ing the ethane-like Ge$_2$Se$_3$ units. These subnetworks were reported in GeSe$_2$ by Boolchand and coworkers [@boolchand2000] and in ternary chalcogenide glasses by Mitkova and coworkers [@mitkova2006]. We find that these Ge-Se stoichiometries have different bondlength distributions: Se rich phases ($n_{Ge-Se} \geq 4$) have bondlengths smaller than 2.55 Å whereas Ge-rich phases ($n_{Ge-Se} < 4$) have bondlengths longer than 2.55 Å. In an insulating conformation, the former phase dominates and registers an RDF peak at $\approx$ 2.40 Å (Fig. \[fig6\]). For metallic conformations, fewer Se atoms are available to Ge. This increases the fraction of Ge-rich phases and the Ge-Se bondlength distribution shifts to longer distances. This is represented by a shift in Ge-Se pair correlation function in Figure \[fig6\] (inset) and appearence of peak P3 in total RDF. Due to increase in fraction of Ge$_2$(Se$_{1/2}$)$_6$, Ge-Ge correlation peak appears around 3.5 Å in metallic models. We note that it is such a Ge-Ge signal in Raman scattering and $^{119}$Sn M$\ddot{o}$ssbauer spectroscopy that led to experimental discovery of Ge-rich Ge$_2$(Se$_{1/2}$)$_6$ phase in stoichiometric bulk Ge$_x$Se$_{100-x}$ glasses [@boolchand2000].

![The total radial distribution function (g(r)) of the insulating and metallized models (black and red curves respectively) at $x$=0.25. Note the bifurcated first peak originates from Ge-Se correlation (P1 at 2.40 Å) and Ag-Se correlation (P2 at 2.67 Å). For metallized model, peak P3 arises due to depletion of tetrahedral 2 and formation of Ge-rich Ge-Se phases.[]{data-label="fig6"}](corr.eps){width=".8\linewidth"}

Now we comment further on the role of Ag-Se phase in metallicity. It is well known that the states around Fermi energy are mainly Se p-orbitals ([@prasai2011; @tafen2005], In GeSAg: [@akola2015]). The electronic structure of metallic model projected onto its constituent subnetworks (Ag-Se and Ge-Se) shows different electronic activity of Se-atoms in the two subnetworks. We find t