## 3 Results and Discussion
The addition of different chemical elements in these multicomponent alloys results in a dense 'random-packed' structure, which significantly restricts atomic mobility, a crucial factor for crystallization. This, in turn, may enhance the thermal stability of the alloys [51; 52]. The particle sizes of Al82 Fe14 Mn2 Ce2 powders are slightly larger than those of Al82 Fe16 Ce2 after milling for 5, 10, and 20 h (Figure 5). This can be explained by the enhanced softness of the powder material with Mn addition, making cold-welding processes during ball-collisions more favorable. The particle shapes of all three alloys appear rather spherical than flake-like, indicating that impact events during ball collisions dominated the sliding events. After milling for 40 h, the particle size of Al82 Fe14 Mn2 Ce2 powders was in the range of 2 \(\div\) 10 \(\upmu\)m due to agglomeration phenomena (Figure 5). Figure 6a,b presents the magnetization curves (M-H) for Al\({}_{82}\)Fe\({}_{16}\)Ce\({}_{2}\) and Al\({}_{82}\)Fe\({}_{14}\)Mn\({}_{2}\)Ce\({}_{2}\) alloys after milling. All the synthesized alloys show similar hysteresis loops, indicating their ferromagnetic nature [53; 54]. Table 2 summarizes the properties obtained from the M-H curves (saturation magnetization-M\({}_{\rm s}\) and coercive force-H\({}_{\rm c}\)). The maximum saturation M\({}_{\rm s}\) decreases from 29.5 and 24.69 emu/g to 1.53 and 1.41 emu/g for Al\({}_{82}\)Fe\({}_{16}\)Ce\({}_{2}\) and Al\({}_{82}\)Fe\({}_{12}\)Mn\({}_{2}\)Ce\({}_{2}\) alloys milled from 5 h to 40 h, respectively. The saturation magnetization values of the two amorphous alloys are similar to that of Al\({}_{82}\)Fe\({}_{14}\)Ti\({}_{2}\)Y\({}_{2}\) amorphous alloys (M\({}_{\rm s}\) = 1.5 emu/g) and slightly greater than that of Al\({}_{82}\)Fe\({}_{14}\)Ni\({}_{2}\)Y\({}_{2}\) amorphous alloys (M\({}_{\rm s}\) = 0.8 emu/g). The saturation magnetization depends on the phases  
Figure 3: SEM images of Al\({}_{82}\)Fe\({}_{16}\)Ce\({}_{2}\) powders after milling for (**a**,**b**) 5 h, (**c**,**d**) 10 h, (**e**,**f**) 20 h, and (**g**,**h**) 40 h.  
present (crystalline structure) in the alloys and their chemical composition. By comparing Figures 2-6, it is realized that by increasing the milling time from 5 to 40 h for the Al82 Fe16 Ce2 and Al82 Fe14 Mn2 Ce2 alloys, the M\({}_{\text{s}}\) decreases due to the content of the ferromagnetic phases-bcc-Fe decreasing, the content of paramagnetic phase-fcc solid solution increasing, and, at the final milling state, a transformation of solid solution to amorphous phase occurring [43]. The tendencies of the coercive force H\({}_{\text{c}}\) of both alloys are similar. In the early milling state, there are large numbers of defects and microstrain introduced to the mixture of powder due to the strong collision between powders and milling tools. Therefore, a high H\({}_{\text{c}}\) value of 366.45 and 398.99 Oe is obtained for the Al82 Fe16 Ce2 and Al82 Fe14 Mn2 Ce2 alloys after 5 h of milling, respectively. For longer milling times of 10 h, line broadening of the peaks in Figures 2 and 4 indicates the reduction in the crystallite size and lattice strain introduced by milling, so H\({}_{\text{c}}\) decreases very quickly to 118 and 81.02 Oe for the Al82 Fe16 Ce2 and Al82 Fe14 Mn2 Ce2 alloys, respectively. The H\({}_{\text{c}}\) increases again with increasing milling time to 20 h when amorphous phases start forming in the alloys. In their amorphized state, the Al82 Fe16 Ce2 and Al82 Fe14 Mn2 Ce2 alloys show coercivity (H\({}_{\text{c}}\)) values of 156.69 Oe and 158.45 Oe, respectively. These values are lower than those exhibited by the Al82 Fe14 Ni2Y2 and Al82 Fe14 Ti2Y2 alloys, which are 186.5 Oe and 198.9 Oe. According to the standard classification of ferromagnetic materials, those with an H\({}_{\text{c}}\) value less than 1000 A/m (approximately 12.57 Oe) are considered to be'soft magnetic'.