Section 6: Material modelling in solid mechanics - GAMM 2012
Section 6: Material modelling in solid mechanics - GAMM 2012
Section 6: Material modelling in solid mechanics - GAMM 2012
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<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 1<br />
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
Organizers: Daniel Balzani (Universität Duisburg-Essen), Wolfgang Dreyer (WIAS Berl<strong>in</strong>)<br />
S6.1: Microstructures <strong>in</strong> Elasto-Plasticity I Tue, 13:30–15:30<br />
Chair: Thorsten Bartel S1|01–A03<br />
A model for martensitic microstructure, its geometry and <strong>in</strong>terface effects<br />
Mehdi Goodarzi, Klaus Hackl (Universität Bochum)<br />
Martensitic materials demonstrate a characteristic microstructure <strong>in</strong> the form of parallel layers of<br />
compatible phases. This is the consequence of a symmetry-break<strong>in</strong>g phase transformation which<br />
can be well understood with<strong>in</strong> a cont<strong>in</strong>uum mechanical framework by <strong>in</strong>vestigat<strong>in</strong>g energetically<br />
favorable configurations of phase mixtures. We present a micromechanical model built upon this<br />
approach that reflects numerous attributes of the microstructure.<br />
In this model, a specific class of lam<strong>in</strong>ate geometries is constructed based on coherence condition<br />
allow<strong>in</strong>g for curved tw<strong>in</strong> <strong>in</strong>terfaces as well as three-dimensional aggregates. Proper forms of<br />
surface energies are then proposed based on scal<strong>in</strong>g arguments and crystallographic considerations.<br />
We afterwards look <strong>in</strong>to energy m<strong>in</strong>imiz<strong>in</strong>g geometries with<strong>in</strong> the class of morphologies that<br />
are considered. The results are notably compliant to the observed scale properties, size effects<br />
and accommodation patterns <strong>in</strong> the microstructure of martensite.<br />
A Formulation of F<strong>in</strong>ite Gradient Crystal Plasticity with Systematic Separation of<br />
Long- and Short-Range States<br />
S. Mauthe, F. Hildebrand, C. Miehe (Universität Stuttgart)<br />
With the ongo<strong>in</strong>g trend of m<strong>in</strong>iaturization and nanotechnology, the predictive model<strong>in</strong>g of size<br />
effects play an <strong>in</strong>creas<strong>in</strong>gly important role <strong>in</strong> metal plasticity. These size effects ma<strong>in</strong>ly stem<br />
from geometrically necessary dislocations whose description requires gradient-extended theories<br />
of crystal plasticity. However, a key challenge of the formulation and numerical implementation of<br />
gradient crystal plasticity is the complexity with<strong>in</strong> full multislip scenarios, <strong>in</strong> particular <strong>in</strong> context<br />
of rate-<strong>in</strong>dependent sett<strong>in</strong>gs.<br />
In order to partially overcome this difficulty, we suggest a new viscous regularized formulation<br />
of rate-<strong>in</strong>dependent crystal plasticity, that exploits <strong>in</strong> a systematic manner the long- and<br />
short-range nature of the <strong>in</strong>volved variables. To this end, we outl<strong>in</strong>e a multifield scenario, where<br />
the macro-deformation and the plastic slips on crystallographic systems are the primary fields.<br />
Related to these primary fields, we def<strong>in</strong>e as the long-range state the deformation gradient, the<br />
plastic slips and their gradients. We then <strong>in</strong>troduce as the short-range plastic state the plastic<br />
deformation map, the dislocation density tensor and scalar harden<strong>in</strong>g parameters associated with<br />
the slip systems. It is then shown that the evolution of the short range state is fully determ<strong>in</strong>ed<br />
by the evolution of the long-range state. This separation <strong>in</strong>to long- and short-range states<br />
is systematically exploited <strong>in</strong> the algorithmic treatment by a new update structure, where the<br />
short-range variables play the role of a local history base.<br />
The model problem under consideration accounts <strong>in</strong> a canonical format for basic effects related<br />
to statistically stored and geometrically necessary dislocation flow, yield<strong>in</strong>g micro-force balances<br />
<strong>in</strong>clud<strong>in</strong>g non-convex cross-harden<strong>in</strong>g, k<strong>in</strong>ematic harden<strong>in</strong>g and size effects. Further key <strong>in</strong>gredients<br />
of the proposed algorithmic formulation are geometrically exact updates of the short-range<br />
