## 3 Results and Discussion
### Thermomechanical Property Tests
The ANOVA test within each dataset (n = 22) yielded a significant Snedecor F value for both strain at break (\(p<0.05\), F = 25.88) and elongation (\(p<0.05\), F = 971.47), signifying the influence of time groups on these variables. The assessment of the impact fracture energy per unit area, JC, was conducted through Charpy impact tests (Figure 9a). Similar to [35], the initially processed virgin PP exhibits high impact resistance, which gradually decreases with the addition of the plant-based filler until it remains relatively constant at a CAG of 35%. The loss of impact resistance could be due to PP degradation by chain scission [39]. Despite two heterogeneous materials being present, a perfect integration is observed in the mechanical behavior of the CAG. However, as in the case with charges of mineral origin, elevating the quantity of stress concentrators beyond a specific threshold may induce particle agglomeration, causing the material to gradually become brittle. Consequently, this can lead to rapid crack propagation and eventual material failure through fracture. This phenomenon is not perceived when the CoP content does not exceed 35%. Similarly, the outcomes of the ANOVA tests within each dataset (n = 34) revealed a significant Snedecor F value (\(p<0.05\), F = 1461.45). Therefore, the time groups exerted an effect on the response variable (Charypy). Similar to [40], the fluidity of the CAG increases as a function of the CoP content (Figure 9b), except for a slight drop in the 30% CoP mix, in which this resulting CAG property presents approximately the same rheological properties as virgin PP. However, when a 35% load is added, the fluidity increases three-fold. This finding aligns with the observations documented by [11], when mixing 5 wt.% CoP caused a reduction of around 50% of the MFI, which was attributed to the extrusion process of the CAG. These phenomena of trend changes are characteristic of PP. Certainly, given that PP is a semicrystalline polymer, one can infer at the initial stage that the most degraded chains are likely to be those from the amorphous phase [39; 41]  
The ANOVA test within each dataset (\(n=29\)) produced a significant Snedecor F value (\(p<0.05\), F = 182.12), indicating that the time groups had an impact on the MFI. The thermograms depicted in Figure 10 display the DSC results for the 11.1 mg samples. The striped areas corresponding to the pure PP and the CAG exhibited remarkable similarity. The initial phase signifies material homogenization (these phases have been shortened to focus on the relevant processes), while the subsequent phase change indicates polymer melt (T\({}_{\rm m}\)). The following line visible in all graphs represents the pulse line or solidification. The enthalpy (\(\Delta\)H) of the process and the subsequent crystallinity remained consistent across all the cases. The T\({}_{\rm m}\) of the pure CoP was approximately 169.93 \({}^{\circ}\)C, and the T\({}_{\rm m}\) of the processed pure PP was around 166.23 \({}^{\circ}\)C, whereas the T\({}_{\rm m}\) in the CAG (CoPX:PPY) ranged between 168.59 and 169.18 \({}^{\circ}\)C, suggesting no significant change with the addition of the CoP. For semicrystalline thermoplastics, in molten conditions, the long molecular chains form irregular entangled coils, while these chains rearrange themselves and form crystal-like structures when they solidify [42]. According to [38; 43], DSC results show that the CAG also improved the nucleating activity of the CoP, making the crystallinity of PP occur at higher temperatures. Table 4 presents a summary of the crystallinity rates of the CAG, calculated using Equation (1). It is evident that the crystallinity rate, \(\chi_{\rm c}\), is not notably influenced by the augmentation of the additive content, according to [44]. Note how the 20:80 blend exhibits a 29-31% match between \(\chi_{\rm c}\) and the 30:70 [45] and a change of trend is revealed in the 35:65 mix, with crystallinity increasing once again.