charge transfer at surfaces [2] or by potentially increasing catalytic selectivity by the localization of minority carriers, [3] and have been predicted to form better transparent conducting oxides (TCOs) than materials that conduct through band transport. [4] But polaron transport is sluggish, and the polaron-induced limitations to charge carrier mobility are well known to the applied science community. [3,5,6] These limitations are especially prevalent in transition metal oxides, which are prone to form smallpolarons (tightly bound) due to the strong electron correlation within the valence d-orbitals. [7] For instance, next-generation p-type TCOs like CuAlO 2 and ZnRh 2 O 4 , which are essential to realizing low-power transparent electronics, have limited performance due to the low mobilities of smallpolarons. [8] The transport of small-polarons in energy-conversion materials have necessitated decreasing diffusion path dimensions to the nanometer length scale [3] and smallpolarons can establish a fundamental limit for the Fermi level in materials like Fe 2 O 3. [9] Similarly, in small-polaron oxides used as active materials in Li-ion batteries, the low mobility of polarons has been observed to slow down Li diffusion, leading to accumulation of Li-ions at the electrode interface and low battery capacities. [2] The small-polaron hopping model has been used for six decades to rationalize electronic charge transport in oxides. The model was developed for binary oxides, and, despite its significance, its accuracy has not been rigorously tested for higher-order oxides. Here, the small-polaron transport model is tested by using a spinel system with mixed cation oxidation states (Mn x Fe 3−x O 4). Using molecular-beam epitaxy (MBE), a series of single crystal Mn x Fe 3−x O 4 thin films with controlled stoichiometry, 0 ≤ x ≤ 2.3, and lattice strain are grown, and the cation site-occupation is determined through X-ray emission spectroscopy (XES). Density functional theory + U analysis shows that charge transport occurs only between like-cations (Fe/Fe or Mn/Mn). The site-occupation data and percolation models show that there are limited stoichiometric ranges for transport along Fe and Mn pathways. Furthermore, due to asymmetric hopping barriers and formation energies, the Oh Mn + + 2 2 polaron is energetically preferred to the Oh Fe + + 2 2 polaron, resulting in an asymmetric contribution of Mn/Mn pathways. All of these findings are not contained in the conventional small-polaron hopping model, highlighting its inadequacy. To correct the model, new parameters in the nearestneighbor hopping equation are introduced to account for percolation, cross-hopping, and polaron-distribution, and it is found that a near-perfect correlation can be made between experiment and theory for the electronic conductivity.