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    Numerical Simulation with Comsol Multiphysics of Crystallization

    Kinetics of Semi-Crystalline Polymer during Cooling: Application to

    Injection Moulding Process.

    N. Brahmia*, 1

    , P. Bourgin1, M. Boutaous

    *, 1, D. Garcia

    2

    1Laboratoire de Recherche Pluridisciplinaire en Plasturgie LR2P . Site de plasturgie de lINSA de Lyon

    BP 807-01108 Bellignat. 2Ple Europen de Plasturgie. 2, rue P.M. Curie -01100 [email protected]

    Abstract: Thermoplastic polymers are

    frequently used in several industries. They

    represent the most important group of polymeric

    materials. During injection moulding process,

    the cooling phase including solidification is oftenthe most significant part of a manufacturing

    cycle. For semicrystalline polymers, where

    different crystal structures appear, the thermo

    mechanical histories play a very important role

    in the estimation of the final parts properties.

    During the cooling stage, the behavior of these

    polymers is very difficult to model because of

    the complication of the crystallization process

    which is coupled to heat transfer and material

    properties change. The aim of this work is the

    study of the coupling phenomena between the

    crystallization and the thermal kinetics in the

    polymer injection moulding process, by usingComsol multiphysics software.

    Keywords: Injection moulding, semicrystalline

    polymer, crystallization kinetics, thermal

    properties, heat transfer

    1. Introduction

    Injection moulding is one of the most widely

    used processes in the polymer processing

    industry. The computer simulation of the process

    is an essential tool to predict the final properties

    of the part. For this calculation the knowledge ofrheological and thermomechanical material

    characteristics is of great importance. To

    understand the crystallization process of

    semicrystalline thermoplastics, during the

    injection moulding process, it is necessary to

    take into account the kinetics of crystallization

    and to consider the temperature and

    crystallization dependency of all the

    thermophysical properties of the material. All

    these variables parameters make the simulation

    more complicated. Generally, the simulations of

    injection process, consider isothermal or isobar

    case. In this work we have used Comsol

    multiphysics software to study the coupling

    between heat transfer and crystallization kinetics

    during the solidification of a semicrystalline

    polymer, such as polypropylene. First, thepolymer studied was precisely characterized and

    the crystallization kinetics was defined, using

    isothermal and no-isothermal DSC experiments.

    The results are compared to some data find in the

    literature, and then the influence of several

    parameters are computed and commented.

    2. Experimental section

    In this study, the polymer used is an injection

    moulding grade of a semicrystalline polymer

    which is polypropylene. Before startingsimulation, several characterizations of the

    material such as, viscosity, thermal conductivity,

    heat capacity and specific volume must be

    determined.

    2.1 Thermal properties

    To study heat transfer during crystallization

    of a polymer, it is necessary to take into account

    these thermal properties as a function of

    temperature and relative crystallinity (). Thisparameter, as shown byFulchiron [1], is defined

    by:

    =X

    Xc (1)

    WhereXc is the crystallinity depending on time,

    temperature and pressure and X, the

    crystallinity at the end of the solidification.The heat capacity is described using simple

    mixing rule between the solid state and the liquid

    state values weighted by the relative crystallinity

    :

    )()1()(),( TCTCTC apscpp += (2)

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    Where Cpsc and Cpa are the heat capacity of the

    solid state and the liquid state, respectively.

    The specific heat Cp in each phase of the polymerwas obtained by using calorimetric techniques

    (DSC), as shown in figure (1).

    For the polymer used in this work, Le Bot[2]

    proposed a linear temperature dependency versus

    temperature forCpsc and Cpa:

    1774.2+T3.4656)( =TC ap (3)

    1329.2+T8.3619)( =TC cps (4)

    With T in degree C and Cp in J.kg-1.K-1.

    1000

    2000

    3000

    4000

    5000

    6000

    7000

    8000

    20 40 60 80 100 120 140 160 180 200 220 240

    Temperature (C)

    Cp(J/kg.K

    )

    Figure 1: Evolution of heat capacity versus

    temperature.

    The thermal conductivity is also described by a

    mixing rule between solid state and liquid state

    as follows:

    )()(),( TTT asc += (5)

    0,14

    0,16

    0,18

    0,2

    0,22

    0,24

    20 40 60 80 100 120 140 160 180 200 220 240 260

    Temperature (C)

    Thermalconductivity(W/mK)

    Figure 2. Thermal conductivity versus temperature.

