I. INTRODUCTION Crystal growth takes place at the interface of the solid and liquid phases and is deter- mined by the structure of the crystal surface, the temperature and the supersaturation. Each growth unit is incorporated into the crystal when the energy barrier for absorption is overcome by the unit’s kinetic energy. For rough surfaces, such as K- and S-faces, the density of privileged sites, i.e. kinks, is high and growth is fast. In this work, however, we consider initially flat faces such as the F-faces. For these surfaces, at low supersaturation values, kink sites are scarce and the growth process is slow. Growth units encounter the kinks directly from solution, or via a random walk due to 2D-diffusion on the surface. New steps are either generated through spiral dislocations or 2D-nucleation[1–6]. The tempera- ture is a determining factor. It is well known that there exists a critical value, T$_{R}$ , where the step edge free energy vanishes and the crystal surface becomes rough at the growth unit scale. This is a thermodynamic phase transition, known as thermal roughening[7–12]. At constant temperature, the driving force is the chemical potential difference or su- persaturation and an increase in the driving force will translate into a decrease in critical nucleus size. Since for temperatures less than T$_{R}$ the step edge’s free energy is greater than zero, according to the Gibbs-Thomson relation [13, 14], an activation barrier for the forma- tion of the critical two-dimensional nucleus exists and with it, a critical nucleus size larger than the crystal’s individual building blocks. The size of this 2D-critical nucleus is inversely proportional to the temperature and the supersaturation [1]. Recently, it has been reported for protein crystallization systems [15, 16] that for temper- atures lower than T$_{R}$ there exists a critical supersaturation for which the size of the critical two-dimensional nucleus is reduced to the order of one growth unit and the activation bar- rier for two-dimensional nucleation essentially vanishes. Due to a large step density and a very small two-dimensional critical nucleus at elevated supersaturations, the surface becomes rough and offers many favorable sites almost uniformly distributed across the surface. Con- sequently, arriving molecules can be incorporated quasi at any site. This transition from a slow, layer-by-layer growth regime to a fast continuous growth regime at high driving forces is referred to as kinetic roughening transition [17–22]. Kinetic roughening for the case of crystallization from solution has been observed for many small molecules, i.e. SiO$_{2}$ , Al$_{2}$O$_{3}$ , ZnO and ZnS [23, 24], n-paraffins [25, 26] and 2