## 1 Introduction  
Engineering components used in critical applications such as offshore platforms, pressure vessels, and aircraft landing gears are frequently exposed to cyclic loading, which can lead to catastrophic failure due to the gradual accumulation of plastic strain over repeated loading cycles. Failure in such systems is primarily caused by the irreversible inelastic progressive deformation that develops under asymmetric stress loading. This time-dependent buildup of plastic deformation under asymmetrical stress-controlled conditions is referred to as the ratcheting phenomenon. The ratcheting response of a material is strongly affected by several factors, including its microstructural characteristics, applied stress levels and rates, operating temperature, loading sequence, and step patterns [1]. Elevated temperature service conditions tend to intensify the ratcheting behavior of materials, except in certain intermediate temperature ranges, where the dynamic strain aging (DSA) phenomenon occurs and alters the response of the material temporarily [1,2]. The dynamic strain aging (DSA) phenomenon happens in some steels, including SA333 and SA508, in which the mechanical response of the material is influenced by both temperature and strain rate during material deformation. The key signs of dynamic strain aging are the presence of serrated flow or yield point elongation in the stress-strain curve, which indicates localized fluctuations in flow stress [3]. The DSA event can also be identified through other patterns, such as peaks or plateaus in strength versus temperature curves, dips in ductility with increasing temperature, and the onset of negative strain rate sensitivity (SRS) [4]. In C-Mn steels, DSA occurrence is often attributed to interactions between dislocations and solute atoms such as carbon and nitrogen [5,6]. These elements diffuse toward dislocations at elevated temperatures and form solute atmospheres that hinder the mobility of dislocations through the process of pinning [7,8]. [PERSON] and [PERSON] [9,10] explored the influence of the DSA process on yield strength and cumulative plastic strain under cyclic loading in stainless steels at elevated temperatures. They proposed a temperature-dependent function integrated into the dynamic recovery term of the A-V hardening model. [PERSON] et al. [11] extended the Ohno-Wang hardening model [12] to develop a single model predicting DSA effects in a temperature range of 293-823 K, showing an increase in DSA activity with rising operating temperature. [PERSON] et al. [13] presented how the DSA event had a significant impact on the mechanical properties of railway steel bars primarily under various strain rates and with high contact temperatures. At higher strain rates, steel samples with finer pearlitic structures displayed increased strength and hardness. [PERSON] et al. [14] investigated the ratcheting response of SA333 steel at room temperature and within the 250-350 \({}^{\circ}\)C temperature range. Their results indicated that ratcheting deformation was suppressed at intermediate temperatures. However, with increasing cyclic stress amplitude, greater ratcheting strain and shorter fatigue life were achieved. [PERSON] and [PERSON] [15] conducted cyclic tests on some carbon steel alloys of AISI 1008, 1010, 1020, 1035, and 1522 over a temperature range of 373-873 K and at various strain rates. They reported negative strain-rate sensitivity of flow stress in the DSA-active regime. To better understand the DSA mechanism, researchers have employed several techniques, including transmission electron microscopy (TEM) [16], X-ray diffraction (XRD) [17], and mechanical testing [18]. In addition to using analytical approaches to assess ratcheting behavior at elevated temperatures, the most common numerical methods, such as finite element analysis, have been widely utilized, where experimental data acquisition was found to be complex, lengthy, and costly [19, 20, 21].