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The early attempts of [PERSON] and coworkers provided a qualitative or semi-quantitative analysis of the SRO structure of borate glasses by employing infrared reflectance and Raman spectroscopies [16; 19; 20; 21]. Moreover, while synchronous NMR studies can unambiguously provide a quantification of the tetrahedral units population, the discrimination of the corresponding molar fractions of the various triangular units is still unresolved [22; 23; 24; 25]. In addition, valuable information on the SRO structure of glasses can be obtained by employing advanced experimental methods, like neutron and X-ray diffraction [26; 27; 28; 29], extended X-ray absorption fine structure (EXAFS), or X-ray absorption near-edge structure (XANES) techniques [30; 31; 32]. More details on these advanced methods can be found in the excellent reviews for neutron diffraction studies [33] and EXAFS-XANES techniques [34; 35] and references therein. It is worthwhile to note that a detailed mapping of the borate structure can be obtained by employing classical molecular dynamics (CMD) simulations [36; 37; 38; 39], machine-learning molecular dynamics [40], or ab initio molecular dynamics (AIMD) studies [41; 42]. All these simulations are calibrated to reproduce existing experimental data, mostly the radial distribution functions and the structure factors obtained through neutron scattering or X-ray diffraction studies, though a convincing agreement with vibrational or NMR spectra is still lacking. Recently, we fully resolved the SRO structure of bismuth borate glasses, xBi\({}_{2}\)O\({}_{3}\)-(1-x)B\({}_{2}\)O\({}_{3}\), by a careful analysis of infrared absorption coefficient spectra into Gaussian component bands, combined with charge and mass balance considerations as well as the Lambert-Beer law for the integrated areas of the component bands [43]. Moreover, we also identified the SRO structure of binary zinc borate glasses, xZnO-(1-x)B\({}_{2}\)O\({}_{3}\), by a completely different approach, introducing an extension of the well-known lever rule, namely the short-range order configuration model (SROC) [44]. A brief discussion of the SROC model is presented in the next section. While the analysis of infrared absorption coefficient spectra into Gaussian component bands can, in principle, be applied in any family of glassy materials, the unknown molar fractions of the structural units, along with the unknown absorption coefficients of each particular unit, may result in an underdetermined system of equations with the number of unknown parameters exceeding the number of equations. On the other hand, the application of the SROC model is always possible when the metal oxide acts exclusively as a modifier of the former glass, from a chemical viewpoint of glass formation. In the case of metal oxides that assume both a modifier and network-forming role, the SROC model cannot be applied [44]. With the above restriction in mind, this article extends the application of the SROC model to bismuth borate glasses, namely xBi\({}_{2}\)O\({}_{3}\)-(1-x)B\({}_{2}\)O\({}_{3}\), in the \(0.20\leq\mathrm{x}\leq 0.40\) range, where Bi\({}_{2}\)O\({}_{3}\) acts predominantly as modifier [43]. Our extension requires a modification of the originally proposed SROC model by adding an additional node in the composition range (see Section 3.2), resulting in an augmented version of the original model. In doing so, we also define the prerequisites and the necessary conditions for any future modified version of the SROC model. The proposed augmented short-range order configuration model (ASROC) of this study provides the molar fractions of the borate units in a continuous way throughout the composition range investigated. Furthermore, it is explicitly shown how the onset of disproportionation reactions between borate units can be handled in the framework of the introduced ASROC model. The results for the SRO structure of the investigated glasses in the \(0.20\leq\mathrm{x}\leq 0.40\) range are in excellent agreement with the existing literature data.