to that, superior tensile properties of AM 316L were also obtained at temperatures of 250 [7] and 800 C. [8] For long time exposures under high temperatures, however, unstable dislocation cells can deteriorate the creep properties. [9,10] Saeidi et al. [8] also observed the propagation of Luders bands, which are closely related to dynamic strain aging (DSA), at 800 C. However, no systematic study on the influence of the SLM microstructure on the mechanical properties over the entire temperature regime from room temperature to 900 C has been conducted yet. This is surprising, as AISI 316L is a widely used austenitic stainless steel for applications at elevated temperatures, and it is known from the conventionally produced material that DSA occurs at elevated temperatures. The improvement of the process parameters in recent years with respect to the laser power, hatch distance, scan strategy, etc. allows nowadays the manufacturing of geometrically accurate parts with high strength. [11] The high thermal gradients and high solidification rates in the SLM process lead to a fine columnar dendritic solidification with microsegregation. Rapid local heating and cooling introduce significant stresses in accordance with the temperature gradient mechanism (TGM). [12] Recent results of Bertsch et al. [13] showed that these stresses and strains contribute strongly to the formation of dislocations. Mainly due to the high dislocation density, networks are formed. These dislocation cells typically overlap the microsegregations. Dendritic segregations and dislocation cells are known to be beneficial for the mechanical properties. [1][2][3]5] The main strengthening mechanisms of the austenitic steel 316L are solid solution and Hall-Petch strengthening. In the case of SLM-processed 316L, additional strengthening by the dendritic substructure has to be considered. These substructures consist of segregated elements and entangled dislocations contributing to the strength of the material. [1,14,15] One model to understand the fundamentals of strengthening by cellular dislocation structures was established by Mughrabi. [16][17][18] The socalled composite model describes the stress distribution in the soft cell and hard wall regions and enables the calculation of the total strengthening effect by a modified Taylor equation, using a geometric constant for the heterogeneous composite, α het , depending on the wall thickness and cell diameter. [18] It was also found by Blum and Reppich, [19,20] for cellular dislocation networks developed under static creep loads, that the