    The thermal conductivity was measured by an

    apparatus based on the transient line source

    method, which is ideally suited to polymers

    because measurements can be made quickly,

    before the onset of thermal degradation and no

    sample preparation is required [3].

    Figure (2) shows that the thermal conductivity of

    amorphous and semicrystalline phase, are

    temperature dependent and a linear fitting gives:

    0.1868+T10)./( -4=KmWsc (6)

    0.1394+T10)./( -4=KmWa (7)

    Where T in C and in W.m-1.K-1

    The density is the inverse of specific volume

    which is deduced from PVT diagrams: figure (3).

    It was evaluated as a weighted mean value of the

    pure amorphous and crystalline densities

    according to:

    )()1()(),,( TVTVPTV asc += (8)

    WhereaV is the specific volume of the

    amorphous sate of the material and Vsc is thespecific volume of the solid state.

    The PVT experimental results were obtained

    using a piston-type dilatometer (GNOMIX).

    A linear fit for specific volume for each phase is

    obtained as:

    2108.1103 3 += TVa (9)

    1.1055+T102.6 3=csV (10)

    Where T in C and V in m3.kg-1

    1

    1,05

    1,1

    1,15

    1,2

    1,25

    1,3

    1,35

    1,4

    1,45

    1,5

    50 100 150 200 250

    Temperature (C)

    Vsp(cm/g)

    P = 40MP

    P = 80MP

    P = 120MP

    P = 160MP

    Figure3: PVT diagram of PP.

    2.2 Crystallization Kinetic

    Crystallization is the process whereby an

    ordered structure is produced from a disorderedphase, usually a melt or solution. It represents a

    mix between nucleation and growth. When asemicrystalline polymer melt is cooled down into

    its crystallization temperature range,crystallization starts around discrete points callednuclei, and the crystal grow around nuclei to

    form what is referred to as spherulites. Once

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    all the spherulites meet their neighbors, thecrystallization process is complete.

    TheAvrami equation [4] has been widely used to

    describe polymer crystallization kinetics under

    isothermal conditions in the form:

    )(exp1)( ntkt = (11)

    Where n is the Avrami index, k is the Avrami

    isothermal crystallization rate constant.

    For non isothermal, isokinetic conditions, and

    assuming that the number of activated nuclei isconstant, Nakamura & al [5] developed the

    following equation fromAvrami theory [4]:

    )12()(exp1)(

    0

    nt

    dtTKt

    =

    WhereK(T) is the non-isothermal crystallizationrate constant.

    [ ]

    ==

    2

    1

    11 1)2(ln)()(

    tTkTK nn

    (13)

    Where

    2

    1t is the crystallization half time.

    2

    1

    1

    t

    indicates the overall rate of isothermal

    crystallization. By assuming that the number of

    nucleation sites is independent of temperatureand all sites are activated at the same time,Hoffman & al [6] developed the following

    expression to describe the overall rate ofcrystallization as a function of temperature:

    )14(exp)(

    exp11 *

    02

    1

    2

    1

    =

    TT

    K

    TTR

    U

    tt

    g

    Where T is the crystallization temperature, and

    021

    1

    t

    is a factor that includes all the terms which

    are independent of temperature. R is the

    universal gas constant, U* is the activation

    energy of the transport of crystallizing units

    across the phase boundary. T is the temperature

    under which such as transport ceases. Kg is the

    spherulite growth rate, TTT f = is the super

    cooling. According to Hoffman & al [6] the

    parameter U*

    and T can be assigneduniversal values 6284 J/mol.K and Tg -30K

    respectively. Tg is the glass transitiontemperature of the material.

    Differentiation of equation (12) leads todifferential form of Nakamura crystallization

    kinetics, which is more useful in modeling:

    [ ] )15())1(ln)1()(1

    n

    n

    TKnt

    =

    To determineK(T), different DSC measurements

    of isothermal and no isothermal crystallization

    were carried out, following a measurement

    protocol used previously byKoscher [7,8] and

    Juo [9] and. By fitting the experimental resultsusing equations (13) and (14), the parameters

    which permitted to determine K (T), were

    defined.

