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8/2/2019 Crystal Basics
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I. Basics of Crystal Plasticity
Plastic deformation
deformation which remains after load is removed
atomic rearrangements (change of neighbours)
Plastic deformation of crystals preserves lattice structure.
shearing of lattice planes against each other (slip)
plastic displacements are quantized in terms of multiple lattice vectors
At low temperatures / high stresses: Deformation of crystals occurs exclusively
by slip of lattice planes
Slip system is characterized by:
slip plane normal slip direction
slip vector (a lattice vector in the slip direction)
often: slip planes are most densely packed lattice planes
slip directions are most densely packed lattice directions
n
r
sr
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On surface: slip can be seen in the form of slip steps along lines where
the slip planes intersect the surface
Example: Slip lines on the surface
of a polycrystalline Ni specimen. Slip
traces from two slip systems are visible
A
F
F
No shear stress if slip direction or slip plane normal are perpendicular
to the tensile axis
Maximum shear stress if slip plane and slip direction are under 45o
to the tensile axis.In single crystals: Slip starts on slip system with
highest resolved shear stress
Driving force for slip: Tensile stress
leads to resolved shear stress in slip system
coscosR =
nr
sr
AF/=R
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How do lattice planes slip?
Not: breaking all bonds simultaneously (this would imply a perfectly strong, but
also perfectly brittle material!)
Instead: slip involves motion of defects: Dislocations
Side view of the motion of an edge dislocation
Dislocation is characterized by slip vector (Burgers vector) and slip plane
Burgers vector: when you make a closed circuit around a dislocation,
there is a mismatch of one lattice vector. This is the Burgers vector
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Type of dislocation depends on orientation of the dislocation line
with respect to the Burgers vector.
Screw dislocation: line is parallel to Burgers vector
Edge dislocation: line is perpendicular to Burgers vector
Some top views of dislocations: (blue = atoms above slip plane
red = atoms below slip plane)
an edge dislocation a screw dislocation
A dislocation loop
Dislocation = boundary ofslipped area
(follow a vertical row of blue atoms
to see the displacement
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Stress required to move dislocations:
1) Stress required to displace dislocation by one Burgers vector (stress to
break bonds): Peierls stress
2) Stress required to move dislocation across obstacles
A dislocation pinned
by a localized obstacle
Introduction of dislocation obstacles: solution/precipitation hardening
3) Stress required to overcome dislocation interactions: work hardening
Dislocations: Internal stresses and dislocation interactions
Dislocations create lattice distorsions and stress and strain fields
Typically 5% of work done during deformation is stored as elastic energy
of the dislocation stress fields
Elastic energy per unit length of dislocation line:(Consequence: only dislocations with smallest Burgers vectors occur)
Stress fields decay like where ris the vertical distance
from the dislocation
2
L ~ GbE
rGb /~
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Stress fields lead to dislocation interactions
Estimating the magnitude of dislocation interactions:
Dislocation density
Mean dislocation spacing
Characteristic interaction stress
areaunit
pointsonintersectiofnumber
eunit volum
linesndislocatiooflength
==
/1=d
GbdGb ~/~
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Rate of deformation by slip (shearing rate ):
proportional to
dislocation density
Burgers vector modulus b
dislocation velocity v
Orowans equation:
Dislocation velocity depends on stress, temperature and presence
of dislocation obstacles
Often: thermally activated process with activation energy
Empirical relation for dislocation glide velocity:
whereNG = stress exponent for glide (typically ~10), T temperature
bvdt
d
=
dt
d
E
=kT
E
Gvv G
NG
exp0
Dislocation climb:
Dislocation can move perpendicular to its glide plane only if matter
is added or removed: climb motion
By climbing, dislocations can move past obstacles
Climb is possible if diffusion processes lead to transport of matter
Usually: vacancy diffusion
Rate of climb depends on concentration and diffusivity of
lattice vacancies : proportional to self-diffusion rate
climb velocity:
whereNC= stress exponent for climb (typically ~3),ESD activation energy
for self-diffusion (formation + migration energies of vacancies)
=kT
E
Gvv SD
NC
exp0
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Diffusional creep:
No motion of dislocations, deformation due to matter transport by
point-defect diffusion
Stress exponent is small (1 or 2)
Often grain boundary diffusion: activation energy is small)
Creep rate
=kT
E
G
D
ND
exp0
&&
Different deformation mechanisms are characterized by different
activation energies and stress exponents
Determination of stress exponents:
Experiments at constant
temperature but varying stress
Plot log(deformation rate)
vs. log(stress)
Determination of activation energies:
Experiments at constant stress
but varying temperature
Plot log(deformation rate)
vs 1/temperature
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Different deformation mechanisms operate in general simultaneously
But: Usually one mechanism (the fastest) prevails
Boundaries between different deformation
mechanisms: Equate respective rates
For rates in the form
we get for the boundary between two mechanisms i and j
hence
choose semi-logarithmic representation of stress vs. temperature
=kT
E
Gdt
d iN
i
i
i
exp0
&
=
kT
E
GkT
E
G
j
N
j
i
N
i
ji
expexp 00
&&
kT
EE
GNN
ji
ji
j
i
=
+
ln)(ln0
0
&
&
Result: Deformation mechanism maps (Example: Ni-base superalloy)