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Application of Asymptotic Expansion Homogenization to Atomic Scale
N Chandra and S Namilae
Department of Mechanical EngineeringFAMU-FSU College of Engineering
Florida State University
Why link atoms and continuum ?
“Nanotechnology”
Atomic details (structural and Material) have profound influence on properties
-Thermomechanical-Physical, electrical, magnetic
However computational problems-100 nm cube of Si ~ billion atoms
Macroscopic phenomenon effected by atomic scale details
Fracture Crack tip
Plasticity Dislocation
Grain boundaries
“Materials by design”
Creep /SP
Problems in Atomic scale domain
Grain boundaries play a important role in the strengthening and deformation of metallic materials.
Some problems involving grain boundaries :
Grain Boundary Structure Grain boundary Energy Grain Boundary Sliding Effect of Impurity atoms
Equilibrium Grain Boundary Structures
[110]3 and [110]11 are low energy boundaries, [001]5 and [110]9 are high energy boundaries
[110]3 (1,1,1) [001]5(2,1,0)
[110]9(2,21) [110]11(1,1,3)
GB
GB
GB
GB
Experimental Results1
1 Proceeding Symposium on grain boundary structure and related phenomenon, 1986 p789
Grain Boundary Energy Computation
Calculation
GBE = (Eatoms in GB configuration) – N Eeq(of single atom)
0
1
2
3
0 20 40 60 80 120 140 160 180
100
(b)
(
111)
(113
)
(
112)
Egb
,eV
/A2
Egb
,eV
/A2
S5
(55)
S(44) S27
(552)
S9
()
S27(5)
S()
S
(8)
S(2)
S(225)S7(4)
S4
(5)
S4
(556)
S9(22)
S
(2)
S4
(44)
S(2)
S(0)
S(00)
Grain Boundary Sliding Simulation
4 5 o
Y ’
X ’
Y
X
Z [1 1 0 ]
GB
Generation of crystal for simulation of sliding. Free boundary conditions in X and Y directions, periodic boundary condition in Z direction.
X’
Y’
A state of shear stress is applied
L
NMMM
O
QPPP
0 0
0 0
0 0 0 T = 450K
Simulation cell contains about 14000 to 15000 atoms
Grain boundaries studied: 3(1 1 1), 9(2 2 1), 11 ( 1 1 3 ), 17 (3 3 4 ), 43 (5 5 6 ) and 51 (5 5 1)
Sliding Results
0 20 40 60 80 100 120 140
0
0.5
1
1.5
2
2.5
3
3.5
4
4.5
0
0.5
1
1.5
2
2.5
3
3.5
4
4.5
E10
(eV
/A)
Slid
ing
Dis
tanc
e(A
)
GB
x2
2
74
922
555
4556
Fig.6 Extent of sliding and Grain boundary energy Vs misorientation angle
Sliding Distance
Grain Boundary energy
EG
BX
10-2
(eV
/A2)
Grain boundary sliding is more in the boundary, which has higher grain boundary energy
Monzen et al1 observed a similar variation of energy and tendency to slide by measuring nanometer scale sliding in copper
Monzen, R; Futakuchi, M; Suzuki, T Scr. Met. Mater., 32, No. 8, pp. 1277, (1995)Monzen, R; Sumi, Y Phil. Mag. A, 70, No. 5, 805, (1994)Monzen, R; Sumi, Y; Kitagawa, K; Mori, T Acta Met. Mater. 38, No. 12, 2553 (1990)
1
Reversing the direction of sliding changes the magnitude of sliding
Mg Segregation in Al Grain Boundaries
Y distance from GB (A)
E10
(eV
/A)
0 5 10 15 20
2.86
2.88
2.9
2.92
2.94
2.96
2.98
3
GB
X
-22
E for Pure Al = 2.82 10 (eV/A )GB
x-2 2
1 2 S9 (2 2 )STGB
Mg Atom
Y
Position 1
Position 2
Y distance from GB (A)0 2 4 6 8 10 12 14
0.75
0.755
0.76
0.765
0.77
0.775
0.78
E10
(eV
/A)
GB
x
22
EGB For Pure Al =0.65 x 10-2 (eV/A2)
Mg Atom
Y
S ( ) STGB
Segregation of Mg atoms to particular locations in grain boundary is based on size effect and hydrostatic pressure
Variation of grain boundary energy in presence of Mg atom
Hydrostatic Stress and Segregation Energy
Grain boundary energy and segregation are influenced by changes in coordination of atoms at grain boundary
Simulation results also indicate that there is an increase In grain boundary sliding when Mg atoms are present
Effect of Mg on sliding
(r/r )
Num
ber
ofA
tom
s
0 1 2 30
2
4
6
8
10
12
e (r/r )
Num
ber
ofA
tom
s
0 1 20
2
4
6
8
10
e(r/r )
Num
ber
ofA
tom
s
0 1 2 30
2
4
6
8
10
e
Distribution of atoms around impurity atom in 9 STGB
Problems in macroscopic domain influenced by atomic scale
MD provides useful insights into phenomenon like grain boundary sliding
Problems in real materials have thousands of grains in different orientations
Multiscale continuum atomic methods required
A possible approach is to use Asymptotic Expansion Homogenization theory with strong math basis, as a tool to link the atomic scale to predict the macroscopic behavior
Sinclair (1975) Hoagland et.al (1976)
Mullins (1982)
Gumbusch et.al. (1991)
Tadmor et.al. (1996), Shenoy et.al. (1999)
Flexible Border Technique
Finite element Atomistic method
FE-At method
Quasicontinuum method
Continuum-Atomics linking
Rafii Tabor (1998)
Broughton et.al. (2000)
Lidorkis et. al. (2001)
Friesecke and James
Three scale model
Coarse grained molecular dynamics
Handshaking methods -CLS
Multiscale scheme
Continuum-Atomics linking
Other efforts: CZM based, description of continuum in atomic Regions, lipid membranes etc
Homogenization methods for Heterogeneous Materials
