目的 研究含氢20号钢在土壤模拟液中的腐蚀行为，探讨充氢时间对20号钢表面腐蚀形貌和腐蚀产物的影响，得到含氢20号钢在土壤模拟液中的腐蚀机理。方法 采用腐蚀失重法分析了不同充氢时间下20号钢的腐蚀速率，利用极化曲线和电化学阻抗谱，分析不同充氢时间下20号钢的电化学腐蚀行为，并通过SEM表征得到不同充氢时间下20号钢表面的腐蚀形貌和腐蚀产物，同时结合EDS和拉曼光谱分析得到20号钢表面腐蚀产物的组成。结果 随着充氢时间的增加，20号钢腐蚀速率逐渐增大。在充氢初期，20号钢的腐蚀速率显著增大，当充氢时间超过24 h，20号钢腐蚀速率趋于稳定，氢含量逐渐达到饱和，样品表面出现大量的黄褐色腐蚀产物和点蚀坑。结论 在充氢初期，氢主要吸附于金属表面夹杂物处，使样品表面Al2O3夹杂物处微裂纹增多。随着样品中氢含量的持续增大，大量的氢吸附溶解于20号钢的晶相和相界处，促进了点蚀的发生和发展。此外，氢促进20号钢表面局部腐蚀产物形貌和组成发生变化，出现了Fe2O3晶型的改变，促进了γ-FeOOH和β-FeOOH的生成。

The work aims to study the corrosion behavior of hydrogen-containing 20# steel in soil simulation solution, explore the effect of hydrogen charging time on the surface corrosion morphology and corrosion products of 20# steel, and obtain the corrosion mechanism of hydrogen-containing 20# steel in soil simulation solution. Corrosion weight loss was used to analyze the corrosion rate of 20# steel under different hydrogen charging time. The electrochemical corrosion behavior of 20# steel under different hydrogen charging time was analyzed. The corrosion morphology and products on the surface of 20# steel under different hydrogen charging time were characterized by SEM for comparative analysis. At the same time, the composition of the corrosion products of 20# steel was obtained by combining EDS and Raman analysis tests. In the simulated soil solution, the self-corrosion potential and corrosion rate of 20# steel gradually increased with the increase of hydrogen charging time. In the initial stage of hydrogen charging, the corrosion rate of 20# steel increased significantly, and the hydrogen mainly adsorbed on the surface inclusions of the metal, promoting the increase of microcracks at the Al2O3 inclusions on the sample surface. Due to the different elastic moduli of inclusions and metal matrix, a large number of dislocations were generated around the inclusion interface, helping to adsorb hydrogen around the precipitates. The hydrogen was adsorbed around the precipitates, promoting the dissolution of metals around the precipitates. As the hydrogen charging time continued to increase, the hydrogen content in the sample continued to increase. When the hydrogen charging time was 24 hours, the corrosion rate of 20# steel tended to stabilize, indicating that the hydrogen content in the 20# steel sample gradually reached saturation. At this time, the percentage increase in the corrosion rate of 20# steel was 47.69% and there were a large number of yellow brown corrosion products and corrosion pits on the surface of the sample. The relationship between hydrogen charge time and corrosion rate was established, the model demonstrated that upon complete saturation of hydrogen adsorption sites in the steel matrix, the 20# steel exhibited a maximum corrosion rate of 0.141 6 mm/a, representing an 81.77% enhancement in corrosion degradation compared to non-hydrogen charging. A large amount of hydrogen was adsorbed and dissolved in the metal crystal phase and phase boundaries, promoting the occurrence and development of pitting corrosion. In addition, hydrogen promoted changes in the morphology and composition of localized corrosion products of 20# steel. SEM observations revealed that the 20# steel under non-hydrogen charging exhibited corrosion products with polygonal platelet morphologies. As the hydrogen charging time increased, the size of the polygonal flakes gradually increased. At the same time, a large amount of layered corrosion products accumulated locally and the corrosion products were loose and porous. The hydrogen increases hydroxide ion concentration in corrosion products and the formation of γ-FeOOH and β-FeOOH. In contrast to the FeOOH polymorphs, Fe2O3 exhibits enhanced protective properties on metallic substrates. The porous architecture characteristic of γ-FeOOH and β-FeOOH accelerates interfacial electrochemical kinetics within the corrosion product layer, thereby promoting pit initiation and propagation through enhanced ion transport pathways.