46  Prakt. Met. Sonderband 38 (2006) 
at the edge of the deformed grain and not inside the grains. Additionally, “normal” large 4c). 
angle grain boundaries are more susceptible to recrystallization than twin boundaries. The recr 
recrystallized grains do not remain isolated, but form very soon closed networks resulting sites 
in the well-known necklace structure. Moreover, no preferred growth direction of these 
grains can be found neither due to the texture of the initial deformed grain nor due to the 
direction of the strain (see inverse pole figures in Fig. 3 c,d). 
Fig 
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in 
wit 
The 
300 pm incre 
[001] [0011 10011 foo 001? grair 
N ‘7 aver 
- remc 
grow 
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and 
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GL oC nn. : 00 101 
Fig. 3: Inverse pole figure map of the recrystallized (a) and deformed (b) fraction as 
function of the strain, with the strain values atop of the image. The black areas represent 
the respective second fraction. Inverse pole figures of the recrystallized (c) as well as the 
deformed grains (d). 
One of the mechanisms for recrystallization is the transformation of subgrain boundaries 
into large angle grain boundaries. The example in Fig. 4 demonstrates that in many grains 
the majority of small angle misorientations in the range between 1°-5° with misorientation 
angles greater than 2° (Fig. 4a) are located rather close to the grain boundaries, whereas 
a lower value of 1° (Fig. 4b) results in an approximately statistical scatter across the whole 
grains. Since misorientations are caused by strains (i.e. caused by dislocations), their 
height and distribution should be a rough measure for the local dislocation densities. 3.2 
In the deformed fraction a subgrain structure close to the high angle grain boundaries can 
be observed, albeit not with completely closed boundaries, but with grain sizes of Once 
approximately the size of the recrystallized grains (see structures marked by arrows in Fig. recn 
oe 0.92