state and a dest<strong>in</strong>ct regularization of the rate-<strong>in</strong>dependent dissipation function that preserves the<br />
range of the elastic doma<strong>in</strong>.<br />
The formulation is shown to be fully variational <strong>in</strong> nature, goverend by rate-type cont<strong>in</strong>uous
2 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
and <strong>in</strong>cremental algorithmic variational pr<strong>in</strong>ciples. We demonstrate the model<strong>in</strong>g capabilities and<br />
algorithmic performance by means of representative numerical examples for multislip scenarios<br />
<strong>in</strong> fcc s<strong>in</strong>gle crystals.<br />
Numerical Implementation of a Three-Dimensional Cont<strong>in</strong>uum Dislocation Microplasticity<br />
Theory<br />
Stephan Wulf<strong>in</strong>ghoff, Thomas Böhlke (KIT)<br />
The <strong>modell<strong>in</strong>g</strong> of the mechanical behaviour of micro-devices can not be established by classical<br />
cont<strong>in</strong>uum mechanical plasticity models without <strong>in</strong>ternal length scale. Depend<strong>in</strong>g on the system<br />
size, ab-<strong>in</strong>itio simulations or Discrete Dislocation Dynamics serve as mature tools to predict the<br />
mechanical response of very small systems. Anyhow, the gap between these discrete and classical<br />
cont<strong>in</strong>uum mechanical methods is not yet filled. Besides phenomenological gradient plasticity<br />
models, dislocation density based approaches have emerged which account explicitly for dislocation<br />
transport and l<strong>in</strong>e length <strong>in</strong>crease. The presentation is based on the k<strong>in</strong>ematical cont<strong>in</strong>uum<br />
mechanical dislocation framework of Hochra<strong>in</strong>er et al. [1] which can be considered as a generalization<br />
of Nye’s theory [3]. The theory transfers the k<strong>in</strong>ematics of three-dimensional systems of<br />
discrete dislocations to a cont<strong>in</strong>uum mechanical representation <strong>in</strong> terms of cont<strong>in</strong>uously distributed<br />
dislocations. An averaged version of the theory by Hochra<strong>in</strong>er et al. [2] (see also Sandfeld et<br />
al. [4]) leads to a significant reduction of the computational simulation effords and will ma<strong>in</strong>ly<br />
be addressed. The k<strong>in</strong>ematical dislocation theory is coupled to a crystal plasticity framework.<br />
The presentation will focus on the numerical implementation of the theory, especially on promis<strong>in</strong>g<br />
schemes for the numerical coupl<strong>in</strong>g of the set of PDEs. F<strong>in</strong>ite Element simulation results<br />
demonstrate the performance of the implementation <strong>in</strong> three-dimensional applications.<br />
[1] T. Hochra<strong>in</strong>er, M. Zaiser and P. Gumbsch, A three-dimensional cont<strong>in</strong>uum theory of dislocations:<br />
k<strong>in</strong>ematics and mean field formulation. Philosophical Magaz<strong>in</strong>e 87 (2007), 1261–1282.<br />
[2] T. Hochra<strong>in</strong>er, M. Zaiser and P. Gumbsch, Dislocation transport and l<strong>in</strong>e length <strong>in</strong>crease <strong>in</strong><br />
averaged descriptions of dislocations. arXiv:1010.2884v1<br />
[3] J. F. Nye, Some geometrical relations <strong>in</strong> dislocated crystals. Acta Metallurgica 1 (1953),<br />
153–162.<br />
[4] S. Sandfeld, T. Hochra<strong>in</strong>er, M. Zaiser and P. Gumbsch, Cont<strong>in</strong>uum model<strong>in</strong>g of dislocation<br />
plasticity: Theory, numerical implementation, and validation by discrete dislocation<br />
simulations. J. Mater. Res. 26 (2011), 623–632.<br />
Rigorous derivation of a dissipation for lam<strong>in</strong>ate microstructures<br />
Sebastian He<strong>in</strong>z (WIAS Berl<strong>in</strong>)<br />
We study models for f<strong>in</strong>ite plasticity <strong>in</strong> the framework of rate-<strong>in</strong>dependent evolutionary systems.<br />
The correspond<strong>in</strong>g <strong>in</strong>cremental m<strong>in</strong>imization problems, <strong>in</strong> general, admit no solutions due to<br />
the creation of microstructure, see [1]. We focus on the case where the microstructure is made of<br />
simple lam<strong>in</strong>ates only. We show <strong>in</strong> a mathematical rigorous way how the <strong>in</strong>cremental m<strong>in</strong>imization<br />
problem can be relaxed and identify the relaxed dissipation as the one <strong>in</strong>troduced <strong>in</strong> [2].<br />
[1] C. Carstensen, K. Hackl, A. Mielke. Non-convex potentials and microstructures <strong>in</strong> f<strong>in</strong>ite-stra<strong>in</strong><br />
plasticity, Proc. Royal Soc. London, Ser. A 458 (2002), 299 – 317.
