usnccm-xi identification of fracture properties 11th us...
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USNCCM-XI11th US National Congress on Computational Mechanics
MinneapolisJuly 25-29, 2011
M. Alfano, G. Lubineau, A. MoussawiComposite and Heterogeneous Materials Analysis and Simulations,
King Abdullah University of Science and TechnologyKingdom of Saudi Arabia
G. H. PaulinoDepartment of Civil and Environmental Engineering,
University of Illinois at Urbana-Champaign, USA
Minneapolis, July 25th 2011
Identification of fracture properties for a cohesive model using digital
image correlation
M. Alfano et al. (http://cohmas.kaust.edu.sa) 2
1. Introduction and motivation
2. Objective
3. Proposed approach
4. Algorithm and implementation of the inverse procedure
5. Target applications and experimental set-up (current status)
6. Follow-up work
Outline-
3
Introduction and motivations (1/4)Mechanical testing
as produced
θ ≈ 83o
laser treated
20o
δ
griparea
1.5 mm
25 mm
45 mm
40 mm
100 mm
100 mm
P, P
laser treated
grit-blasted
Alfano M, Furgiuele F, Lubineau G, Paulino GH. Role of laser surface preparation on damage and decohesion of Al/epoxy joints. Submitted for Journal publication.
4
Introduction and motivations (2/4)PPR based cohesive model
Park K, Paulino GH, Roesler JR. A unified potential-based cohesive model of mixed-mode fracture. Journal of the Mechanics and Physics of Solids. 2009;57(6):891-908.
Γn = −φn
α
m
m
m =α (α− 1)λ2
n
1− αλ2n
δn =φn
σmaxαλn (1− λn)
α−1 α
m+ 1
·
α
mλn + 1
m−1
non-dimensional exponent;
energy constant;
final crack opening width;
T (∆n) =∂Ψ∂∆n
=
= Γnδn
m
1− ∆n
δn
α mα + ∆n
δn
m−1− α
1− ∆n
δn
α−1 mα + ∆n
δn
m
Ψ(∆n) = φn + Γn
1− ∆n
δn
α m
α+
∆n
δn
m
unknown properties to be identifiedX = φn,σmax,λn,α : unknown cohesive properties;
5
Introduction and motivations (3/4)PPR for mode I fracture
Park K, Paulino GH, Roesler JR. A unified potential-based cohesive model of mixed-mode fracture. Journal of the Mechanics and Physics of Solids. 2009;57(6):891-908.
Cohesive energy (N/mm)
Coh
esiv
e st
reng
th (M
Pa)
(b)
2.8 3 3.2 3.4 3.6 3.8 4 4.2
10
20
30
40
50
60
70
80
0.1
0.2
0.3
0.4
0.5
0.6
0.7
0.8
0.9
Φ
6
Introduction and motivations (4/4)Identification of bond toughness using the CZM
Φ = U(δ)EXP − U(δ)FE 2
U(δ) =
δi
δi−1
P (δ)dδ = (δi − δi−1)×P (δi) + P (δi−1)
2
Alfano M, Furgiuele F, Lubineau G, Paulino GH. Identification of mode-I cohesive zone parameters of Al / epoxy T-peel joints with laser treated substrates. Submitted for Journal publication.
φn = 0.7÷ 0.9 N/mm
σmax = 0.5÷ 5 MPa
φn = 3.2÷ 3.8 N/mm
σmax = 20÷ 85 MPa
The response function is not affected by shape factor and
slope indicator
P
δ
Exp
FEA
7
Remarks and objective of the work-
A global response is often obtained from experiments, however, it may have low sensitivity to certain cohesive properties.
The uniqueness of the obtained cohesive zone model is not guaranteed.
Although the cohesive models obtained using global data can yield satisfactory predictive capabilities in FEA simulations of fracture, the development of an alternative procedure is needed, e.g. to determine cohesive strength.
A solution may be provided by the original combination of experimental full-field measurements techniques and inverse problems.
