately cause the formation of high surface area lithium (HSAL) during lithium deposition (charging) and hole/pit formation during dissolution (discharging). [20][21][22] In the worst case, the HSAL morphology takes the form of dendrites, i.e., small needle like lithium deposits that can grow through the separator from the anode towards the cathode. This process can lead to an internal short circuit of the cell resulting in local overheating and possibly cause a cell fire due to an increased reactivity with the electrolyte and the low melting point of lithium (180.54 °C). [23] Practical approaches to improve the rechargeable lithiummetal anode from the electrode material's point of view concentrate on either using coated lithium powder [24,25] or foil [26] and lithium with surface micropatterning. [27,28] The main underlying principle is increasing the specific surface area thus decreasing the effective current density and the resulting overpotential. However, the behavior of the lithium-metal electrode is quite complex and electrolyte-dependent [22,[29][30][31] and there is a need to identify the optimal conditions under which lithium-metal electrodes can cycle with both an increased reversibility and low overpotentials. [32] As-received lithium-metal foil contains several contaminants, [33] particularly on the surface. [34] In addition, even a new lithium foil that is considered to be smooth shows a non-negligible surface roughness that Lithium metal as an electrode material possesses a native surface film, which leads to a rough surface and this has a negative impact on the cycling behavior. A simple, fast, and reproducible technique is shown, which makes it possible to flatten and thin the native surface film of the lithium-metal anode. Atomic force microscopy and scanning electron microscopy images are presented to verify the success of the method and X-ray photoelectron spectroscopy measurements reveal that the chemical composition of the lithium surface is also changed. Furthermore, galvanostatic measurements indicate superior c...

Lithium–sulfur batteries are still characterized by the low intrinsic electronic conductivity of sulfur in both its charged state (S8) as well as discharged state (Li2S). Here, using ball milling, a well‐dispersed active material within the carbon network is achieved using carbon black Super C65 and synthetic graphite KS6 as conductive agents. Calendering these electrodes increases the electronic percolation path resulting in enhanced electrochemical performances and reaction kinetics. Using high‐speed and high‐impact preparation methods improves the quality and performances of the S8/C composite electrodes when compared with electrodes prepared using a simple mixing method (magnetic stirring). The scanning electron microscopy images indicate that KS6 is able to incase S8 particles, resulting in a homogeneous distribution of the active material that in turn enhances the accessibility of the active material by the electrolyte and electrons. Compared with the S8/Super C65 composite electrode, a discharge capacity of 703 mAh g−1 is delivered by the S8/KS6 composite electrode during the first cycle. After 30 cycles, the S8/KS6 composite electrode delivers 477 mAh g−1 compared to only 411 mAh g−1 for the S8/Super C65 composite electrode due to a continuous capacity fading.