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 3<br />
[2] K. Hackl, D. M. Kochmann. Relaxed potentials and evolution equations for <strong>in</strong>elastic microstructures.<br />
In B. Daya Reddy, editor, IUTAM Symposium on Theoretical, Computational<br />
and Modell<strong>in</strong>g Aspects of Inelastic Media, pages 27 – 39. Spr<strong>in</strong>ger-Verlag, 2008.<br />
Thermodynamically and variationally consistent model<strong>in</strong>g of distortional harden<strong>in</strong>g:<br />
application to magnesium<br />
Baodong Shi (Helmholtz-Zentrum Geesthacht), Jörn Mosler (Helmholtz-Zentrum Geesthacht, TU<br />
Dortmund)<br />
To capture the complex elastoplastic response of many materials, classical isotropic and k<strong>in</strong>ematic<br />
harden<strong>in</strong>g alone are often not sufficient. Typical phenomena which cannot be predicted by the<br />
aforementioned harden<strong>in</strong>g models <strong>in</strong>clude, among others, cross harden<strong>in</strong>g or more generally, the<br />
distortion of the yield function. However, such phenomena do play an important role <strong>in</strong> several<br />
applications <strong>in</strong> particular, for non-radial load<strong>in</strong>g paths. Thus, they usually cannot be ignored. In<br />
the present contribution, a novel macroscopic model captur<strong>in</strong>g all such effects is proposed. In contrast<br />
to most of the exist<strong>in</strong>g models <strong>in</strong> the literature, it is strictly derived from thermodynamical<br />
arguments. Furthermore, it is the first macroscopic model <strong>in</strong>clud<strong>in</strong>g distortional harden<strong>in</strong>g which<br />
is also variationally consistent. More explicitly, all state variables follow naturally from energy<br />
m<strong>in</strong>imization with<strong>in</strong> advocated framework.<br />
A viscosity-limit approach to the evolution of microstructures <strong>in</strong> f<strong>in</strong>ite plasticity<br />
Christ<strong>in</strong>a Günther, Klaus Hackl (Universität Bochum)<br />
<strong>Material</strong> microstructures <strong>in</strong> f<strong>in</strong>ite s<strong>in</strong>gle-slip crystal plasticity occur and evolve due to deformation.<br />
Their formation is not arbitrary, they tend to form structured spatial patterns. This h<strong>in</strong>ts at a<br />
universal underly<strong>in</strong>g mechanism, <strong>in</strong> the same manner as the m<strong>in</strong>imization of the global energy governs<br />
the behavior of purely elastic materials. For non-quasiconvex potentials, the m<strong>in</strong>imizers are<br />
small scale fluctuations, related to probability distributions of the deformation gradients, which<br />
can be found by the relaxation of the potential.<br />
As <strong>in</strong> the approach of D.Kochmann and K.Hackl, we use a variational framework, focus<strong>in</strong>g on the<br />
Lagrange functional. For the treatment of the lam<strong>in</strong>ates, the potentials have to be adapted. The<br />
new approach rests on the <strong>in</strong>troduction of a small smooth transition zone between the lam<strong>in</strong>ates<br />
<strong>in</strong> order to avoid a global m<strong>in</strong>imization. This makes the evolution equations more handable for<br />
numerical calculations. We present explicit time-evolution equations for the volume fractions and<br />
the <strong>in</strong>ternal variables. We outl<strong>in</strong>e a numerical scheme and show some examples.<br />
S6.2: Polymers and Elastomers I Tue, 13:30–15:30<br />
Chair: Mikhail Itskov, Vladimir Kolupaev S1|01–A1<br />
Constitutive <strong>modell<strong>in</strong>g</strong> of chemical age<strong>in</strong>g<br />
Alexander Lion, Michael Johlitz (Universität der Bundeswehr München)<br />
In order to model chemical age<strong>in</strong>g of rubber a three-dimensional theory is proposed. The fundamentals<br />