Gain AL, Carroll J, Paulino GH, Lambros J. A hybrid experimental / numerical technique to extract cohesive fracture properties for mode-I fracture of quasi-brittle materials. International Journal of Fracture. 2011;169:113-131.Shen B, Paulino GH. Direct Extraction of Cohesive Fracture Properties from Digital Image Correlation: A Hybrid Inverse Technique. Experimental Mechanics. 2011;51(2):143-161.
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Forward versus inverse problemForward problem
Ωσ : δ dΩ−
Γext
Text · δ∆u dΓext +
−
Γcoh
Tcoh · δ∆u dΓcoh = 0
Principle of virtual work Ω : specimen domainΓext : external boundaryΓcoh : cohesive surfaces∆u : cohesive surfaces opening displacementσ : stress tensor : strain tensor
Forward problem P
CMOD
Step 1
1
u
Kb =
ΩBTEB dΩ
Kcoh =
Γcoh
NT ∂T
∂∆uN dΓcoh
Fext =
Γext
TextdΓext
(Kb +Kc(u,X))u = Fext
P-CMOD
+T
∆u
9
P
CMOD
Step 2
Step 3
Step 1
crack growth
ROI
P-CMOD
Inverse problem(optimization)
T
∆u
X = φn ,σmax ,α ,λn
ωi (X) =1
(Umax,i)2
nn
j=1
[uexp − u (X)]2j
X = argminX∈RM
Π =m
i=1
ωi (X)
m : available measurement instants (load levels)nn : nodal displacements in the ROI
Forward versus inverse problemInverse problem (objective of the work)
u(X) = K−1b F
ext(uexp ;X)
Fext
(uexp ;X) = Fext −Kc(uexp ;X)uexp
Optimization algorithm?
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Exploration algorithm based on the mechanism of natural selection and genetics: the strongest individuals (chromosomes) in a population survive and generate offsprings.
Genetic algorithmFundamentals concepts
A chromosome represents a generic solution of the problem, in our context a set of cohesive fracture parameters (X):
X Φn σmax λn α
1. Random generation of the initial population (individuals X) satisfying suitable restraint conditions (e.g. fracture energy must not be negative);
Basic steps of the GA
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2. The chromosomes are evaluated, using some measures of fitness. We defined the following objective function (or cost function):
Genetic algorithmBasic steps of the algorithm
ωi (X) =1
(Umax,i)2
nn
j=1
[uexp − u (X)]2j
X = argminX∈RM
Π =m
i=1
ωi (X)
m : available measurement instants (load levels)nn : nodal displacements in the ROI
3. Individuals for reproduction are firstly chosen based on their fitness
4. and some of them are processed by means of genetic operators (crossover and mutation) to create a new populations
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Crossover (type 1)
X1 Φn σmax λn α X2 Φn σmax λn α
X3 Φn σmax λn α X4 Φn σmax λn α
Crossover (type 2)
X3 = a ·X1 + (1− a) ·X2
X4 = (1− a) ·X1 + a ·X2a ∈ [0, 1]
5. New chromosomes, called offspring, are formed by merging two chromosomes from current generation
Genetic algorithmBasic steps of the algorithm
13
X1 Φn σmax λn α
X2 Φn σ’max λn α
σmax = σmax + r ·∆σmax
r ∈ [−1, 1] ,∆σmax = cost.
5. New chromosomes are also formed by modifying a chromosome using a mutation operator
Genetic algorithmBasic steps of the algorithm
6. The newly created population replace the old one and the process restarts.
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Genetic algorithmFundamentals concepts
Initialsolutions
Start Population P(t)chromosomes
(φn ,σmax ,λn ,α)1(φn ,σmax ,λn ,α)2(φn ,σmax ,λn ,α)3
(φn ,σmax ,λn ,α)n
.
.
.
chromosomesOffsprings C(t)
crossover
mutation
CC(t)
CM(t)
Solution candidates
(fitness computation)
Newpopulation
Terminating condition?