    3. Mathematical modeling

    Our aim is the analysis of a cooling of plate

    of semicrystalline polymer like in the cooling

    phase of injection moulding process. The systemis composed of a plate of polymer between two

    blocks of metal. The thickness of each block is

    of 30 mm, and of the plate is of 5mm. The width

    of the system is of about 50 mm (Figure 4).

    Figure 4: Model Geometry

    The general energy equation has been used todescribe the heat transfer in the system:

    )16(),(),(),( Qy

    TT

    yt

    TTCT p +

    =

    Where Qis a term source defined by:

    tHTQ

    = ),( (17)

    H is the total enthalpy released duringcrystallization process.

    The crystallization kinetics is given byNakamura equation as follows:

    n

    n

    TKnt

    1

    ))1ln(()1()(

    =

    (18)

    The Nakamura constant K (T) as proposed byKoscher[7, 8] is given by:

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    )19()(

    exp.)(

    exp

    )(3

    4)(

    *

    03

    1

    0

    =

    TTT

    K

    TTR

    U

    GTNTK

    f

    g

    The polymer tested by Koscher [7, 8] is an

    injection grade of isotactic polypropylene (EltexHV 252). The values of different parameters in

    K(T), are listed as follows:

    )1.15)(156.0(exp)(0 += TTTN f (20)

    G0 =21083.2 ,Kg=

    5105.5 (K2), U

    *= 6284

    J/mol.K, Tf =210C, T= -30C, H =90 10

    3

    J/kgand n =3.

    The material properties are defined by the

    general equations: (2), (5) and (8). Foramorphous and semicrystalline states the

    functions are listed in table 1:

    Cpa (, T) 212410.3 +T

    Cp sc (, T) 145168.10 +T

    a (, T) 189.01025.6 5 + T

    sc (, T) 31.01096.44 + T

    a (, T) )10773.6138.1(14 T+

    sc (, T) )10225.4077.1(14

    T+

    Table 1: Material properties of PP Eltex HV225

    4. Results and discussion

    4.1 Numerical validation of the model

    The objective of this section, is to ensure that

    Comsol multiphysics, solves correctly the

    problem, without any numerical errors. To do,

    we have opted to compare the results to those

    find in the literature. Due to the lake of data

    obtained in similar systems, the phenomenon

    was simplified. We have assumed that the

    system is cooled at constant cooling rate as in

    differential scanning calorimeter (DSC). The

    temperature is homogenously distributed in thepolymer, and decreases linearly:

    tVTT ref = 0 , where T0 represent the initial

    temperature of the system and Vref is the cooling

    rate value. TheNakamura crystallization kinetics

    was then solved using diffusion equation in

    general module of Comsol multiphysics

    software, and also by Matlab software using a

    finite differences scheme to discretize the

    equations.

    0

    0,1

    0,2

    0,3

    0,4

    0,5

    0,6

    0,7

    0,8

    0,9

    1

    90100110120130140150Temperature (C)

    Relativecrystallinity

    Simulation _Comsol

    Simulation_Matlab

    Figure 5: Evolution of relative crystallinity versustemperature: Comparison between Comsolmultiphysics and Matlab results for constant coolingrate (20C/min).

    For the same time step, the evolution of relative

    crystallinity was calculated for a cooling rate of20C/min. The result shows no difference

    between the two calculations and this had

    permitted us to validate our model numerically.

    4.2. Comparison with experimental results:

    The second validation of the model is made

    by comparison with experimental results from

    literature [8]. The system which was simplified

    before, as a simple case of DSC, was studied for

    constant and variable temperatures. The relative

    crystallinity was calculated for several constantvalues of cooling rates and temperatures.

    Comparison between our simulations results,

    Koscher & al [8] experimental results and their

    own calculations were carried out as shown in

    figure (6) and (7).

    For constant cooling rate, our results were more

    representative of the experimental results,

    compared to those calculated in the literature.

    This simulation permitted to improve the

    calculation of crystallization kinetics. In the

    figure (6), we can see that the Comsol

    simulations follow with a good agreement theexperimental results.

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    Figure 6: Comparison at constant cooling rate ofrelative crystallinity, between Comsol multiphysics

    results, Koscher measurements and Koscher

    calculations [8]

    Figure 7: Comparison of relative crystallinity for

    isothermal crystallization, between Comsolmultiphysics results, experimental measurements, and

    Koschercalculations [8]

    4.3 Simulation of effective cooling of the

    polymer plate: coupling of the heat and

    the crystallization equations

    In this section, we consider the system

    presented in figure (4). Some simplifications are

    assumed compared to the reel conditions in

    injection moulding process.