of this approach are different decompositions of the deformation gradient <strong>in</strong> comb<strong>in</strong>ation<br />
with an additive split of the Helmholtz free energy <strong>in</strong>to three parts. Its first part belongs to the<br />
volumetric material behaviour. The second part is a temperature-dependent hyperelasticity model<br />
which depends on an additional <strong>in</strong>ternal variable to consider the long-term degradation of the<br />
primary rubber network. The third contribution is a functional of the deformation history and a<br />
further <strong>in</strong>ternal variable; it describes the creation of a new network which rema<strong>in</strong>s free of stress
4 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
when the deformation is constant <strong>in</strong> time. The constitutive relations for the stress tensor and the<br />
<strong>in</strong>ternal variables are deduced us<strong>in</strong>g the Clausius-Duhem <strong>in</strong>equality. In order to sketch the ma<strong>in</strong><br />
properties of the model, expressions <strong>in</strong> closed form are derived with respect to cont<strong>in</strong>uous and<br />
<strong>in</strong>termittent relaxation tests as well as for the compression set test. Under the assumption of near<br />
<strong>in</strong>compressible material behaviour, the theory can also represent age<strong>in</strong>g-<strong>in</strong>duced changes <strong>in</strong> volume<br />
and their effect on the stress relaxation. The simulations are <strong>in</strong> accordance with experimental<br />
data from literature.<br />
[1] A. Lion, M. Johlitz, On the representation of chemical age<strong>in</strong>g of rubber <strong>in</strong> cont<strong>in</strong>uum <strong>mechanics</strong>,<br />
International Journal of Solids and Structures, under review.<br />
Multi-phase model<strong>in</strong>g of shape memory polymers<br />
Nico Hempel, Markus Böl (TU Braunschweig)<br />
Shape memory polymers are a highly versatile class of so-called smart materials. They are able to<br />
store a certa<strong>in</strong> state of deformation and remember another one by means of an external stimulus<br />
such as light or temperature. Usually, the physical mechanism responsible for this behavior is a<br />
temperature-dependent phase transition between an “active”, entropy-elastic phase and a “frozen”,<br />
energy-elastic phase. As polymers are usually capable of experienc<strong>in</strong>g large deformations, models<br />
are required which are able to represent both the phase transitions and states of large deformation.<br />
In the present work, we propose a model based on the idea of the multiplicative decomposition<br />
of the deformation gradient. Evolution equations for the several deformation components are<br />
presented that provide for the storage of the entropy-elastic stra<strong>in</strong> and its recovery dur<strong>in</strong>g the<br />
transition between the frozen phase and the active phase. First characteristic shape memory cycles<br />
will be presented as a last po<strong>in</strong>t.<br />
On response functions <strong>in</strong> l<strong>in</strong>ear thermoelastic models of shape memory polymers<br />
Aycan Özlem Ayd<strong>in</strong>, Rasa Kazakevičiute-Makovska , Holger Steeb (Universität Bochum)<br />
There are two basic classes of constitutive models for thermoresponsive Shape Memory Polymers<br />
(SMPs), rheological and thermoelastic models. In this work, we present a detailed analysis of<br />
l<strong>in</strong>ear thermoelastic models. The first model with<strong>in</strong> this class has been proposed by Liu et al. [1]<br />
and <strong>in</strong> the follow<strong>in</strong>g years numerous modifications of that model have been presented (cf. e.g. [2]).<br />
All these models have a common mathematical structure with three basic response functions.<br />
Different models developed with<strong>in</strong> this concept follow from the general theory by specifications<br />
