(Energy Technology Division Research Award) PEM Fuel Cell Electrode Layer Degradation

Tuesday, 26 May 2015: 08:00
Boulevard Room A (Hilton Chicago)
R. L. Borup, R. Mukundan, J. D. Fairweather, D. Spernjak, D. A. Langlois (Los Alamos National Laboratory), K. L. More (Oak Ridge National Laboratory), G. Maranzana (LEMTA, Université de Lorraine, Vandoeuvre-lès-Nancy), A. Lamibrac (LEMTA CNRS), J. Dillet (LEMTA, Université de Lorraine, Vandoeuvre-lès-Nancy), S. Didierjean (LEMTA, CNRS, Vandoeuvre-lès-Nancy), O. Lottin (LEMTA, Université de Lorraine, Vandoeuvre-lès-Nancy), L. Guétaz (CEA, LITEN), R. Ahluwalia, S. Arisetty (Argonne National Laboratory), and K. Rau (Los Alamos National Laboratory)
PEM fuel cells (PEMFCs) show great promise to increase the fuel efficiency for transportation applications; however, for this increase in efficiency to be implemented in a wide-spread manner, these systems need to be competitive with current technologies.   

As PEMFCs have evolved for transportation applications from prior applications (space and stationary), materials changes have been made to increase the power density and decrease the cost (including thinner, higher conductivity membranes and higher surface area/lower Pt loadings) that have negatively affected the durability.  In addition, as these systems were developed for transportation, the operating conditions changed, including frequent start-up/shut-downs, power cycling, and higher temperature/lower relative humidity operation. 

While there has been significant progress in improving durability with lower cost materials, further improvements are needed to meet the commercialization targets. Past improvements have largely been made possible because of the fundamental understanding of the underlying degradation mechanisms. By investigating component and cell degradation modes and defining the fundamental degradation mechanisms of individual components and component interactions, new materials can be designed to improve durability.  

The primary degradation modes involve materials in the the electrode layer.  The high cost of the noble metal(s) used as the catalyst makes this a crucial area requiring durability improvement. Other degradation modes include decreases in electrode kinetics and increases in resistance of both transport and conductivity.  Although the electrode structure and durability thereof has been studied extensively, perfect solutions for commercialization do not yet exist.

The primary degradation mechanisms within the cathode catalyst layer include catalyst nanoparticle stability, catalyst support degradation, porosity losses, and ionomer degradation. Catalyst support carbon corrosion occurs under normal fuel cell operating conditions and is exacerbated by the voltage cycling inherent in transportation drive cycles.  An example of how the drive cycle potential cycling affects carbon corrosion, as measured by CO2 evolution, is shown in Figure 1.  The peak in CO2 evolution occurs when the cell potential increases from high power operation to low power near open circuit.  This correlates with when CO2 evolution is observed during cyclic voltammograms, which occurs during the positive sweep at  ~ 0.55 to 0.60 V.  The evolution of this CO2 peak suggests that oxygen is adsorbed onto the carbon and/or CO is formed on the Pt surface.

Many materials and operating variables affect the amount of carbon corrosion, including the type of carbon support used, the Pt loading and dispersion, and operating conditions, such as relative humidity (RH) and temperature.  Not surprisingly, high surface area carbons with a low extent of graphitization, exhibit the greatest amount of corrosion, followed by Vulcan carbon, which has some meso-graphitic structure, and the least amount of carbon corrosion occurs with graphitized, low surface area carbon (LSAC).  Higher Pt loadings and poor Pt dispersions lead to higher rates of carbon corrosion, which in turn leads to loss of Pt surface area, thinning of the electrode layer, and increases in mass transport losses.

However, as Figure 2 demonstrates, carbon corrosion is only a portion of the issues in play.  Figure 3 shows the initial and final Pt particle sizes for the same carbon support materials.  In this case, the Pt size (measured by XRD) is inversely correlated to the amount of carbon corrosion, with the greatest Pt size observed after shut-down/start-up ageing for graphitized LSAC carbon.

Together with the other degradation mechanisms, a reduction in catalyst layer thickness is observed during drive cycle operation, which can be due to the loss of carbon through carbon corrosion or due to compaction; both effects likely lead to a loss of void volume.  This reduction in thickness includes a sharp decrease in catalyst layer thickness within the first 100 hours of operation (30%), eventually reaching ~50% of its thickness after 1000 hours.  Most of this reduction in electrode thickness does not appear to be directly due to carbon corrosion as there is little evidence for carbon corrosion from microscopic analysis, especially during the early stages of operation, where the thickness reduction is substantially more than what should be due to carbon corrosion.


Funding for this work is from DOE EERE FCTO, Technology Development Manager Nancy Garland

I gratefully acknowledge all of my collaborators from Los Alamos, Ion Power, University of Nancy, Commissariat à l'énergie atomique et aux énergies alternatives, Argonne National Lab and Oak Ridge National Lab.