three-dimensional full-field x-ray orientation microscopy · ebsd comparison on ti sample comparing...
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Three-dimensional Full-fieldX-ray Orientation Microscopy
Nicola Viganòa),b),c), W. Ludwiga),b), K.J. Batenburgc),d),e)
a) European Synchrotron Radiation Facility, Grenoble, Franceb) MATEIS, University INSA of Lyon, Francec) VisionLab, University of Antwerp, Belgiumd) Centrum Wiskunde & Informatica, Amsterdam, Netherlandse) Universiteit Leiden, Netherlands
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Wait! Local “orientation”, uhm... what?
● Crystallographic Orientation:“Relationship between the crystal coordinate system and a reference coordinate system”
● Plastic deformation can result in an orientation change:If the deformation doesn't change the intrinsic structure of the coordinate system, it simply results in a rotation of the said system.
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X
Y
Z
X
Y
Z
Rotation Axis
Reference System Rotated System
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OK, but what about deformation in grains?
● Disorientation map for a poly-crystal:
● Highest levels of deformation at the grain boundaries.
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Summary
● Introduction to Diffraction Contrast Tomography● Materials with Deformation● Our Model / Algorithm● Results● Conclusions
Nicola Viganò 4
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Intro to Diffraction Contrast Tomography 1/2
● Diffraction Contrast Tomography is a non-destructive characterization of 3D grain microstructure:● Assumes undeformed materials● Uses 2D monochromatic beams● Simultaneous acquisition of
transmitted and diffracted beam● Acquisition time: 0.1-10h● Performs a continuous rotation
over 360°, with steps of 0.05-0.1° (7200-3600 images)
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W. Ludwig et al., Rev. Sci. Instr. 2009
Synchrotron beam
ω
Detector Plane
Grain alignedfor Diffraction Diffraction Spot
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Intro to Diffraction Contrast Tomography 2/2
● Using the Friedel pairs it is possible to index the grains● Diffraction spots as projections● We use traditional oblique angles
tomography codes to reconstructthe shape of the grains
● This also works for multi-phase materials! a) Phase Contrast Tomography
b) DCT – Austenite
c) DCT – Ferrite
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P. Reischig et al., J. of Applied Crystal 2013
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Summary
● Introduction to Diffraction Contrast Tomography● Materials with Deformation● Our Model /Algorithm● Results● Conclusions
Nicola Viganò 7
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Reconstruction of (un)deformed material
● Given a 3D voxellated volume
● If not deformed:● All voxels have same projection angle● Simple (line) back-projection geometry● Can be handled as a 3D (oblique angle)
ART problem
● If deformed:● Vector (Tensor) field with 3 (9) unknowns
Or equivalently: scalar 6D (12D) problem● Complicated back-projection geometry● Needs another approach...
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x = x1
x2
x3
x =
x1
x2
x3
r1
r2
r3
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Reconstruction with plastic deformation
● Strain is a small perturbation compared to the plastic deformation of the crystal lattice. If we ignore it:● The reconstruction representation can be modelled either as a
3D vector field, or as a 6D scalar field● In the 3D vector field representation, each vector of each voxel is the
associated local average orientation● In the 6D scalar field representation, each intensity of each voxel is the
intensity of the “diffraction signal” for the given point of the extended representation
● The deformed projection geometryboth distorts the projected images,and spreads the signal over multipleimages, for each projection
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x =
x1
x2
x3
r1
r2
r3Diffraction Blob
ω+δ ω−δω
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Summary
● Introduction to Diffraction Contrast Tomography● Materials with Deformation● Our Model /Algorithm● Results● Conclusions
Nicola Viganò 10
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Insight of the 6D space
● 3D orientation-space volume that forms an ODF● 3D real-space a collection of one ODF for each voxel in
the volume
● In our implementation we do the inverse: 3D real-space volume are the voxels of a 3D orientation-space
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r3
r1
r2
o3
o1
o2
Single voxel ODF (Orientation Distribution Function)
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Projection geometry in standard DCT
● Undeformed grains will project to the same ωs
● Oblique angle reconstruction, using traditional algorithms (e.g. SIRT)
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Points in the orientation space
● Projection geometry of three different orientations:
