Rechargeable lithium ion batteries are integral to today's information-rich, mobile society. Currently they are one of the most popular types of battery used in portable electronics because of their high energy density and flexible design. Despite their increasing use at the present time, there is great continued commercial interest in developing new and improved electrode materials for lithium ion batteries that would lead to dramatically higher energy capacity and longer cycle life. Silicon is one of the most promising anode materials because it has the highest known theoretical charge capacity and is the second most abundant element on earth. However, silicon anodes have limited applications because of the huge volume change associated with the insertion and extraction of lithium. This causes cracking and pulverization of the anode, which leads to a loss of electrical contact and eventual fading of capacity. Nanostructured silicon anodes, as compared to the previously tested silicon film anodes, can help overcome the above issues. As arrays of silicon nanowires or nanorods, which help accommodate the volume changes, or as nanoscale compliant layers, which increase the stress resilience of silicon films, nanoengineered silicon anodes show potential to enable a new generation of lithium ion batteries with significantly higher reversible charge capacity and longer cycle life.

We show how finite-size scaling of bulk photovoltaic effect-generated electric field in epitaxial ferroelectric insulating BaTiO3(001) films and photo-Hall response involving the bulk photovoltaic current reveal large room-temperature mean free path of photogenerated non-thermalized electrons. Experimental determination of mesoscopic ballistic optically generated carrier transport opens a new paradigm for hot electron-based solar energy conversion, and for facile control of ballistic transport distinct from existing low-dimensional semiconductor interfaces, surfaces, layers or other structures.

In this topical review, we outline the construction of a reflection high-energy electron diffraction (RHEED) surface pole figure from a polycrystalline film by recording multiple RHEED patterns as the substrate is rotated around the surface normal. Due to the short penetration depth of electrons, the constructed pole figure is a surface pole figure. It is in contrast to the conventional x-ray pole figure which gives the average texture information of the entire polycrystalline film. Examples of the surface pole figure construction processes of a fibre texture and a biaxial texture are illustrated using Ru vertical nanorods and Mg nanoblades, respectively. For a biaxially textured film, there often exists an in-plane morphological anisotropy. Then additional intensity normalization must be applied to compensate for the effects of anisotropic morphology on RHEED surface pole figure construction. Rich information on the texture evolution, such as the change in the tilt angle of the texture axis, has been obtained from the in situ study of oblique angle vapour deposition of Mg nanoblades using RHEED surface pole figures. Finally we make a comparison between the RHEED surface pole figure and the conventional x-ray pole figure techniques.

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We observed the growth of unusual Mg nanoblades by oblique angle deposition. Although the vapor flux is obliquely incident, these nanoblades stand vertically on the substrates. The thickness of the Mg nanoblades along the incident vapor direction is reduced to approximately 15 nm to -30 nm at a vapor incident angle approximately 75 degrees, while the width perpendicular to the incident vapor direction is as wide as a few hundred nm. In addition to the anisotropic blade morphology, a (1010) [0001] biaxial (II-O) texture was observed using in situ reflection high energy electron diffraction (RHEED). The tilt angles of the texture axis and the nanoblades are correlated with the high surface diffusion on the (0001) surface along the [2130] direction. We also propose that the observed very thin thickness of the nanoblade along the vapor flux direction is due to the appearance of the surface steps parallel to the [0110] direction and the low surface diffusion on the top surface of the nanoblades.