We anticipate our workflow would accelerate inorganic compounds phase transition studies, for example, the polymorphic transitions in BaTiO 3 , SrTiO 3 , CsPbI 3 and ZrS 2 by eliminating or reducing the need for ab initio molecular dynamics. Our implemented renormalization scheme relies solely on 0K force calculations to generate temperature-dependent displaced configurations. Additionally, the workflow provides valuable CTE insights for thin film, and may be used in the future to facilitate the selection of substrate/film combinations that minimize CTE mismatch. It might also be applied to screen compounds with negative CTE values, such as MZrF 6 (M=Ca,Mg,Sr) , ZrW 2 O 8 , silicon clathrate frameworks , LnFe(CN) 6 (Ln = Y, La) . For LTC calculations, our workflow boosts both accuracy and efficiency compared with previous models or methods. In the future, our plan is to extend our investigated systems to more complex materials such as ZrCuSiAs and CsAg 7 S 4 . In summary, we have developed a workflow that can efficiently extract high-order anharmonic IFCs and compute thermal properties within an automated pipeline with the input of merely the crystal structure and bulk modulus (for which other atomate routines exist ). Parameters are evaluated to optimize throughput and accuracy. The benchmarked parameters, as shown in Supplementary Tables S5 and S6, accurately capture third-order anharmonic properties across various materials. For the comparison between experimental and calculated CTE, R 2 values of 0.84, 0.89, and 0.91 were achieved for metals, semiconductors, and insulators, respectively, demonstrating high accuracy. Similarly, for LTC, R 2 values of 0.97 for metals and semiconductors, and 0.98 for insulators, highlight strong predictive capability. The computational costs primarily depend on crystal symmetry and primitive cell size, which affects the number of configurations needed for force constant fitting, rather than the material type. For dynamically unstable materials, in which the harmonic approximation is not capable of computing thermal properties, we adopt a renormalization procedure to incorporate the temperature effect and stabilize the high-temperature phase. The phase transition temperatures after considering temperature-dependent free energy corrections achieve less than 10% error. Notably, our workflow attains the goal of 2-3 orders of magnitude speedup compared with the conventional finite-displacement method for 3rd-order IFC calculations. The emergence of this workflow makes high-throughput calculations accessible for general lattice dynamic properties. We will continue to improve our protocols based on the practice of large-scale computation for various materials and new emerging tools, and hope that this method facilitates the practical application of lattice dynamics workflows in both theoretical and applied studies of materials properties.