of the relevant response functions. The general mathematical form of the response functions<br />
is discussed and an experimental methodology determ<strong>in</strong><strong>in</strong>g of response functions directly from<br />
experimental data is presented. Representative examples illustrate the quality and the efficiency<br />
of the proposed methodology. It is shown that a reliable evaluation of thermoelastic models for<br />
SMPs requires a comparison with data for all four steps of the termomechanical cycle, both under<br />
stra<strong>in</strong>- and stress controlled conditions.<br />
[1] Y. Liu, K. Gall, M. L. Dunn, A. R. Greenberg, J. Diani, Thermo<strong>mechanics</strong> of shape memory<br />
polymers: Uniaxial experiments and constitutive model<strong>in</strong>g, Int. J. Plasticity, vol. 22, pp.<br />
279-313, 2006.<br />
[2] R. Kazakevičiute-Makovska, H. Steeb, A. Özlem Aydın, On the evolution law for the frozen<br />
fraction <strong>in</strong> the l<strong>in</strong>ear theories of shape memory polymers, Arch. App. Mech., <strong>in</strong> press, 2011.
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 5<br />
Model<strong>in</strong>g the f<strong>in</strong>ite stra<strong>in</strong> deformation and <strong>in</strong>itial anisotropy of amorphous thermoplastic<br />
polymers<br />
Philipp Hempel, Thomas Seelig (KIT)<br />
The present work deals with model<strong>in</strong>g the temperature dependent f<strong>in</strong>ite stra<strong>in</strong> deformation behavior<br />
of amorphous thermoplastic polymers <strong>in</strong>corporat<strong>in</strong>g the effect of an <strong>in</strong>itial anisotropy. The<br />
anisotropy prevails <strong>in</strong> form of a frozen-<strong>in</strong> pre-orientation of molecular cha<strong>in</strong>s and results from preced<strong>in</strong>g<br />
manufactur<strong>in</strong>g processes (e.g. <strong>in</strong>jection mold<strong>in</strong>g) at elevated temperatures and subsequent<br />
rapid cool<strong>in</strong>g. The <strong>in</strong>itial molecular orientation affects the mechanical response <strong>in</strong> terms of flow<br />
strength and harden<strong>in</strong>g.<br />
The standard f<strong>in</strong>ite stra<strong>in</strong> k<strong>in</strong>ematics with a multiplicative split of the deformation gradient <strong>in</strong>to<br />
an elastic and plastic part is modified by <strong>in</strong>troduc<strong>in</strong>g a network deformation gradient which comprises<br />
the actual plastic deformation and the <strong>in</strong>itial (process<strong>in</strong>g <strong>in</strong>duced) pre-deformation [1],[2].<br />
As a computational example, an <strong>in</strong>jection molded plate is <strong>in</strong>vestigated which displays nonuniform<br />
shr<strong>in</strong>kage and buckl<strong>in</strong>g dur<strong>in</strong>g heat<strong>in</strong>g due to the action of the frozen-<strong>in</strong> network stress. The<br />
spatial distribution of molecular pre-orientation, and hence <strong>in</strong>itial anisotropy, <strong>in</strong> the FE model is<br />
estimated from optical birefr<strong>in</strong>gence.<br />
[1] E.M. Arruda, M.C. Boyce, Evolution of plastic anisotropy <strong>in</strong> amorphous polymers dur<strong>in</strong>g<br />
f<strong>in</strong>ite stra<strong>in</strong><strong>in</strong>g, International Journal of Plasticity (1993), 6 –697.<br />
[2] M.C. Boyce, D.M. Parks, A.S. Argon, Plastic flow <strong>in</strong> oriented glassy polymers, International<br />
Journal of Plasticity (1998), 6 – 593.<br />
Model<strong>in</strong>g of <strong>in</strong>duced anisotropy at large deformations for polymers<br />
Ismail Caylak, Rolf Mahnken (Universität Paderborn)<br />
In this presentation we develop a model to describe the <strong>in</strong>duced plasticity of polymers at large<br />
deformations. Polymers such as stretch films exhibit a pronounced strength <strong>in</strong> the load<strong>in</strong>g direction.<br />
