Prakt. Met. Sonderband 46 (2014) 337
of SEM and R35.25
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the influence foo
cause higher — 7 NN -
same crack nm 73 12
n field during TO =
1 super alloy
0 0.25 um.
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vitates of the
cause a very
able for good
9 Fig. 1: specimen geometry and configuration of stage-I-crack (crack side B), RO! with
1} slip planes magnification (magnification reference Polaroid 545) and loading direction (left hand side)
e slip system and outline of implementation of investigation steps (right hand side)
r notch was
‘ormation can
a cross about 2.2 CRACK INITIATION AND CRACK GROWTH
upport crack The specimen was loaded ex situ with a stress ratio of R = -0.1 and a stress range of 600
MPa. Replica were taken every 2000 cycles to observe the crack growth rates and to
detect when the crack tips reach the ROIs. A da/dN-curve was collected according to
ASTM E647-13 by 7-point smoothening (Fig. 2).
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module. The 54k
her than the _ |
ne rearrange Y * ++ N
e dislocation *1,00E-06 5 $ sok 695
igh the crack
*
e exactly the 3
ns alignment
st achievable 1,00E-07 de
Zeiss Sigma 2 OK, [MPavm] 4
La maximum Fig. 2: da/dN-curve: the cycle numbers for image collection were marked
at the stress
ess gradient 2.3 MEASUREMENT IMAGES
ie ROI with a
The measurement images (Fig. 3b) were achieved from 54000 up to 78000 load cycles
region of an with exactly the same SEM beam and detector parameters as the reference images.
was in good Special attention was dedicated to the exact repositioning of the specimen in the in situ
tensile module and the SEM to avoid translation and rotation artefacts in the image
correlation analysis.