    - At initial time, the temperature of all the system(mould and polymer) is homogeneous T (t =0) =

    T0.

    - The cooling boundary conditions are imposed

    at the interface metal/polymer. Due to the plate

    dimensions, the heat transfer occurs only by

    conduction in one dimensional direction. The

    contact between the polymer and the mould is

    assumed to be perfect, without any thermal

    contact resistance.

    - In order to control the thermal kinetics in the

    polymer, we have assumed a linear decrease of

    the temperature at the interface metal/polymer asfollows:

    tVTT Cooling = 0 Where, Vcooling represents the cooling rate.

    Figure (8) shows the temperature evolution in

    the plate during the cooling process, at several

    locations. At the middle of the plate (at x= 0),

    due to the polymer thermal inertia, the

    temperature diminution begins after 60 sec. The

    variation which occurs between (725 and 895)

    sec corresponds to the crystallization of polymer.

    It is characterized by a plateau that appear at

    147C, and which corresponds to the release of

    latent heat of crystallization. After 920 sec the

    polymer is entirely solidified. The temperature

    evolution in the solid phase tends to an

    asymptotic form (the system tends to be

    thermally homogeneous).

    Figure 8: Temperature evolution at different positionsin the polymer plate, (Vcooling = 6C/min)

    Figure (9) presents the evolution of relative

    crystallinity as function of time at different

    locations in the plate. We notice that the polymerin the skin layer crystallizes more quickly then in

    the core layer. The total crystallization time is

    about 180sec.

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    0

    0,1

    0,2

    0,3

    0,4

    0,5

    0,6

    0,7

    0,8

    0,9

    1

    1,1

    300 400 500 600 700 800 900 1000

    Time (s)

    RelativeCrystllinity

    x = 0

    x = 2 mm

    x = 3.5 mm

    x = 4.8 mm

    Figure 9: Evolution of relative crystallinity atdifferent position of the plate, for Vcooling = 6C/min.

    4.3.1 Effect of the cooling rate

    In order to study the effect of the cooling rate

    on the material properties, several simulations

    with different boundary conditions are made.

    The effect of the thermal kinetics on the

    crystallization rate can be observed on the figure

    (10). As expected, we observe that the decrease

    in initial temperature leads to the acceleration of

    the crystallization and conversely.

    10

    30

    50

    70

    90

    110

    130

    150

    170

    190

    210

    0 100 200 300 400 500 600 700 800 900

    Time (s)

    Temperature(C)

    Vcooling = 12C/min

    V cooling= 30C/min

    Figure 10: Evolution of temperature at core polymerfor two different cooling rates

    The cooling time is reduced of about (242 sec)

    when we increase the VCooling of about 18C/min.

    Figure (11) shows the evolution of relative

    crystallinity at the polymer core for different

    cooling rates. It shows that the crystallization is

    shifted to the lower temperatures when the

    cooling rate is more important. A difference of

    10 C between the corresponding temperatures

    of the half-time transformation is observed, for

    two different thermal kinetics: VCooling = 12

    C/min and VCooling = 30C/min.

    -0,1

    0

    0,1

    0,2

    0,3

    0,4

    0,5

    0,6

    0,7

    0,8

    0,9

    1

    1,1

    70 80 90 100 110 120 130 140Temperature (C)

    RelativeCrystallinity

    Vcooling = 12C/min

    Vcooling = 30C/min

    Figure 11: Effect of cooling rate on crystallization atpolymer core layer.

    4.3.2 Effect of initial temperature

    To explore the polymer thermal history, we have

    studied the effect of the initial temperature in the

    material behavior, figure (12).

    0

    20

    40

    60

    80

    100

    120

    140

    160

    180

    200

    220

    0 100 200 300 400 500Time (s)

    Temperature(C)

    T0 = 180C

    T0 = 190C

    T0 = 200C

    T0 = 208 C

    Figure 12: Effect of initial temperature ontemperature profile at polymer core.

    Its clear from the evolution of temperature

    profile in the polymer core, that initial

    temperature affects drastically the cooling

    kinetics. When T0 increases, the crystallization

    begin with a delay, but the rate of cooling and

    the temperature of crystallization doesnt

    changes.

