the rigidity of the polymeric chains has a smaller effect on the low-frequency spectra. Therefore, the low-frequency spectra are mainly determined by the non-bonding LJ interactions, whereas the elasticity is mainly determined mainly by the bonding rigidity. As a results, the BP decouples with the macroscopic elasticity, as demonstrated in the previous study [@Giuntoli:2018fv].

In contrast to the the results presented in Ref. [@Giuntoli:2018fv], the rigidity of the polymeric chains is necessary to determine the elasticity and the low-frequency spectra with respect to the bonding energy scale of $\varepsilon_\mathrm{FENE} = 30$. In fact, the $\varepsilon_\mathrm{bend}$ reduces the height of $g(\omega_\mathrm{BP})/\omega_\mathrm{BP}^2$, as shown in Fig \[fig4\]. In this case, the BP couples with the macroscopic elasticity. However, the plot of the scaled $g(\omega)/( \omega^2 A_\mathrm{D})$ as a function of$\omega/\omega_\mathrm{D}$ does not collapse between the polymer glasses and LJ glass, as shown in Fig. \[fig6\]. The height of $g(\omega)/ (\omega^2 A_\mathrm{D})$ is consistent between the polymer glasses and LJ glass, but $\omega/\omega_\mathrm{D}$ of the LJ glass is lower than that of the polymer glasses. This result indicates that vibrational states differences between polymer glasses and LJ glasses cannot be described only by changes in macroscopic elasticity, changes in the local elastic properties 