The undeformed state of the films is isotropic, whereas after the uni-axial load<strong>in</strong>g the<br />
material becomes anisotropic. In order to consider this <strong>in</strong>duced ansiotropy dur<strong>in</strong>g the stretch<br />
process, a spectral decomposition of the <strong>in</strong>elastic Cauchy-Green tensor is done. Therefore, the<br />
yield function can be formulated as a function of the anisotropic tensor, where aga<strong>in</strong> the anisotropic<br />
tensor is a function of the maximum eigenvalue. A backward Euler scheme is used for<br />
updat<strong>in</strong>g the evolution equations, and the algorithmic tangent operator is derived. The numerical<br />
implementation of the result<strong>in</strong>g set of constitutive equations is used <strong>in</strong> a f<strong>in</strong>ite element program<br />
and for parameter identification.<br />
S6.3: Microstructures <strong>in</strong> Elasto-Plasticity II Tue, 16:00–18:00<br />
Chair: Dennis Kochmann, Sebastian He<strong>in</strong>z S1|01–A03<br />
Microstructure development <strong>in</strong> a Cosserat cont<strong>in</strong>uum as a consequence of energy<br />
relaxation<br />
Muhammad Sabeel Khan, Klaus Hackl (Universität Bochum)<br />
A rate-<strong>in</strong>dependent <strong>in</strong>elastic material model for a Cosserat cont<strong>in</strong>uum is presented. The free energy<br />
of the material is enriched with an <strong>in</strong>teraction potential tak<strong>in</strong>g <strong>in</strong>to account the <strong>in</strong>tergranular
6 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
k<strong>in</strong>ematics at the cont<strong>in</strong>uum scale. As a result the total energy becomes non-convex, thus giv<strong>in</strong>g<br />
rise to the development of microstructure. To guarantee the existence of m<strong>in</strong>imizers an exact<br />
quasi-convex envelope of the correspond<strong>in</strong>g energy functional is derived. As a result microstructure<br />
occurs <strong>in</strong> both the displacement and micro-rotation field. The correspond<strong>in</strong>g relaxed energy<br />
is then used for f<strong>in</strong>d<strong>in</strong>g the m<strong>in</strong>imizers of the two field m<strong>in</strong>imization problem correspond<strong>in</strong>g to a<br />
Cosserat cont<strong>in</strong>uum. F<strong>in</strong>ite element formulation and numerical simulations are presented. Analytical<br />
and numerical results are discussed.<br />
About the Microstructural Effects of Polycrystall<strong>in</strong>e <strong>Material</strong>s and their Macroscopic<br />
Representation at F<strong>in</strong>ite Deformation<br />
Eva Lehmann, Stefan Loehnert, Peter Wriggers (Universität Hannover)<br />
In the sheet bulk metal form<strong>in</strong>g field, the strict geometrical requirements of the workpieces result<br />
<strong>in</strong> a need of a precise prediction of the material behaviour. The simulation of such form<strong>in</strong>g processes<br />
requires a valid material model, perform<strong>in</strong>g well for a huge variety of different geometrical<br />
characteristics and f<strong>in</strong>ite deformation.<br />
Because of the crystall<strong>in</strong>e nature of metals, anisotropies have to be taken <strong>in</strong>to account. Macroscopically<br />
observable plastic deformation is traced back to dislocations with<strong>in</strong> considered slip<br />
systems <strong>in</strong> the crystals caus<strong>in</strong>g plastic anisotropy on the microscopic and the macroscopic level.<br />
A f<strong>in</strong>ite crystal plasticity model is used to model polycrystall<strong>in</strong>e materials <strong>in</strong> representative<br />
volume elements (RVEs) of the microstructure. A multiplicative decomposition of the deformation<br />
gradient <strong>in</strong>to elastic and plastic parts is performed, as well as a volumetric-deviatoric split of the<br />
elastic contribution. In order to circumvent s<strong>in</strong>gularities stemm<strong>in</strong>g from the l<strong>in</strong>ear dependency<br />