    Figure (13) shows, the evolution of relative

    crystallinity at the interface (mould/polymer) and

    at polymer core.

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    -0,1

    0

    0,1

    0,2

    0,3

    0,4

    0,5

    0,6

    0,7

    0,8

    0,9

    1

    1,1

    60 70 80 90 100 110 120 130Temperature (C)

    RelativeCrystallinity

    T0 = 180C, x = 0

    T0 = 208C, x = 0

    T0 = 180C, x = 4.5mm

    T0 = 208C, x = 4.5mm

    Figure 13: Effect of initial temperature on relative

    crystallinity at polymer core layer for Vcooling =30C/min.

    We note that crystallization beginsapproximately at the same temperature at the

    interface mould/polymer and also at the polymer

    core, but it continues on more important ranges

    of temperatures at the interfaces. Indeed, at the

    polymer core, crystallization plateau slow down

    considerably the cooling, so, the temperature

    changes less quickly, whereas crystallization

    continues. At the interface, temperatures

    decrease quickly, and the crystallization takes a

    large range of temperatures.

    5. Conclusion

    Comsol multiphysics software was used to

    simulate the cooling of a polymer as in the

    injection moulding process of a semicrystalline

    polymer. To simplify the injection mould

    configuration, we have considered a one-

    dimensional heat transfer in a system of

    polypropylene plate, initially at melt

    temperature, cooled between two metallic

    blocks. To take into account crystallization process of the material,Nakamura differential

    equation was coupled to the equations system.

    Simulations permitted us to determine profile

    temperature and relative crystallinity evolution atdifferent positions of the system. The good

    agreement between Matlab calculations and

    Comsol multiphysics simulations, in a simplified

    case, permitted us to validate our model. The

    study of the effect of different parameters such

    as the initial temperature of the system and the

    cooling rate, on the crystallization was also

    carried out. In spite of simplifyied Nakamura

    crystallization model, relative crystallinity had

    been well represented. The difficulties of

    numerical simulations, with the coupling

    between the heat transfer equation and

    crystallization equation, are easily solved andinteresting results and comparisons are obtained.

    The next objective will be to use a more

    developed crystallization kinetics model in a 3D

    simulation of the heat transfer in the injection

    moulding process.

    .

    6. References

    1. R. Fulchiron, E. Koscher, G. Poutot, D.Delaunay, G. Rgnier, Analysis of Pressure

    Effect on the Crystallization Kinetics of

    Polypropylene: Dilatometric Measurements and

    Thermal Gradient Modelling, J. Macromol. Sci,Phys., Vol. (3-4), pp 297-314 (2001).

    2. P. Le Bot, Comportement Thermique des

    Semi-Cristallins Injects: Application la

    Prdiction des Retraits, thse de doctorat, Epun

    de Nantes, 1998.

    3. H. LOBO, C. Cohen, Measurement of

    Thermal Conductivity of Polymer, Polymer

    Engineering and Science, Vol.30, pp 65-70, N2(1990).

    4. M. Avrami, Granulation, Phase Change and

    Microstructure: Kinetics of Phase Change,

    Journal of Chemistry and Physics, Vol. 9, pp177-

    184 (1941).5. K. Nakamura, T. Watanabe, Some Aspects of

    Non-Isothermal Crystallization of Polymers: I.

    Relationship between Crystallization

    Temperature, Crystallinity, and Cooling

    Conditions, Journal of applied Polymer, Vol. 26,

    pp 1077-1091 (1972).6. J.D. Hoffman, G. T. Davis and J.I Lauritzen,

    Crystalline and Non-Crystalline Solids, Treatise

    on Solids, J. B. Hannay, Plenum., New York

    (1976).

    7. E. Koscher, R. Fulchiron, Influence of Shear

    on Polypropylene Crystallization: Morphology:

    Development and Kinetics, Polymer, Vol.43, pp

    6931-6942 (2002).

    8. E. Koscher, Effets du Cisaillements sur la

    Cristallisation du Polypropylne : Aspects

    Cintiques et Morphologiques, thse de doctorat,

    universit Claude Bernard Lyon 1, 2002.

    9. J. Juo, Numerical Simulation of Stress-

    Induced Crystallization of Injection Molded

    Semicrystalline Thermoplastics, PHD Degree,

    Faculty of New Jersey Institute of Technology,

    (2001).

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