V. Focused Fundamental Research - EERE - U.S. Department of ...
V. Focused Fundamental Research - EERE - U.S. Department of ...
V. Focused Fundamental Research - EERE - U.S. Department of ...
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Sastry – U. Michigan<br />
V.E.2 Thermo-electrochemistry, Capacity Degradation and Mechanics with SEI Layer (U. Michigan)<br />
inside the active particle as well as the SEI layer, in the<br />
latter case by considering a misfit due to the difference in<br />
volume expansion between the two phases. For this<br />
experimental study, the interfacial impedance change as a<br />
function <strong>of</strong> cycling number and storage at various<br />
conditions is measured via the EIS technique. The<br />
composition change and thickness <strong>of</strong> the surface layer<br />
were then examined via X-ray Photoelectron<br />
Spectroscopy.<br />
Results<br />
Multiphysics FE model – The microstructure <strong>of</strong><br />
percolated particle aggregates has been generated using a<br />
Brownian dynamics simulation as shown in Figure V - 184a.<br />
(blue: active materials, red: inert materials). This<br />
microstructure <strong>of</strong> particle aggregates has been modeled for<br />
finite element analysis as shown in Figure V - 184b and Figure V<br />
- 184c. At the middle <strong>of</strong> the cathode, the temporal variation<br />
<strong>of</strong> reaction current density from the pseudo-2D thermoelectrochemical<br />
model and 3D microscopic model is<br />
compared in Figure V - 185, which reveals a 14% difference.<br />
In Table V - 4, the calculated effective diffusivity and<br />
conductivity are compared with the approach <strong>of</strong><br />
Bruggeman’s equation.<br />
(a) (b) (c)<br />
Figure V - 184: (a) aggregated structure (b) voxel mesh (c) tetrahedral mesh<br />
Figure V - 185: reaction current density<br />
Table V - 4: Change in surface atomic concentration <strong>of</strong> each element<br />
Volume<br />
fraction<br />
Bruggeman 3D<br />
microstructure<br />
D eff active/D active 0.49 0.34 0.346<br />
D eff elyte/D elyte 0.51 0.37 0.378<br />
σ eff solid/σ solid 0.49 0.34 0.300<br />
Capacity fade due to SEI layer formation - The<br />
developed model enabled us to overcome the limitation <strong>of</strong><br />
a conventional approach that assumes a steady state (at low<br />
frequencies the system may vary due to the long duration<br />
<strong>of</strong> measurement). Also, this numerical approach can<br />
facilitate the experimental studies on capacity fade due to<br />
SEI layer formation because capacity fade in Li-ion<br />
batteries comes from complex processes. The simulation<br />
demonstrated that capacity fade was accelerated as the film<br />
resistance increases, as shown in Figure V - 186a. It also<br />
demonstrated that impedance characteristics and frequency<br />
responses were changed depending on film resistance, as<br />
shown in Figure V - 186b.<br />
(a)<br />
Figure V - 186: (a) capacity change (b) frequency response function<br />
Anode particles near the separator underwent high<br />
stress due to (de)intercalation, which resulted in structural<br />
degradation <strong>of</strong> the active particles as shown in Figure V -<br />
187a. When the SEI layer was formed at the surface <strong>of</strong> the<br />
(b)<br />
anode particle, this layer changed the stress evolution<br />
inside the particle due to the mismatch <strong>of</strong> the partial molar<br />
volume as shown in Figure V - 187b. Also, this SEI layer itself<br />
underwent high stress due to the expansion <strong>of</strong> the active<br />
FY 2011 Annual Progress Report 633 Energy Storage R&D