## 3 Results
### Computational Model Validation  
The proposed and implemented numerical model was validated from the comparison between the experimental and the numerical simulation results. The combination of materials used were PoH15, PoH20, PoB5H15, and PoB5H25. The results are summarized in Table 4, and a comparison was made between the elastic modulus values of the samples. An improvement in the elastic modulus was perceived in the samples with bentonite, where the PoB5H15 and PoB5H20 samples show increases of 45.22% and 26.87%, respectively, compared to the PoH15 and PoH20 samples. This could be attributed to the rigidity of the filler particles, which increases the modulus due to the reinforcing effect [40]. Not so for the PoB5H25 sample, which presented a loss of stiffness of 26.39% compared to PoH25. This behavior occurs in fiber-reinforced polymer matrix composites and is justified by the existence of a limit in the amount of fibers which can begin to optimally cohere the matrix and, when this limit is exceeded, a decrease occurs in the material properties [36; 37]. The semi-empirical equations will be applied to hybrid polymer nanocomposites reinforced with similar fibers and clays. Despite the different collapse loads used, all the samples exhibited similar cracking, propagation, and physical discontinuity behavior. The cracks start at one of the ends of the specimen, because the highest mechanical stress was discovered at the ends. In that way, the crack propagates diagonally, as illustrated in Figure 11.  
The fractomechanical behavior is presented from experimental stress-strain graphs (blue color) and although all the samples have the same behavior, Figure 11 presents the stress-strain graph corresponding to 15% of fibers, specifically the PoH15 material, where two zones are seen, one linear elastic and the other softening. The linear elastic zone harbors a higher fracture energy than the softening zone, due to the nature of the properties of the natural fibers in conjunction with the matrix. At the same time, it is possible to \begin{table}
\begin{tabular}{c c c c c} \hline \hline \multirow{2}{*}{**Sample**} & **Endurance** & \multirow{2}{*}{**Elongation (\%)**} & **Elastic Module** & \multirow{2}{*}{**Increase (\%)**} \\  & **(MPa)** & & **(MPa)** & \\ \hline PoH15 & 18.37 & 9.60 & 191.35 & \\ PoB5H15 & 18.34 & 6.60 & 277.88 & 45.22 \\ PoH20 & 21.06 & 10.1 & 208.51 & \\ PoB5H20 & 20.37 & 7.70 & 264.55 & 26.87 \\ PoH25 & 24.16 & 4.50 & 536.89 & \\ PoB5H25 & 21.34 & 5.40 & 395.19 & \(-\)26.39 \\ \hline \hline \end{tabular}
\end{table} 
Table 4: Experimental results. Figure 11: View of the breakage of the composite material samples. visualize that when the maximum tensile load is exceeded, the total collapse of the material is progressive and not instantaneous like brittle materials. The fibers present a tensile stress of 23.15 N, and maximum tension of 283 MPa. The constitutive model proposed through the implementation of the calculation algorithm has a good fit concerning the collapse load since the tensional arguments start the criterion of failure or damage, as shown in Figure 12a-d. On the other hand, the loss of mechanical properties, generated by the numerical softening controlled by the internal variable of damage, presents a convincing but not exact fit. Since the proposed algorithm does not contemplate the normalization of the fracture energy in the damage parameter and focuses on a linear damage loss, it is adjusted by the unit deformation at the moment the discontinuity is completed, which is highly sensitive to local deformation at each node and, therefore, to the element that is analyzed at different times. The two main contributions of this work are that it was determined that the addition of bentonite nanoparticles, at 5 wt%, previously organophilized, increased the tensile and impact resistance of the polymeric matrix composites (thermoset) reinforced with Cannabis sativa fibers.