tao wu theoretical modeling and experimental...
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Theoretical Modeling and Experimental Characterization of Stress Development in Parts Manufactured Through Large Area Maskless Photopolymerization
Tao Wu, Suman Das
Woodruff School of Mechanical Engineering, Georgia Institute of Technology, Atlanta, GA 30318
Abstract
This paper aims at investigating the evolution of stresses in parts manufactured through large area maskless photopolymerization (LAMP). A theoretical model was established to understand the curing process for LAMP and a finite element analysis was performed to model the dynamic evolution of stresses during the layer-by-layer fabrication process using Abaqus software. This model serves to suggest strategies for reducing stresses, part warpage, and crack development in parts made through LAMP.
Introduction Large Area Maskless Photopolymerization (LAMP) is a direct digital manufacturing technology that can build three-dimensional objects layer-by-layer with both high speed and fine feature resolution. A schematic of the LAMP process being developed by the direct digital manufacturing (DDM) laboratory at Georgia Tech is shown in Fig 1. The core part of LAMP system is the spatial light modulator (SLM), which is a digital micro-mirror device (DMD). It is an optical chip with more than 1.3 million mirrors which can be turned on or off according to the color (white or black) of pixels in the corresponding bitmap image. A UV source is used to project light onto the DMD and expose the photocurable ceramic-loaded liquid resin according to the input image. The optical imaging head, with the UV lamp and DMD inside, moves in a serpentine path and raster scans the building area. Using this exposure mechanism, LAMP can realize massively parallel scanning lithography and its patterning speed is much higher than the traditional stereolithography in which only one single beam is used for scanning. In industry, extremely complex interior cooling passages of turbine airfoils are usually produced by investment casting, which typically involves the creation of over thousand tools needed for fabricating the cores, patterns, mold, and setters. The DDM group in Georgia Tech is using the LAMP process to produce the integral ceramic cored molds directly. In this way, the production rate, casting yield and costs can be improved dramatically when compared to the conventional investment casting procedures. Therefore, direct digital manufacturing using LAMP is a kind of technology that disrupts the current state-of-the-art investment casting process, not only in the manufacturing of airfoils but also in many other applications involved complex components.
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Thithrough by inducresults feach curthe devethis papalleviati
1. Cur
Thimechanimechanimodulusmodeledseveral kmore coinstantanconversi
Where E
Figu
s paper maithe LAMP
cing defectsfrom the difrrently expoelopment ofper is to ining residual
re Dependenis model dical propertical properts is stronglyd by Dillmakinetic and
onvenient α-neous isotrion degree α
Eα0 and Eα
ure 1. Schem
inly focusesprocess. Re
s such as disfferent degreosed layer wf residual stnvestigate th
stresses and
nt Modulusdescribes thties. For thties are isot
y cure depenan and Sefeviscoelastic
-mixing ruleropic resin α:
α1 are the Y
E
matic illustr
s on studyinesidual strestortion, cracees of shrin
will tend to ptress is stronhe mechanid improving
Th
s he relation he ceramic tropic and t
ndent, influeneris [1]. Hoc parametere model [2, modulus, d
Young’s m
0 (1 )E Eα= −
ration of Ge
ng the evoluss can have acks and dela
nkage in seqproduce flexngly influenisms of strg part quality
heoretical m
between thparticle lo
the Poissonnced by the
owever, thisrs which nee3] is used h
denoted E0
moduli of un
0 1E Eα αα+ +
orgia Tech’
ution of intea significanamination. Tquentially exxure of the lanced by proress evolutioy.
model
he conversiaded resin
n’s ratio (ν)kinetic-visc
s rigorous med extensivehere to get t, is expres
ncured (α=0
(1 )(γα α+ −
’s LAMP m
rnal stresset effect on t
The residualxposed layerayers solidifcessing histon so as to
ion degree composite is assumedcoelastic intmodel requie experimenthe cure depsed explici
0) and full
1 0( )E Eα α−
machine
s in a part bthe quality ol stress in LArs. The contfied previoutory. The obo infer stra
(α) of resiused in L
d constant. teractions suires the evantal data. Thpendent moditly as a fu
ly cured (α
being built of the parts AMP parts traction of usly. Thus, bjective of ategies for
in and its AMP, the The resin
uccessfully aluation of herefore, a dulus. The unction of
(1)
α=1) resin,
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respectively. The parameter γ (-1<γ<1) is introduced to quantify the competing mechanisms between stress relaxation and chemical hardening [1]. Increasing γ will make the modulus increase more rapidly at a relatively low conversion degree. In this paper, a zero value of γ is used for the simulation.
The material used in LAMP is silica particles loaded resin composite. The effective bulk modulus of this composite can be derived according to the self-consistent method [4], shown in equation (2).
(2)
Where K0 and K1 are the bulk moduli of matrix (resin) and inhomogeneity (particle) respectively. ̅ is the effective shear modulus of composite and c1 is the concentration of particles loading. The particles can be considered rigid compared to resin, thus we obtain:
(3) ̅ can be expressed as a function of and the effective Poisson’s ratio ν, which is considered as constant here.
(4)
Substitute into equation (3), we obtain:
(5)
The relation between bulk modulus and Young’s modulus can be expressed as:
(6)
Make use of equations (5) and (6), we obtain the effective Young’s modulus of composite as a function of resin’s modulus E0, effective Poisson’s ratio ν and particles concentration c1.
