Abstract

Excellent physical and optical properties of AlN films such as high melting temperature, high thermal conductivity at room temperature, good chemical stability, wide band gap [1, 2] make AlN very promising for several applications such as UV-visible detectors and emitters, optoelectronic displays, and GaAs and silicon carbide passivation [2, 3]. Furthermore, AlN is a suitable candidate for the fabrication of AlxGayIn1−x−yN [3] based electronic and optical device applications. AlN thin films have been grown by using several growth techniques under different growth conditions such as temperature, pressure, precursors, etc. While high-temperature (typically above 1100 ◦C) grown epitaxial AlN films are used in active electronic and optoelectronic device layers, polycrystalline and amorphous AlN films grown at CMOS-compatible temperatures (lower than 300 ◦C) are widely used as dielectric and passivation layers for microelectronic devices [4]. To utilize the full potential of the group III-nitride material system for the mature CMOS technology requires the growth of group III-nitride alloys and heterostructures in the temperature range below 300 ◦C. To overcome the presently encountered limitations for low growth temperatures, plasma enhanced atomic layer deposition (PEALD) of AlN is a promising growth technique which not only reduces the film growth temperature, but also satisfies critical conformality and sub-monolayer thickness control as well [5, 6]. Although the growth of AlN films at different low growth temperatures (100–500 ◦C) has been studied by several groups based on PEALD growth method [7–9], the properties of crys-

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