The temperature-dependent flow behavior in nominally binary Al-Mg alloys measured recently [1,2] is interpreted in the context of a parameter-free solute strengthening model. The recent measurements show consistently higher strengths as compared to literature data on true binary Al-Mg alloys, which is attributed to the presence of Fe in the nominally binary Al-Mg. Using the Fe concentration as a single fitting parameter, the model predictions for the newer materials when treated as Al-Mg-(Fe) alloys agree with experiments to the same degree as obtained for the true binary Al-Mg. The model then predicts the activation volume in good agreement with experimental trends.In interpreting experimental data for strengths of Al alloys, multiple mechanisms operating simultaneously are often invoked because the application of simple or ad-hoc theories does not explain observed trends. For instance, HallPetch effects [2], anomalous athermal stresses [6], solute clustering [6,7], and/or unphysical dislocation/solute interactions [8][9][10], have been invoked to justify deviations between various solute strengthening theories [8][9][10][11][12] and experimental data. However, such reasonable attempts to rationalize experimental data obfuscate the relevant underlying mechanisms. Here we re-examine recent data on a set of nominally binary Al-Mg alloys first reported by Jobba et al.[1] and then further analyzed by Niewczas et al. [2]. We show that the finitetemperature flow behavior of the alloys in these works can be explained by the inclusion of a low concentration of Fe without the need to invoke any other additional mechanisms.The solute strengthening model was developed in Refs. [13,14] and only key points are summarized here. When moving through a random field of solutes with concentration c, an initially straight dislocation can lower its energy by bowing into regions containing favorable solute configurations and bowing away from regions with unfavorable solute configurations. The segments thus reside in favorable solute configurations and require stress-and thermally-driven activation to escape and move to the next favorable environment. The characteristic energy barrier ∆E b for pinned segments is ∆E b = 1.22