## 1 Introduction  
The use of continuous carbon fibre-reinforced polymer (CCFRP) parts in industrial applications offers enormous potential to significantly reduce future products' consumption and CO\({}_{2}\) emissions economically and effectively [1]. CCFRP parts are characterised by their low weight-to-strength ratio and high mechanical tensile properties along the fibre direction. By using continuous fibres, the mechanical properties of fibre-reinforced parts can be increased along the load path [2]. Additive manufacturing processes offer a promising approach for the tool-less and time-efficient production of CCFRP parts with a high degree of individualisation and shape complexity. Material extrusion (MEX), such as fused layer modelling (FLM) or ARBURG plastic free-forming (APF), is well established in the literature for the additive manufacturing of CCFRP parts [3, 4, 5, 6, 7, 8, 9, 10]. Another category of processes for CCFRP parts is vast photopolymerisation (VPP) [11, 12, 13]. CCFRP parts produced by these processes (MEX and VPP), however, do not optimally meet the quality requirements for the matrix. Due to the nature of these processes, support structures are required, which have to be removed and disposed of after production. This results in the time- and cost-effective disposal and post-processing steps. In addition, the use of support structures limits the ability to create overhangs, cavities and undercuts, which results in limited part complexity. Furthermore,the breaking off of support structures can cause surface defects on the remaining part surfaces and, thus, lead to a more inhomogeneous appearance of the parts. Moreover, MEX and VPP do not allow for economic small-batch production. By contrast, the laser-sintering (LS) process represents a promising alternative for producing CCFRP parts. In a process comparison among MEX, VPP and LS with regard to the mechanical and thermal properties, as well as the long-term stability of the polymer parts produced, the LS process proves to be particularly advantageous, since the LS process enables the production of robust functional parts in injection moulding quality [14; 15]. According to [14], the Young's modulus of laser-sintered specimens is higher than the values determined for the Young's modulus of injection-moulded specimens, which is caused by a higher degree of crystallinity of the molecular structure of the semi-crystalline thermoplastics. The tensile strength was almost identical to that of the injection-moulded specimens. Other advantages of the LS process are the absence of support structures and the associated greater design freedom. In the LS process, the unsintered powder acts as a support structure, eliminating the need for time-consuming and costly post-processing steps [16]. By realising undercuts, cavities and overhangs, LS can produce near net-shape functional parts with high complexity in a single process step. Due to the ability to compactly position parts vertically and horizontally in the powder bed, the LS process allows for the economical production of small batches [14; 17]. Compared to FLM parts, LS parts have up to three times less anisotropy, higher dimensional accuracy and less surface roughness [14; 17; 18]. The LS process, thus, produces polymer parts with promising basic properties (matrix) for CCFRP parts. However, no commercially available LS machines combine the advantages of the LS process with the advantages of continuous fibres. Challenges to integrating continuous fibres in the LS process arise, particularly in the complex temperature control and the repetitive application movement of the recoater for each layer. To combine the process-specific advantages of the LS process as well as the promising part properties with the advantages of continuous carbon fibres, the technical feasibility (i.e., the layered integration of continuous fibre rovings into laser-sintered parts made of PA12) was demonstrated in [19; 20].