Cl, Br, or I) where a monovalent molecular cation and divalent metal cation are occupied in the A-site and the B-site, respectively to active layers in various ways. [3] Thanks to their defect tolerance properties, many researchers have tried to control charge transport behaviors by minimizing defects that possibly exist in grain boundaries (GBs), interfaces, and structural imperfections. [4][5][6][7][8] In early research, single-crystal methyl-ammonium lead iodide (MAPbI 3 ) TFTs were reported whose maximum hole mobility (μ h ) was 4.7 cm 2 V −1 s −1 with bottom-gate bottom-contact (BGBC) configuration by Yu et al. [7] Recently, Zhu et al. reported 2D phenethylammonium tin iodide ((PEA) 2 SnI 4 ) TFTs with the methods of enlarging grain sizes by mixing the Lewis-based solvents and passivating iodide vacancies by oxygen treatment. [8] Comprehensively, these trials were based on optimizing morphologies of the films to overcome the Schottky barrier which is detrimental to the injection in the channel layers during the switching operation. Despite their feasible controllability, they still have unresolved problems in adjusting TFTs due to weak charge conduction, environmental instabilities, and gate-screening effect from ion migration. [9][10][11] Here, the defect-controlled inorganic halide perovskites (IHPs) were investigated. IHPs consisting of the extensive inorganic framework are considered to be alternative semiconducting materials, allowing TFTs to be operated for a longterm period and better conduction. [12,13] Among them, we chose cesium lead iodide (CsPbI 3 ) that has high intrinsic carrier mobility and diffusion length. [14] Even at the experimental value of the carrier mobility of the cubic (α)-CsPbI 3 film through a terahertz spectroscopy method, a charge carrier mobility of CsPbI 3 is above 30 cm 2 V −1 s −1 . [15] This value is higher than that of MAPbI 3 , MAPbI 3-x Cl x , FASnI 3 , FAPbBr 3 , and PEASnI 4, considering that the carrier mobility measurement method is the same. [16] Furthermore, extrinsic point defects can be formed by adding various additives, which can further improve the carrier mobility of the conventional α-CsPbI 3 . This electrically promising potential of α-CsPbI 3 is the main reason why we choose the active layer in TFT.However, high hole-doped HPs can be disadvantageous to TFT devices due to the difficulty to inhibit an overabundance of the hole carriers even in the off-state operation. [17] This can So far, it has been difficult to fabricate thin-film field-effect transistors (TFTs) based on inorganic halide perovskites (IHPs) due to their phase-instability and uncontrollable trap density. Here, the bottom-gate bottom-contact structured p-type TFTs are presented using the optimized IHP in the active layer. The stable cubic-CsPbI 3 phase is successfully synthesized by doping bismuth iodide and reduced defect densities by adding potassium bromide. The IHP TFTs based on the tailored cubic-CsPbI 3 show high hole mobility of ≈10 cm 2 V −1 s −1 , an on-off current ratio of 10 3 , a...