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doi:10.14311/APP.2017.13.0029Acta Polytechnica CTU Proceedings
13:29–34, 2017 © Czech Technical University in Prague, 2017
available online at http://ojs.cvut.cz/ojs/index.php/app
SYNTHESIZED ENRICHMENT FUNCTIONS FOR EXTENDEDFINITE ELEMENT
ANALYSES WITH FULLY RESOLVED
MICROSTRUCTURE
Martin Doškářa,∗, Jan Nováka, Jan Zemana,b
a Faculty of Civil Engineering, Czech Technical University in
Prague, Thákurova 7/2077, 166 29 Prague 6, CzechRepublic
b The Institute of Information Theory and Automation, Academy of
Sciences of the Czech Republic,Pod Vodárenskou věží 4, 182 08
Prague 8, Czech Republic
∗ corresponding author: [email protected]
Abstract. Inspired by the first order numerical homogenization,
we present a method for extractingcontinuous fluctuation fields
from the Wang tile based compression of a material microstructure.
Thefluctuation fields are then used as enrichment basis in Extended
Finite Element Method (XFEM) toreduce number of unknowns in
problems with fully resolved microstructural geometry synthesized
bymeans of the tiling concept. In addition, the XFEM basis
functions are taken as reduced modes ofa detailed discretization in
order to circumvent the need for non-standard numerical
quadratures. Themethodology is illustrated with a scalar
steady-state problem.
Keywords: Wang tiling, microstructure synthesis,
microstructure-informed enrichment functions,extended finite
element method.
1. IntroductionAll materials exhibit heterogeneous
microstructure atcertain level of detail. Besides the physical
propertiesof microstructural constituents, the overall responseis
also dictated by their spatial arrangement. Withthe advance of
numerical methods and computationalpower, there is an emphasis on
devising approachesthat take the microstructural characteristics
into ac-count and propagate knowledge of material composi-tion into
upper-scale models.
In our contribution, we focus on problems in whichthe underlying
microstructural geometry is explicitlyknown. We consider problems
where the character-istic length of the microstructure is
comparable tothe dimension of an upper-scale model; hence,
thenested numerical homogenization, such as the FE2method [1], is
not applicable because the underlyingassumption of the separation
of scales is violated [2,and references therein].
This work supplements our previous results regard-ing efficient
modelling of materials with stochasticheterogeneous microstructure,
e.g., [3, 4]. The mi-crostructural geometry of a macro-scale
model—aswell as its finite element discretization—is
synthesizedusing the Wang tiling concept, recalled in Section
2.Here, we present a method to extract dominant re-sponses of a
compressed microstructure to prescribedmacroscopic loading. We
reuse the extracted responsesto synthesize a
microstructure-informed enrichmentbasis in order to accelerate the
upper scale calculations.The numerical scheme, outlined in Section
4, combineseXtended Finite Element Framework (XFEM) [5, 6,and
references therein], used for definition of local
basis functions, with the reduced order modellingapproach [7],
allowing for utilization of standard fi-nite element procedures.
Finally, Section 5 illustratesthe methodology with a
two-dimensional problem ofsteady-state thermal conduction in an
L-shaped do-main.
2. Wang tiling conceptMicrostructure of random heterogeneous
materialsis usually represented by means of a periodic finite-size
model—appearing in the literature under variousnames such as
Statistically Optimal RepresentativeUnit Cell, Statistically
Similar Representative VolumeElement, or Statistically Equivalent
Periodic Unit Cell(SEPUC)—that resembles the material in terms
ofvarious spatial statistics. This setting is particularlysuitable
for the family of FE2 simulations,e.g., [1], inwhich it is often
accompanied with periodic boundaryconditions imposed at the
micro-scale level. How-ever, when used for microstructure
synthesis, this rep-resentation introduces unrealistic, spurious
periodiccorrelations.The formalism of Wang tiles represents a
compro-
mise between the amount of induced correlation andcomplexity of
a microstructure representation. In-stead of a single cell,
microstructural information iscompressed into a set of equi-sized
Wang tiles withpre-defined requirements on mutual compatibility.
