# Deformation Behaviour of Cold-Rolled Ni/CNT Nanocomposites
## 3 Results and Discussion
### Texture Evolution  
The texture evolution is investigated for the Ni matrix and Ni/CNTs nanocomposites at three strain values (0.11, 0.36, and 0.69). The orientation distribution functions (ODFs) and [111] PFs of these samples can be observed in Figure 8 for the Euler angle \(\varphi_{2}=0^{\circ}\), \(15^{\circ}\), \(30^{\circ}\), \(45^{\circ}\), \(65^{\circ}\), and \(75^{\circ}\).  
For face-centered cubic (CFC) structures, the rolling texture components are Copper [112] <111>, S [231] <346>, Brass [110]<112>, and Goss [110]<001> that are indicated in the figure; these texture components were also analysed in some authors' works in order to characterize deformed samples [13; 33]. For texture evolution, the initial grain orientation is an important parameter, and both samples have differences in their crystallographic orientation prior to deformation, as previously analysed in Figure 2. For the strain of 0.11, the two samples (Ni matrix and Ni/CNTs nanocomposites) are mostly characterized by random orientation. However, it becomes possible to determine some orientations with higher intensity. For the Ni matrix, the highest intensity occurs for the Cube and Brass rolling texture components, while for the nanocomposite, the Cube component has the highest intensity. With increasing strain up to 0.36, the Ni matrix develops texture components mainly composed of Copper and Goss, and starts to create other textures such as bb, A1, and C.  
In contrast, the cold-rolled nanocomposite with the same strain mainly exhibits the Copper and Taylor texture components. For the higher strain (0.69), the texture shows similarities between Ni and Ni/CNTs samples. This is most evident in the {111} pole figure's components, where the highest intensities are the Goss, Copper, and Taylor for both samples, with A and C being more significant for the Ni matrix, and Cube for nanocomposites. The Ni sample reveals that from 0.36, the shear texture components (bb, A1, and C) also occur beside the rolling texture components. [PERSON] et al. [41] revealed that for cold-rolled samples, the development of shear texture for inhomogeneous rolling due to the deformation geometry and friction between the rolls and sheet is possible. The main shear textures observed in FCC metals consist mainly of {001}<110>, {111}<112>, and {111}<110> orientations, which are in agreement to some extent in this study.  
These results show that the Ni and Ni/CNTs exhibit different textures for the 0.11 and 0.36 strains and become similar for higher strains. This behaviour can also contribute to the differences observed between the hardness values of the cold-rolled nanocomposites and Ni matrix at the same deformations.  
The different stages of microstructural evolution during the cold-rolling can give rise to these differences. Figure 9 shows the IPF maps and Kernel misorientation maps of the  
Figure 8: Orientation distribution functions (ODFs) and [111]pole figures (PF) of the deformed Ni and Ni/CNT samples. The points present in ODFs are present with corresponding components.  
Ni and Ni/CNT samples deformed with strains of 0.36 and 0.69. It is possible to observe in this figure that the Ni matrix presents micro sheet bands for the strain of 0.36. For strain 0.69, these bands and regions with domains (sub-grains) are more evident. For the nanocomposites cold-rolled up to a strain of 0.36, the dislocation reorganization concerning the sintered sample is visible, and the dislocation density is lower than that of the Ni sample. For the strain of 0.69, the microstructure is similar to the Ni sample, making it possible to identify the micro shear bands. These observations are being referred to by other authors [14] regarding the microstructural evolution during cold-rolling.