of the slip system vectors, a viscoplastic power-law is <strong>in</strong>troduced provid<strong>in</strong>g the evolution of the<br />
plastic slips and slip resistances.<br />
The model is validated with experimental microstructural data under deformation. The validation<br />
on the macroscopic scale is performed through the reproduction of the experimentally<br />
calculated <strong>in</strong>itial yield surface. Additionally, homogenised stress-stra<strong>in</strong> curves from the microstructure<br />
build the outcome for a suitable effective material model. Through optimisation techniques,<br />
effective material parameters can be determ<strong>in</strong>ed and compared to results from real form<strong>in</strong>g processes.<br />
A rheological model for arbitrary symmetric distortion of the yield surface<br />
A.V. Shutov, J. Ihlemann (TU Chemnitz)<br />
A new rheological model is presented, which provides <strong>in</strong>sight <strong>in</strong>to phenomenological <strong>modell<strong>in</strong>g</strong> of<br />
comb<strong>in</strong>ed nonl<strong>in</strong>ear k<strong>in</strong>ematic and distortional harden<strong>in</strong>g. The model is constructed by coupl<strong>in</strong>g<br />
idealized two-dimensional rheological elements like Hooke-body, Newton-body, and modified St.<br />
Venant element [1,2]. The symmetric distortion of the yield surface and its orientation depend<strong>in</strong>g<br />
on the recent load<strong>in</strong>g path are captured by the rheological model <strong>in</strong> a vivid way. We emphasize the<br />
flexibility of the proposed approach s<strong>in</strong>ce it can be used to capture any smooth convex saturated<br />
form of the yield surface observed experimentally, if the yield surface is symmetric with respect to<br />
the recent load<strong>in</strong>g direction. In particular, an arbitrary sharpen<strong>in</strong>g of the saturated yield locus <strong>in</strong><br />
the load<strong>in</strong>g direction comb<strong>in</strong>ed with a flatten<strong>in</strong>g on the opposite side can be taken <strong>in</strong>to account<br />
[2]. Moreover, the yield locus evolves smoothly and its convexity is ensured at each harden<strong>in</strong>g<br />
stage.<br />
The rheological model serves as a guidel<strong>in</strong>e for construction of new constitutive relations. The<br />
k<strong>in</strong>ematic assumptions, the ansatz for the free energy and for the yield function are motivated by<br />
the rheological model. Additionally to k<strong>in</strong>ematic and distortional harden<strong>in</strong>g, a nonl<strong>in</strong>ear isotropic<br />
harden<strong>in</strong>g is <strong>in</strong>troduced as well. Normality flow rule is considered, and a rigorous proof of ther-
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 7<br />
modynamic consistency is provided. F<strong>in</strong>ally, the predictive capabilities of the result<strong>in</strong>g material<br />
model are verified us<strong>in</strong>g the experimental data for a very high work harden<strong>in</strong>g annealed alum<strong>in</strong>um<br />
alloy 1100 Al.<br />
[1] A.V. Shutov, S. Panhans, R. Kreißig, A phenomenological model of f<strong>in</strong>ite stra<strong>in</strong> viscoplasticity<br />
with distortional harden<strong>in</strong>g, ZAMM, 8, 653 - 680.<br />
[2] A.V. Shutov, J. Ihlemann, A viscoplasticity model with an enhanced control of the yield<br />
surface distortion, Submitted to International Journal of Plasticity.<br />
Towards the simulation of Internal Traverse Gr<strong>in</strong>d<strong>in</strong>g – from mesoscale <strong>modell<strong>in</strong>g</strong> to<br />
process simulations<br />
Raphael Holtermann (TU Dortmund), Andreas Menzel (TU Dortmund / Lund University)<br />
The present work aims at the <strong>modell<strong>in</strong>g</strong> and simulation of Internal Traverse Gr<strong>in</strong>d<strong>in</strong>g of hardened<br />
