## 1 Introduction  
Magnesium (Mg) alloys are considered among the lightest metal alloys in existence and are remarkably strong relative to their weight; in fact, their density is just a fraction of that of aluminum and that of steel [1; 2; 3]. Moreover, Mg alloys have attractive traits [4; 5; 6] in different utilizations, including the aviation and automobile sectors [7; 8; 9], including substantial specific strength, specific stiffness, and significant recyclability. In addition, owing to their weight reductions of around 10%, Mg alloys are seen as a crucial option to minimize carbon dioxide emissions from cars, as this translates to a substantial decrease in energy usage of 5-10% [10]. Nonetheless, Mg alloys' low ability to deform is a key drawback that limits their use in many fields, including aircraft and shipbuilding, due to their hexagonal close-packed (hcp) crystal structure, which results in a small range of potential deformation directions [11]. That is, Mg deformation is extraordinarily challenging because of the large discrepancies in the essential resolved shear stresses for the various slip systems [5; 12; 13; 14]. Hence, Mg and related alloys struggle to form when produced using conventional techniques such as extrusion and rolling without heating [15]. Adversely, the formability of Mg alloys is ameliorated at elevated temperatures [16; 17; 18]; the hardening effects of deformation are mitigated by dynamic recrystallization and recovery processes. Diverse Mg alloys with improved corrosion resistance, ductility, and/or both have been developed over the past few years [19; 20; 21]. Because of this, it is preferable to improve the ability to deform of Mg alloys by employing plastic processing procedures to regulate texture. Methodologies of severe plastic deformation, such as high-pressure torsion [22; 23; 24], equal channel angular pressing (ECAP) [12; 25; 26; 27; 28; 29], twist extrusion (TE) [30], multichannel spiral twist extrusion (MCSTE) [31; 32; 33], accumulative rolling bonding [34], and rolling in a three-high skew rolling mill [35], show promise for providing the ability to deform Mg alloys without heating them [36; 37]. ECAP belongs to the numerous severe plastic deformation methods that can effectively create nanostructures and ultrafine grain (UFG) structures in alloys that are used in a variety of industrial applications [38; 39; 40; 41]. Given the relationship of the microstructural and mechanical attributes of affected materials and the level of permanent alteration produced, a variety of investigators have undertaken a period of study investigating various elements of the ECAP process to examine the effect of processing variables on material behavior. Thus, it was critical to the design of an ECAP process to comprehend the phenomenon of strain growth. As shown by Equation (1) [38; 39], the equivalent strain (\(\epsilon_{eq}\)) could be calculated theoretically based on the die shape. The strain of the specimens produced by the ECAP method was determined by the number of passes (N), the inner channel angle (\(\phi\)), and the outside corner angle (\(\Psi\)), as explained in [38; 39]. The three most common forms of ECAP routes are A, BC, and C [42; 43; 44]. Route A entails making multiple passes over the sample without rotating it while performing any of them. On the other hand, the specimen is turned by 90\({}^{\circ}\) with the very same orientation along its longitudinal axis after each transit in the case of route BC [22; 43; 42]. Upon the completion of every single pass over route C, the specimen is turned by 180\({}^{\circ}\) to face the opposite orientation of the extrusion path [44; 45]. Large alterations in texture, microstructure, and mechanical properties can be linked to ECAP's influence on strain [42]. According to the analysis of [PERSON] et al.