Inthe abstract setting, the compatibility constraints
arerepresented by codes assigned to tile edges, illustratedwith
distinct colours in Figure 1. A realization of thecompressed
microstructure is then synthesized follow-ing a simple stochastic
algorithm: an empty grid of
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M. Doškář, J. Novák, J. Zeman Acta Polytechnica CTU
Proceedings
a desired size is sequentially filled with instances ofWang
tiles such that the adjacent tile edges are com-patible. At each
position, a tile is randomly chosenfrom a subset of tiles compliant
with previously placedtiles; hence, the algorithm generates
stochastic real-izations, providing that set of tiles is rich
enough suchthat multiple tiles are admissible at each assemblystep;
see Figure 1 for an illustration.
Figure 1. The compressed microstructural geome-try represented
with the set of Wang tiles (top) andan illustration of a step in
the tiling algorithm withpartially assembled microstructure
(bottom).
Procedures designed to compress a given microstruc-ture into a
SEPUC can be straightforwardly extendedto take into account
generalized periodicity occurringin the tiling concept, e.g., the
standard optimizationprocedure based on minimizing discrepancy in
thetwo-point probability function was used in [3]. Wealso adapted a
sample-based approach originated inComputer Graphics in order to
address the high com-putational cost of the optimization-based
design [4].Currently, a variety of material microstructures,
rang-ing from particulate media to complex foam-like
mi-crostructures, can be represented with the frameworkof Wang
tiling. Individual realizations of the mi-crostructure are then
generated in linear time withrespect to the required sample size,
which makes thetiling concept appealing for applications where
multi-ple microstructure samples are required, e.g., investi-gation
of the RVE size [8].
3. Synthesized enrichments fieldsThe idea of compressing
fluctuation fields using theWang tiling concept has been introduced
in Novák etal. [9], where the microstructural geometry of
individ-ual tiles was optimized with respect to (i)
meetingprescribed spatial statistics and (ii) minimizing trac-tion
discrepancies among congruent edges in an auxil-iary tiling.
However, the resulting synthesized stressfields exhibited
unavoidable discontinuities and theobjective function required
careful tuning of weightparameters because the two requirements
turned tobe hard to achieve simultaneously. In contrast, thepresent
method generates continuous fields of theprimal unknowns for any
existing microstructure com-pression.
We illustrate the methodology with the steady-stateheat
conduction problem, governed by
∇ · (−K(x) · ∇θ(x)) = 0 , x ∈ Ω , (1)
where θ denotes the unknown temperature field, K isa local heat
conductivity tensor and no heat sourcesare considered.
First, we assume the decomposition of θ into a fluc-tuation part
θ̃, caused by the presence of hetero-geneities, and a macroscopic
part controlled witha macroscopic temperature gradient H,
θ(x) = θ̃(x) + H · x , ∀x ∈ T(i),∀T(i) ∈ S, (2)
where T(i) denotes the domain of the i-th tile and S ={T(i), i =
1 . . . nT
}represent the set of nT available
tiles. Without loss of generality, each tile is assumedcentred,
i.e., T(i) = [−α, α]2, where 2α is the size ofthe tile edge.
In order to enforce continuity of the extracted fields,all tiles
are loaded with the prescribed macroscopicgradient H and solved
simultaneously. Providing thatthe tile geometries are discretized
with a compatibletriangulation—meaning that discretization of the
cor-responding tile edges is the same across all
tiles—thecontinuity is ensured by associating the correspondingedge
unknowns during the localization of an elementcontribution into the
conductivity matrix of the wholeset. The resulting system takes the
standard form
KS θ̃ = F (H) , (3)
where KS = AT(i)∈S KT(i) is the conductivity matrixand F (H) is
a H-dependent loading vector arisingfrom the weak form after
plugging Eq. (2) into Eq. (1).KS has block-diagonal structure
similar to primaldomain decomposition approaches.In addition, two
types of constraints are imposed
on the set system. First, we eliminate zero-energymodes of KS by
requirement
1|S|
∫Sθ̃(x) dx = 0 . (4)
The second constraint prevents the fluctuation field θ̃from
compensating for the loading induced through H .
