To demonstrate the generality of our scattering models, we applied the model fitting and analysis to a variety of D-A conjugated polymer SAXS. We collected and modeled SAXS profiles of the conjugated polymers PTII-2T, DPP2T-TT, and DPP-BTz that we used in our previous study . Information on these material systems can be found in the Experimental section and in the Figure caption. In addition, we visually extracted and modeled scattering profiles of other conjugated polymers published in previous works, including PDPP2FT-C16, P3HT-b-DPPT-T, and P(NDI2OD-T2) . FA model fits and their individual contributions are shown for the conjugated polymers in Figure with parameters summarized in Table . Information on the material systems of the extracted data can be found in the figure caption. PTII-2T in CB shows similar scattering to high MW PII-2T in CB (large aggregates) although the Guinier knee corresponding to the dispersed population occurs as lower 𝑞. As a result the mean radius of the polymer is larger at 22.1 Å. Additionally the intermediate slope corresponding to the semiflexibility of dispersed chains is nearly -1 indicating rod-like rigidity which is in agreement with the high degree of planarity of PTII-2T . As a result, the persistence length is significantly larger than the radius 𝑙 𝑝,𝑝 ≫ 𝑅 𝑝 but its exact value cannot be reliably extracted in this asymptotic limit or with the available 𝑞-range. For DPP2T-TT in CB, while the scattering profile is similar to PTII-2T and high MW PII-2T, the apparent slope at ~0.015 Å -1 is in fact shallower than -1 meaning that the intermediate feature cannot be due to the persistence length of the polymer as the shallowest possible slope possible would be -1 if the polymer were a rigid rod. Therefore, contrary to other polymers the intermediate Guinier knee at 0.03 Å -1 must correspond to the overall size of the polymer as opposed to its cross-section as seen by the low 𝑞 power law slope of 0 in the dispersed polymer contribution. This allows us to extract the contour length of the polymer. The extracted parameters show that the polymer should have a contour length 𝐿 𝑝 of ~15.5 nm, a mean radius 𝑅 𝑝 ̅̅̅̅ of 18.5 Å, and a persistence length 𝑙 𝑝,𝑝 of 9.3 nm which is in agreement with previously reported theoretical values of persistence length . For DPP-BTz in CB, the scattering pattern was fit to the FA model without any dispersed polymer contribution indicating that nearly all of the polymers are in an aggregated state. The fibril aggregate has a diameter 𝐷 𝑓 of 6.2 nm and exhibits rod-like behavior as the fibril persistence length must be significantly larger than the radius to exhibit an effective slope of -1 (𝑙 𝑝,𝑓 ≫ 𝑅 𝑓 ). For PDPP2FT-C16 in CB and P3HT-b-DPPT-T in o-dichlorobenzene (DCB), a similar solution state structure to high MW PII-2T, PTII-2T, and DPP2T-TT is seen consisting of contributions from large fibril aggregates and dispersed polymers. The extracted persistence lengths are 20 nm and 4.7 nm for PDPP2FT-C16 and P3HT-b-DPPT-T, respectively. The relatively high persistence length of PDPP2FT-C16 is consistent with the fact that the DPP unit is flanked by furans resulting in reduced backbone torsion and higher planarity in comparison to a structure with flanking thiophenes . The low persistence length of P3HT-b-DPPT-T is likely a result of the incorporation of the relatively flexible P3HT block into the backbone which has a persistence length of ~3 nm . An alternative fit for P3HT-b-DPPT-T is also possible where the intermediate Guinier knee stems from the aggregate instead of the dispersed polymer (Figure , Table ). For P(NDI2OD-T2) in DCB nearly all the polymers are in an rod-like fibril aggregate state similar to DPP-BTz. In all cases, we were able to fully model and analyze the scattering of the D-A conjugated polymers, including the lamellar structure factor peak at high 𝑞.