We demonstrate that extensive electrochemical shock-electrochemical cycling induced fracture-occurs due to coherency stresses arising from first order cubic-to-cubic phase transformations in the spinels LiMn 2 O 4 and LiMn 1.5 Ni 0.5 O 4 . Electrochemical shock occurs despite the isotropy of the shape changes in these materials. This electrochemical shock mechanism is strongly sensitive to particle size; for LiMn 2 O 4 and LiMn 1.5 Ni 0.5 O 4 , fracture can be averted with particle sizes smaller than ∼1 μm. As a further critical test of the proposed mechanism, iron-doping was used to induce continuous solid solubility of lithium in LiMn Batteries based on ion-intercalation reactions-exemplified by lithium-ion batteries-enable high energy densities which are attractive for applications ranging from portable electronics to electrified transportation to grid-level storage. To achieve high storage capacities and energy density, ion-intercalation hosts must undergo large composition changes, which are often accompanied by large shape changes. These shape changes can result in electrochemical cycling-induced fracture, a phenomenon we have termed "electrochemical shock," which contributes to impedance growth and performance degradation. Electrochemical shock has been observed in a variety of ionintercalation materials with widely varying compositions and crystal structures 1-7 and it can cause severe deleterious effects on battery performance, manifested as impedance growth upon cycling. This has been clearly demonstrated during early cycling (first 500 cycles) of LiNi 0.8 Co 0.15 Al 0.05 O 2 (NCA) cathodes, for example. 3 Previously, we and others showed that electrochemical shock in intercalation electrodes can be C-rate dependent, such as occurs when steep gradients in ion concentration generate diffusion-induced stresses sufficient to cause fracture. 8,9 Alternatively, electrochemical shock can occur by C-rate independent mechanisms, such as anisotropic shape changes in polycrystalline aggregates (e.g. secondary particles); this mechanism depends on crystal symmetry and state-of-charge, but not on cycling rate. Layered LiCoO 2 and isostructural derivative compounds such as Li(Ni,Co,Al)O 2 are a few examples amongst many in which electrochemical shock is dominated by the C-rate independent anisotropic shape change mechanism.10,11 (In distinguishing C-rate dependent vs. independent, we consider the rate dependence of a mechanism, not of a material. We have adopted a convention of calling C-rate independent any electrochemical shock mechanism that persists to arbitrarily small C-rates. Therefore, if electrochemical shock is observed during low C-rate cycling, this is clear evidence that a C-rate independent mechanism is active. At sufficiently high C-rates, the C-rate dependent concentration gradient mechanism will be simultaneously active and the observed damage accumulation in a given material may not be C-rate independent.) This classification scheme applies most directly to materials that undergo brittle fracture,...