The resistivity q of epitaxial W(001) layers grown on MgO(001) at 900 C increases from 5.63 6 0.05 to 27.6 6 0.6 lX-cm with decreasing thickness d ¼ 390 to 4.5 nm. This increase is due to electron-surface scattering but is less pronounced after in situ annealing at 1050 C, leading to a 7%-13% lower q for d < 20 nm. The q(d) data from in situ and ex situ transport measurements at 295 and 77 K cannot be satisfactorily described using the existing Fuchs-Sondheimer (FS) model for surface scattering, as q for d < 9 nm is larger than the FS prediction and the annealing effects are inconsistent with a change in either the bulk mean free path or the surface scattering specularity. In contrast, introducing an additive resistivity term q mound which accounts for surface roughness resolves both shortcomings. The new term is due to electron reflection at surface mounds and is, therefore, proportional to the ballistic resistance times the average surface roughness slope, divided by the layer thickness. This is confirmed by a measured linear relationship between q mound and r/(Ld), where the root-mean-square roughness r and the lateral correlation length L of the surfaces are directly measured using atomic force microscopy and X-ray reflectivity. Published by AIP Publishing. [http://dx.

While the growth of pits in passive metals exposed to chloride solutions is well understood, the processes associated with the initiation and propagation of stable pits, versus pits that form and apparently re-passivate, are still a matter of conjecture. A major challenge in studying pit initiation using electron microscopy has been alteration of the structure and chemistry of the hydrated corrosion films upon transfer to the vacuum environment of the microscope. A recently developed technique uses a microfluidic liquid cell to maintain the aqueous environment in contact with the sample. This work uses such cells to directly observe pits initiating, and growing before reaching stability, in aluminum thin films under potentiostatic polarization in situ in the electron microscope. Polarization curves developed in the cell show good agreement with those observed under conventional electrochemical experimental conditions. We observed current transients representative of metastable pitting and were able to relate crystalline features found in situ with topographic features using atomic force microscopy (AFM). An accumulation of aluminum surrounding an initiated pit, combined with depth profiling using Auger electron spectroscopy suggests that aluminum metal is deposited during the pit initiation process, and may serve to reduce lateral dissolution of the aluminum film. Work is currently underway to determine if this observation is unique to the geometry of the microfluidics cell or if is a general result that occurs at the very beginning of pit initiation.

Controlling the detrimental effects of metal corrosion is a key concern in many aspects of our modern society. In research looking to elucidate the mechanisms that govern corrosion behavior of a metal, electrochemical techniques play an essential role [1]. While it has been shown that liquid cell transmission electron microscopy can visualize in situ the corrosion structures that form in metal thin films immersed in aqueous media [2], integration with electrochemical measurements is needed if crucial information is to be obtained about the underlying processes. Electrochemical cells for in situ TEM have seen significant development due to the needs of battery research [3], but there are technical challenges in translating the method to corrosion research. In particular, the working electrode in most corrosion experiments is the metal of interest itself. However, in the electrochemical cells for liquid cell TEM, the sample is attached to pre-patterned thin film electrodes, commonly made of Au or Pt. The exposed contact between an active metal and a noble metal can lead to rapid galvanic corrosion of the active metal (see Figure 1).Here, we will describe experiments in which a blanket Al thin film (100 nm thick) is deposited over one of the two blank chips (without pre-patterned electrodes, see Figure 2(a)) that make up the microfluidic cell in a Hummingbird Scientific liquid flow holder. The film makes contact with one of the three metal leads as the working electrode and the other two leads are used as reference and counter electrodes respectively. The electrolyte is a mixture of 0.1M Na 2 SO 4 and 0.001M NaCl dissolved in de-ionized water. The solutions are de-aerated by bubbling nitrogen gas overnight and fluid flow is maintained at 5 µl per min using a syringe pump. Potentiostatic polarization is carried out with a Gamry Reference 600 potentiostat with concurrent observations recorded at TV rate (30 frames per sec) in a FEI CM30 TEM operated at 300kV.Figure 2 (c)-(e) shows successive images in which the dissolution of individual grains (seen with dark diffraction contrast) in the film is observed as the potential is raised from -200 mV in 0.5 mV/s steps. As expected, the dissolution takes place in the anodic portion of the curve. These experiments demonstrate direct observation of localized corrosion under potentiostatic control, but the design suffers from two issues. First, corrosion is most rapid at the contact between the film and metal lead, which can lead to loss of electrical contact during an experiment. Second, corrosion takes non-uniformly over the entire film, making it challenging to quantitatively correlate the electrochemical information with the observed phenomena at the silicon nitride window. Strategies to mitigate these issues will be discussed.

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