(7)
It can be seen that the effective modulus is proportional to resin’s modulus. So, the effective modulus of the composite is also related to the conversion degree α of resin.
(8) Equation (8) is similar with (1), but here , ∝ , ∝ are moduli of the composite, not resin.
The experimental data obtained from tensile testing according to ASTM D638 is shown in Table 1.
1 1 00
1
( )(3 4 )3 4
c K K KK KK
μμ
− += +
+
0 1
1
3 43(1 )K cK
cμ+
=−
3 (1 2 )2(1 )K νμ
ν−
=+
01 1
11 3 3
K Kc cν
ν ν+
=+ − +
00,
3(1 2 ) 3(1 2 )EEK K
ν ν= =
− −
01 1
11 3 3
E Ec cν
ν ν+
=+ − +
0 1 1 0(1 ) (1 )( )E E E E Eα α α αα α γα α= − + + − −
750
Properties Value ∝ (MPa) 0.829 ∝ (MPa) 829
ν 0.437 Table 1. Mechanical properties of acrylic-based composite
Here the modulus of uncured composite is chosen arbitrarily small due to the negligible stiffness. 2. Cure Dependent Shrinkage
This model proposes a theoretical relationship between the shrinkage strain and degree of conversion. The volumetric shrinkage occurring during LAMP process is related to the photopolymerization mechanism. The linkage of small monomer units produces large polymer chains and the corresponding intermolecular spacing is reduced from Van der Waals distance (~104Å) to covalent bond (C=C) lengths (~ 1 Å). This results in density changes and thus bulk contraction in the cured resin, which accumulates as the part is fabricated layer-by-layer. Thus, the volumetric shrinkage is a direct measure of the number of covalent bonds formed (degree of conversion) and an exact semi empirical relationship can be derived. Experimentally, the volume change per mole of acrylate groups (C=C) is 22.5cm3/mol [5] when acrylate monomer is polymerized. For a general case of multiacrylates with ceramic filler particles, the volumetric shrinkage value can be estimated through the following equation [6]:
( )(%) 22.5 (1 ) 100( ) 100i i i
mixi mi i
fV FLV M
χα ρχ
ΣΔ= × × − ×
Σ (9)
Where fi is the functionality of monomer (i), χi is mole fraction of monomer (i), Mmi is molecular weight of monomer (i) and ρmix is the density of the mixture.
For the material system used in LAMP, the values of above parameters are shown in Table 2.
Components fi Mmi ρ(g/cm3) v/o (%) w/o (%) χi ρmix(g/cm3)Hexanediol diacrylate, HDDA 2 226 1.02 3.4 18.6 .95 1.68 Ethoxylated Penta erythryitol
tetra acrylate, EPETA 4 528 1.12 31 2.3 .05
Filler (ceramic powder) 2.2 FL=55 72
Table 2. Data of the material system
Assuming a uniform strain contraction for all principle strain components and considering the volumetric strain to be smaller than 10 percent, the value of linear shrinkage strain is approximately one third of the volumetric shrinkage value. Thus the linear shrinkage strain εT can be expressed as:
( )1 22.5 (1 ) 1003 ( ) 100
i i iT mix
i mi i
f FLM
χε α ρχ
Σ= × × × − ×
Σ (10)
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around the bom-left holehere close to
value. Thus,above. Fig 8faster than through 1 thccumulate mon in the cas
oefficient.
he internal scal to each laresses shouldve position a
ations were the trailing eation of thesng the layer-rd size is 2mnal of the squ
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for each lay8. also showthe case of he two neighmore stress. se of IR 819
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a. Misesig 11. 3-D M
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s Stress D Modeling r
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ig 13. Comp
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758
F
Obhorizontdiagona(center) distortiothe holeboundardistortiokeep the
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Fig 14. Com
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on, horizonta should be a
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is paper preprocess. Sim
mena. For bond then beco
of hole and pration on str in which ho vertical alig
on, distributiund the holey from the franding the Lnation and diedge in the
work will be
mparison for
r both stressuch smaller ically (left) t. So we canal alignmenas uniform aally the horizrapidly in 7 y from each
esents theoremulations arth 4 layers aomes constapossibly cauress and distoles are aliggnment of hion of holese in a balan
free boundarLAMP proceimensional airfoil mold
e conducted
the evolutio
s and distortvalue than oare the wor
n conclude tnt of holes isas possible. zontal ones,layers and b
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Summaetical concepre conductedand 7 layersant. The mouses the inititortion are sgned horizonholes shoulds should be aced state in ries to avoidess and for pdiscrepancy
d built by LAto model th
ons of large
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ortion, the creasing the sen the spacinon of hole shze distortionble after aboers verticall
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e of the partsolution in th
ment (layer1
where holescases in wh
case with verstress conceng is small ahould be farn. Also, valuout 10 layerly.
model for thedifferent pris continues tntration occamination. Ttion of four value of strecing is smallso as to keehollow struc
work is a funreduce defeentrations as with most
he trailing ed
1) in four ca
are alignedhich holes arrtically alig
entration andand the arear away fromues of stressrs. So it is be
e layer-by-lint-through to increase urs at the bo
The effects ocases. It is fess and distol. To minim
ep the cure octure is bettndamental sects such as and distortio
serious defdge.
ases
d re aligned
gned holes d
as around m the free s and etter to
ayer
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on. The fects.
759
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