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Inspired in numerical homogenization, e.g. [2], weintroduce the
second constraint enforcing
1|Ω|
∫Ω∇θ̃(x) dx = 0 (5)
in a chosen domain Ω loaded analogously to Eq. (2).Using Green’s
first identity, Eq. (5) can be recast intoa boundary integral∫
∂Ωθ̃(x)n(x) dS = 0 , (6)
where n(x) denotes the outer normal of the boundary.In
particular, we consider three mutually exclusivetypes of the second
constraint:(K) The first type prescribes zero temperature
fluctu-ations at tile boundaries,
θ̃|∂T(i) = 0 , ∀i = 1 . . . nT , (7)
where ∂T(i) stands for the boundary of the i-th tile.(P) In the
second type, the requirement (6) is posedtile-wise, i.e.,∫
∂T(i)θ̃(x)n(x) dS = 0 , ∀i = 1 . . . nT . (8)
(S) The last type imposes Eq. (6) over the whole
set,∫∂Sθ̃(x)n(x) dS = 0 , (9)
where ∂S ={∂T(i), i = 1 . . . nT
}.
Note that (K) corresponds directly to Kinematic Uni-form
Boundary Conditions used in numerical homog-enization, while (P)
and (S) mimic Periodic and Stat-ically Uniform Boundary Conditions,
respectively.Instead of Eq. (3), the final fluctuations θ̃
follows
from KS CTI CTIICI 0 0CII 0 0
θ̃λIλII
=F(H)00
, (10)where CI and CII matrices represent the
discretizedversions of Eq. (4) and one of Eqs. (7), (8), or (9),
re-spectively, and λ• stands for the corresponding vectorof
Lagrange multipliers.While CII straightforwardly eliminates edge
un-
knowns for the constraint type (K), constructing con-tributions
of individual tile separately and localizingthem into CII leads to
an ill-posed problem for types(P) and (S) From Eq. (6), it clearly
follows that if twoopposite sides of a tile are required to be
compatible—hence they feature the same trace of θ̃—the
corre-sponding component of ∇θ̃ average vanishes and sodoes the
tile contribution to the relevant row in CII.In addition, the
ill-posedness also stems from the rep-etition of edge code pairs
within the tile set (swappingthe order of codes changes only the
sign of the edgecontribution to Eq. (5)). In certain cases, this
caneven result in zero matrix CII for the least
restrictiveconstraint (S), in which tile contributions are
summedtogether.
One way to treat the singularity of CII is to performSingular
Value Decomposition on the constraint andtake into account only the
non-zero singular values;however, such a procedure is sensitive to
numericalprecision. Thanks to the simple structure of the
con-straint, the regular part of the constraint can be di-rectly
established as a projection of the original matrixCII. First, all
nc combinations of edge codes pertinentto either horizontal or
vertical edges are identified andenumerated. Next, an empty matrix
P ∈ R2nT ×nc , for(P) type of the constraint, or P ∈ R2×nc , for
(S) type,is created and populated with 1 (or −1) if the
tilecontains an enumerated pair of codes (or a pair in theinverse
order). Odd and even rows of the matrix cor-respond to vertical and
horizontal edges, respectively.If P remains empty for (S), CII
constraint is discardedentirely. Otherwise, the non-singular
constraint ma-trix CII, replacing CII in Eq. (10), is obtained
froma projection CII = PTCII.The outlined strategy allows to define
one enrich-
ment field θ̃ for a prescribed H and the selected type ofthe
second constraint. For the linear problem consid-ered in this work,
two mutually orthonormal loadingcases H =
{1, 0}T and H = {0, 1}T cover all possible
load cases. Combined with three types of CII, we cangenerate up
to six enrichment fields. Note that un-like the nested numerical
homogenization, where thechoice of boundary conditions is based on
their suit-ability in capturing effects of a surrounding medium,we
combine different types of CII to control cardinalityof the set of
compressed fluctuations.
Figure 2. A compressed fluctuation field obtained byprescribing
(S) variant of the second constraint andsetting H = {1, 0}T.