Yes
Bestsolution
Stop
No
t0
t0+1
(φn ,σmax ,λn ,α)1(φn ,σmax ,λn ,α)2
(φn ,σmax ,λn ,α)12(φn ,σmax ,λn ,α)21
(φn ,σmax ,λn ,α)j
(φn ,σmax ,λn ,α)j
selection evaluation
Abaqus/Matlab interaction by means of Linux shell scripts
readoutput file
solve non-linearfracture problem
+
writeinput file
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Target applications and experimental set-upcurrent status
Hot press 15T/300°C
Specialized cutting devices
Ultrasonic Dispersion
propagation in CNT (carbon nanaotube) and fiberreinforced hybrid composites. Wichmann et al. [8]have reported a decrease in the Mode I interlaminarfracture toughness of DWCNT and glass fiber rein-forced epoxy matrix composites, and pointed somedifficulties during the tests caused by the obstructedtracking of the crack tip in the opaque resin usingthe conventional visual crack tracking during DCBtesting. In our previous studies we have reportedsome indirect delamination resistance improvementin a nanotube/fiber reinforced system [9]. The aimof this research is to directly characterize the effectof carbon nanotube filling on the interlaminarmechanical properties of fiber reinforced compos-ites through standard DCB tests.
2. Experimental2.1. Materials
FM-20 epoxy laminating resin was used (P+MPolimerkémia Kft., Hungary) with T-16 curingagent (P+M Polimerkémia Kft., Hungary) asmatrix. The recommended mixing weight ratio was100:20, the resin had a curing treatment of 4 h at60°C.Baytubes® BT150 HP (Bayer, Germany) multi-walled carbon nanotubes (MWCNTs) were used asfiller in one portion of the matrix (Figure 1). Thenanotubes have been produced in a CVD based cat-alytic process resulting in an average outer diame-ter between 13–16 nm, length above 1 µm andcarbon purity above 99% according to the manu-facturer. The carbon nanotubes have been mixed tothe epoxy component of the resin using a three rollmill, four pass-throughs have been carried out to
achieve uniform dispersion and appropriate particlesize (<10 µm).Zoltek PX35FBUD0300 unidirectional carbon fab-ric (Zoltek Ltd., Hungary) has been used as fiberreinforcement in the composites. The fabric con-sisted of 50k rovings, and had a surface weight of300 g/m2.
2.2. Composite preparation
To characterize the effect of the nanotube filling ofthe matrix on the properties of carbon fiber rein-forced composites one carbon fiber/epoxy laminateand four carbon nanotube/carbon fiber/epoxy lami-nates with 0.1, 0.3, 0.5, and 1 weight% nanotubefilling have been produced under the same circum-stances.The laminates have been produced by hand lamina-tion of 10 plies of carbon fabric impregnated withthe resin, the fiber orientation of all laminae hasbeen 0°. A 50 µm thick PET film has been used as adelamination initiator insert in the center plane(between the 5th and 6th lamina) of the laminates.Both sides of the film have been coated with mouldrelease agent to minimize adhesion between thefilm and the matrix of the composite. To avoidtrapped in air bubbles, the laminate has been rolledafter every two plies.To achieve uniform thickness and fiber content thelaminate has been pressed for 12 hours under30 kN at room temperature. The uniform thicknessof all of the laminates has been achieved by using a4 mm thick steel plate placed as a spreader next tothe laminates in the press. The fiber contents were49.2±1.1, 51.9±2.8, 51.7±3.2, 51.9±2.7, and
146
Romhány and Szebényi – eXPRESS Polymer Letters Vol.3, No.3 (2009) 145–151
Figure 1. SEM micrographs of the MWCNT aggregates (a) and MWCNTs (b) used (raw materials)
MWCNT Dispersion
Material processing - DCB with metal and composites substrates
Composite laminates
High resolution
CCD camera(PixelFly)
QM100 long distance microscope(QUESTAR)
INSTRON Testing machine
High intensityLed spotlight In-house developed DIC algorithm
Full-field experimental measurements
(http://cohmas.kaust.edu.sa)