and environmentally friendly. So far, various materials have been developed as anode materials for LIBs, based on three types of storage mechanisms (Figure 1): (1) insertion; (2) alloying; and (3) conversion. For instance, Sn-based electrodes, Si-based electrodes, Ge-based electrodes, metal nitride-based electrodes, and metal oxide-based electrodes follow either alloying or conversion mechanisms [5]. Carbonaceous materials (e.g., graphite) and Li\({}_{4}\)Ti\({}_{5}\)O\({}_{12}\) (LTO) are based on insertion mechanisms [6]. Among various anode materials, graphite remains one of the most widely used anode materials, because it has excellent mechanical thermal stability, good electrical conductivity, low working voltage, non-toxicity, abundant storage, and it can avoid the dendrites formed in the charging and discharging process [7; 8]. However, graphite has a low theoretical capacity of 372 mAh\(\cdot\)g\({}^{-1}\), which cannot meet the demand for high energy density batteries. In addition, due to the large distance between the graphite layers, the electrolysis solution may also be separated from lithium embedding, causing the layered structure to collapse, leading to structural destruction which in turn affects cycle life [9]. In these anode materials, Si has the highest theoretical specific capacity (4200 mAh\(\cdot\)g\({}^{-1}\)) which can reach more than ten times that of traditional graphite. This gives an Si anode enormous application potential [10; 11]. Since the lithiation and delithiation of silicon are alloying reactions (Figure 1), they involve significant volume expansion and shrinkage due to the alloy density changes, with a rate of change exceeding 300% and brings irreversible effects on the electrochemical properties, including the reduction of cycle life and the decrease of coulomb efficiency [12]. The resulting internal stress seriously affects the stability of the structure, not only in the rupture of the structure of the material itself, also reflected in the material macroscopic separation from the fluid collection, seriously influencing the cycle stability. Also, broken silicon in turn brings the internal silicon in contact with the electrolyte, continuous generation of new SEI (solid electrolyte interface), and this leads to a constant reduction of the active material. This is the main reason for the low efficiency of the first circle of the silicon anode materials [13]. To alleviate the significant volume expansion of Si anode materials during cycling, researchers have primarily proposed three solutions: (1) the nano-structuring of Si [14]; (2) composite integration with materials that have pressure-buffering properties [15]; and (3) designing physical barriers to provide space for the expansion of Si [16]. However, these methods generally lead to capacity degradation.  
Since the middle of 1990s, Si-based polymer-derived ceramics have been considered as anode materials of lithium ion batteries in some patent applications [17; 18]. In the last two decades, this research topic has attracted increasing attention because the Si-based ceramics (e.g., SiOC, SiCN) have been proven to exhibit excellent electrochemical properties superior than or unobtainable for other materials [19; 20; 21]. Compared to silicon, the silicon-based PDCs demonstrate enhanced structural stability, minimal volumetric expansion, straightforward fabrication processes, and high compatibility with large-scale manufacturing requirements [22; 23; 24]. Therefore, in this work, we pay more attention to polymer-derived ceramics.