4. Numerical strategyThe fields introduced above are employed as
enrich-ments in a upper-scale model whose microstructuralgeometry
is assembled by means of tiling from the setdepicted in Figure
1.
Assume a upper-scale problem governed by the samedifferential
equation as in Eq. (1), valid in a upper-scale domain Ω and
accompanied by boundary condi-tions
θ(x) = θ̂(x) x ∈ Γθ 6= ∅ , (11)(−K(x)∇θ(x)) · n(x) = q̂(x) x ∈
Γq , (12)
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M. Doškář, J. Novák, J. Zeman Acta Polytechnica CTU
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where θ̂ and q̂ are the given temperature and normalheat flux
profiles, respectively, prescribed at parts Γθand Γq of the domain
boundary ∂Ω. An approximatenumerical solution arises from the weak
form of theproblem
Find θ ∈ V such that a(θ, ϑ) = b(ϑ), ∀ϑ ∈ V0 . (13)
and substitutes for the analytical solution that is usu-ally
intractable. In Eq. (13), a(θ, ϑ) and b(ϑ) denotethe bilinear and
linear form pertinent to Eq. (1); Vand V0 stand for the space of
admissible temperaturefields.
Quality of the approximate solution is governed bysuitability of
a finite-dimensional subspace Vc ⊂ V inwhich the solution is sought
for. In particular, domaindiscretization must accurately resolve
all geometricaldetails in the standard Finite Element (FE)
setting.This requirement leads to very fine meshes in applica-tions
where microstructural geometry of the domainis involved.
Besides local mesh refinements, the approximationspace can be
enhanced by incorporating prior knowl-edge of local character of
the solution. Concretely, inthe Extended Finite Element framework
[5, 6], theapproximate solution θc ∈ Vc takes the form
θc(x) =nc∑i=1
Ni(x) θi +nc∑i=1
ne∑j=1
Ni(x)ψj(x) θji , (14)
where the first sum contains the standard finite el-ement shape
functions Ni(x) and the second termadds ne enrichment functions ψj
for each discretiza-tion node; θi denotes the regular Degree Of
Freedom(DOF) associated with finite-element mesh node xi,θji are
the additional DOFs.In traditional XFEM, only patches of the
domain
are usually enriched with ψj , suited for one geomet-rical
feature. Typically, the enrichment providesasymptotic solution near
a crack tip or introducesstrong/weak discontinuities [6]. Here, we
add globalenrichments that capture collective response of a
ma-terial microstructure. The original shape functionsNi(x) model
the macroscopic response of the do-main, while products Ni(x)ψj(x)
cover the fluctua-tions caused by material heterogeneity. A similar
ideawas introduced by Strouboulis et al. [10], who used nu-merical
“handbook” functions for assemblies of closelypacked inclusions, or
Plews and Duarte [11]. However,both approaches solve local boundary
value problemsdefined on subdomains first and subsequently run
theanalysis of the whole domain. In contrast, we pre-compute the
fluctuations purely “off-line” at the levelof microstructure
compression. i.e., without any in-formation of the domain geometry
or loading, andconstruct the enrichments as an assembly of the
tile-defined fluctuation fields.
In our approach, the upper scale discretizationis constructed
irrespectively of the underlying mi-crostructural geometry of Ω.
Hence, the approxima-tion basis functions in the form of Eq. (14)
togetherwith fluctuations in material parameters due to thepresence
of microstructural geometry preclude efficientuse of standard
numerical procedures for evaluationof the bi-linear form in Eq.
(13).
In order to circumvent this drawback, we constructanother, finer
domain discretization space Vf , assem-bled from the tile
discretization used in the off-linephase for extracting fluctuation
fields. The shapefunctions Ni(x), defined at the coarser
discretization,are projected onto the fine mesh; enrichments
ψj(x)are already defined within the fine discretization
byconstruction. Consequently, Eq. (14) can be under-stood as a
definition of reduced modes for the finediscretization.