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Tomography and Mathematical Optimization
● Tomography can be represented as:● To deal with indeterminacy and noise:● Our case is not so “easy”:● But we linearised it! (by unfolding-sampling the 6D
space, at the expense of multiplying the unknowns)● Assuming that only few of these orientations will be
active in each real-space voxel, we can look for a sparse solution (l1-min):
● Or, if the density is homogeneous in the grains, we could apply a “flatness” constrain on the 3D space representation:
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W x= y
minϕ(x)=‖W x− y‖22
minϕ(x)=‖W x− y‖22+λ‖x‖1 s . t . : x≥0
W ( x ) x= y
minϕ(x)=‖W x− y‖22+λ TV (S x ) s . t . : x≥0
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Details of the mathematics
● The implementation is pretty simple: there's a 1↔1 relationship between the mathematical objects and the functions of the algorithm:● is the projection of all the volumes to the detector
● is the back-projection of the images on the detector to the volumes
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W
W T
Summing all the contributions from the different volumes (orientations) for each ω, we obtain the images on the detector
ω
(o1 , o2 , o3)
(o1 ' , o2 ' , o3 ' )
ω
ω
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Summary
● Introduction to Diffraction Contrast Tomography● Materials with Deformation● Our Model /Algorithm● Results● Conclusions
Nicola Viganò 16
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EBSD Comparison on Ti sample
● Comparing a reconstruction using the 3D-DCT and 6D-DCT on the surface sensitivity, against EBSD measurements
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(a) EBSD – Full surface(b) 3D-DCT– ROI(c) EBSD – ROI(d) 6D-DCT– ROI
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Deformation in Ti sample
● Looking at the reconstructed deformation:
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NaCl sample (up to 1-2 deg of deformation)
● Surface: 3D-DCT 6D-DCT
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(1) Each indexed grain alone(2) With clustering and extension
EBSD
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Real Data (up to 1-2 deg spread)
● Surface: 3D-DCT 6D-DCT
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(1) Each indexed grain alone(2) With clustering and extension
EBSD
Why are those regions missing, and what can we do about it?
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Cluster reconstructions 1/2
● Can we use the 6D algorithm to index grains?● What if we simply tried reconstructing from the raw detector
images taken from an arbitrary bounding box in the 6D-space?● Let's use the indexed grains from a cluster to define the
6D bounding box:
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Sum of all the omegas from one of the blobs defined by the 6D bounding box, when projected to the detector
A [2 2 2] reflection at:θ = 6.21°η = 112.112°Δω = 6.7° (67 images)
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Cluster reconstructions 1/2
● Can we use the 6D algorithm to index grains?● What if we simply tried reconstructing from the raw detector
images taken from an arbitrary bounding box in the 6D-space?● Let's use the indexed grains from a cluster to define the
6D bounding box:
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Cluster reconstructions 2/2
IGM KAM
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Intra-Granular Misorientation Kernel Average Misorientation
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Real Data (up to 1-2 deg spread)
● Surface: 3D-DCT 6D-DCT(1) 6D-DCT(2)
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(1) Each indexed grain alone(2) With clustering and extension
EBSD
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Summary
● Introduction to Diffraction Contrast Tomography● Materials with Deformation● Our Model /Algorithm● Results● Conclusions
Nicola Viganò 25
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Recap of the main ideas
● In this model we represent each voxel as a stack of discretized orientations, each representing the contribution of that voxel to a particular orientation.
● Allowing many orientations per each voxel, it blows up the number of unknowns
● By minimizing the l1-norm of the 6D representation, sparse solutions are prioritized, thereby improving the ability to reconstruct using far more unknowns than equations
● Sampling in the orientation domain is an essential topic
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Conclusions
● Real data shows very good improvements especially for those scenarios (surface sensitivity) where traditional DCT had more troubles.
● Can complement indexing techniques● Shows potential for further improvements and
extensions:● Use of Far-field information● Overcome spot/blob segmentation issues● Overcome overlap on experimental images
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