11.1 Volume fraction

A plot of the texture component with the annealing temperature for Al 8011 alloy showed a linear relationship for the cube and Goss component. Similarly from Figures 17 and 18, cube and RD cube were increasing linearly for Al 1145 alloy. The components S and Cu were in decreasing nature, and a deviation occurred at an annealing temperature of 300°C.

## 11.2 Al alloy

The evolution of Goss intensity was very negligible in Al 1145 alloy as compared to alloy 8011. The dominant texture component in the annealed microstructure,

that is, cube, was due to the higher nucleation rate of cube grains at the already existing cube bands.

Wu et al. [12] and 1998 have shown that ideal cube texture could lead to sharper yield locus under biaxial stretching and thereby sheet formability. Figure 18c and d was clear that the fraction of ideal cube was almost negligible compared to the fraction of cube spread in the microstructure. Apart from the cube component, it was observed that the fractions of RD- and ND-rotated cubes have been enhanced (ND-rotated cube {0 0 1}<130> and RD-rotated cube {1 3 0}<001> were deviated by about 18° along ND and RD, respectively, from the ideal cube orientation). A similar behaviour was observed for the alloy Al 1350.

#### 11.3 Pole figure

From Figure 17, the recalculated 111 pole figures with imposed orthotropic sample symmetry could be seen. Here, a gradual diminishing of deformation components can be seen with the simultaneous development of cube texture with annealing temperature for Al 8011 alloy. From Figure 18, it can be seen that the difference in elongation along the major and minor axes was significant which implied that the anisotropy was higher in these rolled Al 8011 alloy sheets. Figures 17 and 18 represent the recalculated 111 pole figures from the ODF with imposed orthotropic sample symmetry for Al 1145 and Al 1350, respectively. It can be seen that significant deformations were retained up to 250°C beyond which cube texture became prominent with increasing annealing temperature.

11.4 ODF

51

Figure 18.

11.5 α-Fibre and β-fibre

Aluminium and Its Interlinking Properties DOI: http://dx.doi.org/10.5772/intechopen.86553

The intensity of Cu and S components in the φ2—45° and φ2—65° sections, respectively, has decreased with temperature. The φ2—0° section showed qualitatively the strengthening of cube and Goss intensities as a function of temperature.

111 pole figures of annealed samples of Al 8011: (a) 200°C, (b) 250°C, (c) 300°C, (d) 350°C [30, 32–35].

From the α-fibre, it can be inferred that the Goss components increased with simultaneous fall in the orientation densities (f(g)) of deformation components as can be seen from the β-fibre (Figure 17) for Al 8011 alloy. The cube orientation

Figure 18 showed that the formability in the present set of samples improved with increasing annealing temperature. The presence of precipitates could significantly suppress the cube fraction in the microstructure in turn retaining the defor-

The alpha-fibre plots followed a similar trend in all the cases, particularly at starting (ф = 0°) and end (ф = 90°) locations. As there is an increased annealing temperature, the intensity of alpha-fibre also increases. The trend was different at ф<sup>1</sup> = 35°, where a peak change is observed at all alpha-fibre components. In general,

a deep change (intensity of alpha-fibre component) was observed at other annealing temperatures except 300°C. This was due to the equilibrium between precipitation and recrystallization at that temperature. Hence alpha-fibre

showed a strong scattering along the RD in the φ2—0° section.

mation components at lower temperatures.

Aluminium and Its Interlinking Properties DOI: http://dx.doi.org/10.5772/intechopen.86553

Figure 18. 111 pole figures of annealed samples of Al 8011: (a) 200°C, (b) 250°C, (c) 300°C, (d) 350°C [30, 32–35].

#### 11.4 ODF

that is, cube, was due to the higher nucleation rate of cube grains at the already

Wu et al. [12] and 1998 have shown that ideal cube texture could lead to sharper yield locus under biaxial stretching and thereby sheet formability. Figure 18c and d was clear that the fraction of ideal cube was almost negligible compared to the fraction of cube spread in the microstructure. Apart from the cube component, it was observed that the fractions of RD- and ND-rotated cubes have been enhanced (ND-rotated cube {0 0 1}<130> and RD-rotated cube {1 3 0}<001> were deviated by about 18° along ND and RD, respectively, from the ideal cube orientation). A similar behaviour was observed for the alloy Al 1350.

From Figure 17, the recalculated 111 pole figures with imposed orthotropic sample symmetry could be seen. Here, a gradual diminishing of deformation components can be seen with the simultaneous development of cube texture with annealing temperature for Al 8011 alloy. From Figure 18, it can be seen that the difference in elongation along the major and minor axes was significant which implied that the anisotropy was higher in these rolled Al 8011 alloy sheets. Figures 17 and 18 represent the recalculated 111 pole figures from the ODF with imposed orthotropic sample symmetry for Al 1145 and Al 1350, respectively. It can be seen that significant deformations were retained up to 250°C beyond which cube texture became prominent with increasing annealing

Texture analysis based on ODF for the annealed samples of Al 1350: (a) alpha-fibre, (b) beta-fibre, (c) phi,

existing cube bands.

Aluminium Alloys and Composites

11.3 Pole figure

temperature.

Figure 17.

50

(d) volume fraction of texture components.

The intensity of Cu and S components in the φ2—45° and φ2—65° sections, respectively, has decreased with temperature. The φ2—0° section showed qualitatively the strengthening of cube and Goss intensities as a function of temperature.