Let matrix Φ comprises individual reduced modes asits columns,
computed as an element-wise product ofthe projectedNi(x) and ψj(x)
following Eq. (14). Therange of Φ thus defines a subspace of Vf
correspondingto Vc. Instead of solving the large,
fine-discretizationsystem Kfθf = Ff , we restrict the
fine-discretizationunknowns θf via
θf = Φ a , (15)
where a denotes the vector of unknown coefficientspertinent to
the reduced modes. The final algebraicsystem then takes the
form
ΦTKfΦa = ΦTFf . (16)
5. ResultsWe considered the material microstructure of
mono-disperse elliptical inclusions, shown in Figure 1. Bothphases
were assumed isotropic, with the inclusionmaterial being more
conductive (K(x) = 100 I) thanthe matrix phase (K(x) = 1 I). Six
fluctuation fieldsin total, discretized with linear triangular
elements,were extracted, see Figure 2.
The microstructure was superimposed to an upper-scale problem
represented by an L-shaped domainwith uniform temperature profiles
prescribed at thebottom and right-hand side edges. The initial
coarsediscretization of the domain is depicted in Figure 3.The
linear Lagrange basis functions were assumedat the coarse level,
whilst the fine space comprisedthe quadratic Lagrange approximation
arising fromthe product of linear coarse shape functions and
theenrichments.The solution θXFEM of Eq. (16) was compared
against Direct Numerical Simulation (DNS) θDNS,which was taken
as the reference solution. A sequenceof five uniformly refined
coarse discretizations, thefirst one shown in Figure 3, was
investigated. Theproximity of the reference (DNS) and XFEM
solutions
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θ̂ = 20
10 tx
10 ty
θ̂ = 010 tx
10 ty
Figure 3. A scheme of the problem definition. Theedge lengths tx
and ty of the tiles were set as tx =ty = 6. All quantities are in
consistent units.
was quantified via relative errors
�L2 =
∥∥θDNS − θXFEM∥∥L2
‖θDNS‖L2and (17)
�H1 =
∥∥θDNS − θXFEM∥∥H1
‖θDNS‖H1, (18)
where
‖u‖2L2 =∫
Ωu2(x) dx and (19)
‖u‖2H1 =∫
Ωu2(x) +∇u(x) · ∇u(x) dx . (20)
Mean and standard deviations of the errors computedfor five
coarse discretizations and six different tilingrealizations are
given in Figure 4.
10!4 10!3 10!2
XFEM/DNS DOFs
10!2
10!1
0 0
L2H1
Figure 4. Convergence of L2 and H1 errors withincreasing number
of DOFs in the coarse discretiza-tion.
6. ConclusionsWe have presented a method for extracting
continuousfluctuation fields from a microstructure compressed
by means of Wang tiles. We have also demonstratedutilization of
these fields as enrichments in XFEM.In order to avoid non-standard
quadratures, XFEMbasis functions were projected onto a
discretizationarising from assembly of the tile discretization
usedfor computing the fluctuation fields.
The proposed methodology was applied to a steady-state heat
conduction problem defined in an L-shapeddomain with
microstructural geometry provided bythe tiling concept. Only 1.6 %
of the original degreesof freedom were sufficient to obtain 2 %
relative errorcompared to DNS.
On the other hand, the reduction in DOFs acceler-ates only the
solution of Eq. (16). For more significanttime savings, a low-rank
additional approximation ofKf , e.g. using the idea of
hyper-reduction [12], hasto be introduced and is the focus of our
current work.We have also restricted ourself to the first-order
de-composition, Eq. (2); higher order expansion of themacroscopic
loading can be considered to further en-rich the approximation
space.
AcknowledgementsM. Doškář and J. Novák acknowledge the
endowmentof the Ministry of Industry and Trade of the CzechRepublic
under the project No. FV10202. In addi-tion, M. Doškář was
supported by the Grant Agencyof the Czech Technical University in
Prague, project No.SGS17/042/OHK1/1T/11 “Numerical Methods for
Mod-eling Uncertainties in Civil Engineering”.
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Acta Polytechnica CTU Proceedings 13:29–34, 20171 Introduction2
Wang tiling concept3 Synthesized enrichments fields4 Numerical
strategy5 Results6 ConclusionsAcknowledgementsReferences