Its band structure is similar to that of silicon or germanium but with the conduction and valence bands nearly touching at the Γ point. This unique property arises from strong spin-orbit coupling and can ensue a transition to a topological insulator under certain conditions. Stanene, a 2-D monolayer of tin (ideal case) with a honeycomb lattice, exhibits remarkable properties. The band structure of stanene depends on the degree of strain and the presence of substrates or functionalization. Intrinsically, stanene is predicted to be a topological insulator with a bandgap induced by spin-orbit coupling. In a pristine state, stanene exhibits a Dirac-like band structure near the Fermi level, resembling graphene. From the first principle study, the electrons are reported to be confined along the edges of stanene quantum dots which results in layer-dependent morphological, optical, and electronic properties. However, Tin nanoparticles of sizes below 11 nm can only be stable as γ-Sn or β-Sn at any temperature as the large surface energy contributions stabilize these phases. For example, Tin nanoparticles have gained increasing attention in Libased batteries as an anode material as Sn has a much higher capacity and confining to its nano dimension can also help mitigating the volume expansion than currently cripples the successful deployment of graphite-based anodes. However, 3-D materials like traditional tin and tin-based anode materials suffer from the limitations like tedious synthetic procedures, high costs and low yields. Stanene, a two-dimensional allotrope of tin, exhibits remarkable properties making it an ideal candidate for exploring quantum confinement effects. As a finite arrangement of tin atoms, stanene quantum dots (SnQDs), not only are relatively unexplored, but also offer a platform for studying and harnessing quantum phenomena in confined geometries exhibiting unique electronic and optical properties, and providing opportunities for tailoring their behaviour through precise control over size, shape, and composition. SnQDs have been synthesized by Zhang et al. by in-situ electrochemical self-assembly. Although this method for producing SnQDs is interesting, this ultrasonic-assisted self-assembly method combined with a fluid-flow control system is onerous for scalability and hence there is a need for a simpler form of synthesis of SnQDs using elemental tin as the starting material. Electrochemical methods are performed at room temperature, which makes the technique notable, and potentiostatic control aids in the variation of different sizes of QDs. Bulk tin (β-Sn) as a pellet prepared from tin powder (α-Sn) is inexpensive as a suitable material for this exfoliation in 0.5 M LiClO4 in Acetonitrile as the electrolyte. The choice of electrolyte is also supported by the simulation and experimental data where LiClO4 is more dissociated in acetonitrile. For example, Acetonitrile-based electrolytes have a higher conductivity (>30 mS/cm) and lower viscosity values (~ 0.346 cP) that are suitable for this type of synthesis. Here, we investigate the size-dependent electrochemical transformation of the bulk tin to SnQDs at room temperature using 0.5 M LiClO4 in Acetonitrile. The UV and PL results indicate the sizedependent optical properties while the morphological structure of SnQDs is revealed from transmission electron microscopy (TEM) based on their size distribution (band-gap engineering). This is the first report on the synthesis of size-dependent SnQDs and their remarkable applications for energy storage. Although, -7 V is beyond the thermodynamic stability window of this system (-2.8 to +2.5 V), the electrolyte decomposition aids in better yield than its previous potentials. On this basis, the potential is selected and acetonitrile decomposition forms various products after crossing its potential threshold. For example, brief electrolysis at -3.3 V primarily yielded 3aminocrotonitrile (diacetonitrile) as the main product, while prolonged electrolysis produced 2,4,6-trimethyl-1,3,5-triazine, a trimer of acetonitrile. In the presence of water, electrolysis at -2.2 V predominantly forms acetamide. A cyclic voltammogram is shown in S4 to understand the preliminary process of this exfoliation. The initial step involves intercalating the ions and further exfoliation of the bulk tin under an inert atmosphere. After comlete exfoliation, the product is quickly transferred to the deaerated ethanol solution, where the dissolution and precipitation mechanism with rapid effervescence of CO2/CO is seen as indicated in reaction (3). The dissolved products from bulk tin leads to the formation of carbon-coated stanene quantum dots, as confirmed by TEM. and XPS although the exact mechanism is unclear. There is also a phase change in the transformation to quantum dots i.e., for particles less than 10 nm, γ-Sn is more stable at room temperature. The significant surface energy contributions for smaller particle sizes stabilise the γ phase. The γ phase has a hexagonal zero-dimensional, graphite-like planar structure with πconjugated systems fragmented at different times of 6, 12, and 16 h, respectively, resulting in SnQDs forming an interlayer distance of 0.326 nm. The carbon coating on the SnQDs imparts stability following a tentative mechanism given below. which is smaller on average as compared to a size 8.5 nm reported by Zhang et al. Both the examples display sizes close to the average sizes of the SnQDs synthesized for 12 and 16 h, respectively. These micrographs emphasize the tunable nature of SnQD size and shell thickness through controlled synthesis duration, which is crucial for tailoring their optical and electronic properties for various applications. (101) crystal planes respectively. This is analogous to the structural packing of SnO2/Sn confirming the presence of the QDs having defects when the exfoliated bulk Sn is dropped in ethanol. Additionally, for the QDs electrosynthesized at 6 h, the (110) plane is missing revealing the fact that lesser defects were introduced during the synthesis. Moreover, the (101) plane at are assigned to the Sn-O and O-Sn-O stretching and bending modes of SnO2, respectively. There is a clear lack of peaks due to the C=C stretching frequencies which were prominent in the FT-IR spectrum shown in Figure . The spectrum also shows the vibrational modes of O-H-O at 1398 cm -1 and O-H at 3429 and 1642 cm -1 respectively. Therefore, the ethanol washing step is a pre-requisite for the carbon coating on the surface of the SnQDs, the lack of which leads to the undesirable oxidation of the SnQDs resulting in SnO2 QDs.