Heterogeneous Materials e.g. composites, porous materials
Two natural scales, scale of second phase (micro) and scale of overall structure (macro)
Computationally expensive to model the whole structure including fibers etc
Asymptotic Expansion Homogenization (AEH)
Overall Structure
Microstructure
Schematic of macro and micro scales
AEH idea
+uy=
y
ue ux
e x
= +
Overall problem decoupled into Micro Y scale problem andMacro X scale problem
AEH literature Functional analysis
Bensoussan et.al. (1978), Sanchez Palencia (1980) Elasticity well established
Kikuchi et. al. (1990) Adaptive mesh refinement Hollister et. al. (1991) Biomechanics Application Ghosh et. al. (1996),(2001) AEH combined with
VCFEM Buannic et. al. (2000) Beam theory with AEH
Inelastic Problems Fish et.al. (2000) Plasticity Chung et.al. (2001) Viscoplasticty
Transport Problems in Porous media
Formulation Let the material consist of two scales, (1) a micro Y
scale described by atoms interacting through a potential and (2)a macro X scale described by continuum constitutive relations.
Periodic Y scale can consist of inhomogeneities like dislocations impurity atoms etc
Y scale is Scales related through Field equations for overall material given by
X
_ _
0 on (Equilibrium)
on (Constitutive Eqn)
on
Boundary Conditions
on and on u t
fx
C e
ue
x
u u n t
xy
Contd
xy
0 1 22, , , ..u u x y u x y u x y
The functions u(i) (x,y) are Y periodic in variable y. and are independent of the scaling parameter .
The basic concept in AEH is to expand the primary variables as an asymptotic series. Using the expansion for displacement u
From the definition of the scaling parameter, for any g(x,y)
, , ,1g x y g x y g x y
x yx
Hierarchical Equations Strain can be expanded in an asymptotic expansion
0 0 1 1 21
...u u u u u
e uy x y x y
Substituting in equilibrium equation , constitutive equation and separating the coefficients of the powers of three hierarchical equations are obtained as shown below.
0
0 1 0
1 2 0 1
0
0
0
uC
y y
u u uC C
y x y x y
u u u uC C f
y x y x x y
Micro equation
Macro equation
Microscale EquationUsing the following transformation
0
1 uu
x
Micro equation can be solved as
0
. 0u
Cy y x
Y Y
v CC dY v dYy y y
In Variational form
corrector term in macro scale due to microscale perturbations. series of vectors
Microscale Equation• The Y scale here is composed of atoms interacting through an interatomic potential.
• If we consider a finite element mesh refined to atomic scale in the Y region then, would denote the atomic level stiffness matrix • W is the total strain energy density of the Y scale and q dente the displacements of individual atoms. • Micro equation can be solved as
2
q q
W
2
T locB Cq q
W
CY
at atomic level (6xN)BTCloc
q Atomic displacements
Cloc Local elastic constants determined from MD
Macroscale equationGiven by
apply the mean operator on this equation, by virtue of Y-periodicity of u(2) equation reduces to
1 2 0 1
0u u u u
C C fy x y x x y
0
0H uC f
x x
C H is the homogenized elasticity matrix for the overall region given by
1.H
YC dy
Y y
(A)
Equation (A) solved by FEM with appropriate BC gives solution corrected for atomic scale effects
Local Elastic Constants
Based on Kluge et al J. of App. Phy. (1990)
Knowing local strain and local stress in a small region V of MDSimulation local elastic constants
0i
loc
F
dVC
e
system of N interacting atoms in a parallelepiped whose edges are described by vectors a, b and c with H=(a,b,c)
Constant strain application H=Ho to H=Ho+ Ho
(Parinello –Rahman Variable cell MD)
Local Elastic constants
Local stress in small area defined as
, ,1 i j
ij ijij ij
g r r sUr r
r r
, , ( )
( )
i
i j ij i j
i
s r
g r r s s R s r s r
s r
volume , rij distance between ith and jth atoms,
U interatomic potential functionunit step function Dirac delta function Rij center of mass of particles i and j
This Method has been applied to grain boundaries using EAM and pair potentials
Computational Procedure Create an atomic model of microscopic Y
scale Use molecular dynamics to obtain the
material properties at various defects
such as GB, dislocations etc. Form the matrix and homogenized material properties
Make an FEM model of the overall (X scale) macroscopic structure and solve for it using the homogenized equations and atomic scale properties
Summary Incorporating atomic-scale effects in
determining the material behavior is important in a number of engineering applications.
Grain boundaries structure and deformation characteristics can be studied at atomic scale. Using Molecular Dynamics it has been shown that extent of grain boundary sliding is related to grain boundary energy
The formulation for AEH to link atomic to macro scales has been proposed with detailed derivation and implementation schemes.
Work is underway to implement the computational methodology.