100Cr6/AISI 52100 us<strong>in</strong>g electro plated cBN gr<strong>in</strong>d<strong>in</strong>g wheels. We focus on the thermomechanical<br />
behaviour result<strong>in</strong>g from the <strong>in</strong>teraction of tool and workpiece <strong>in</strong> the process zone on a mesoscale.<br />
Based on topology analyses of the gr<strong>in</strong>d<strong>in</strong>g wheel surface, two-dimensional s<strong>in</strong>gle- and multigra<strong>in</strong><br />
representative numerical experiments are performed to <strong>in</strong>vestigate the result<strong>in</strong>g loaddisplacement-behaviour<br />
as well as the specific heat generation due to friction and plastic dissipation.<br />
A thermoelastic-viscoplastic constitutive model is used to capture thermal soften<strong>in</strong>g of the<br />
material taken <strong>in</strong>to account. Based on previous work [1,2], an adaptive remesh<strong>in</strong>g scheme which<br />
uses a comb<strong>in</strong>ation of error estimation and <strong>in</strong>dicator methods, is applied to overcome mesh dependence.<br />
In consequence, the formulation allows to resolve the complex deformation patterns<br />
and to predict a realistic thermomechanical state of the result<strong>in</strong>g workpiece surface [3].<br />
As a future goal, we aim at coupl<strong>in</strong>g the above cutt<strong>in</strong>g zone model to a process scale simulation<br />
to model the thermomechanical behaviour of the entire three-dimensional workpiece.<br />
[1] C. Hortig and B. Svendsen, Simulation of chip formation dur<strong>in</strong>g high-speed cutt<strong>in</strong>g, J. Mat.<br />
Process<strong>in</strong>g Technology 186, 66–76 (2007)<br />
[2] C. Hortig and B. Svendsen, Adaptive model<strong>in</strong>g and simulation of shear band<strong>in</strong>g and high<br />
speed cutt<strong>in</strong>g, Proc. 10th ESAFORM Conference on <strong>Material</strong> Form<strong>in</strong>g CP907, 721–726<br />
(2007)<br />
[3] D. Biermann, A. Menzel, T. Bartel, F. Höhne, R. Holtermann, R. Ostwald, B. Sieben, M.<br />
Tiffe, A. Zabel, Experimental and computational <strong>in</strong>vestigation of mach<strong>in</strong><strong>in</strong>g processes for<br />
functionally graded materials, Procedia Eng<strong>in</strong>eer<strong>in</strong>g, accepted for publication, 2011<br />
Multiscale crystal plasticity based on cont<strong>in</strong>uum theory of dislocation <strong>mechanics</strong>: an<br />
extension to ductile fracture.<br />
Mubeen Shahid, Klaus Hackl (Universität Bochum)<br />
The presentation focuses on the <strong>modell<strong>in</strong>g</strong> of phenomena associated with plastic deformations<br />
<strong>in</strong> crystall<strong>in</strong>e materials. The plastic deformation <strong>in</strong> crystall<strong>in</strong>e materials strongly depends on<br />
aggregate behaviour of dislocations. However there is no universal constitutive frame-work which<br />
directly relates all the attributes of dislocations at microscale to the macroscale deformations,<br />
both qualitatively and quantitatively.
8 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
First the macroscale constitutive model based on the cont<strong>in</strong>uum theory of dislocations [1,2]<br />
is discussed. The plastic deformation and crack growth dur<strong>in</strong>g ductile fracture mutually effect<br />
each other, where dislocations’ movement shape the crack growth, and the latter effects the<br />
dislocations density [3]. We discuss the numerical implementation of the proposed crystal viscoelastoplasticity<br />
model coupled with modern dislocation measures [1,2] and present an example<br />
where the mechanisms of crystal plasticity are l<strong>in</strong>ked to the ductile fracture. The results focus<br />
the effect of severe plastic deformation on dislocations evolution and crack growth behaviour,<br />
follow<strong>in</strong>g the approach of Cherepanov [3].<br />
[1] T. Hochra<strong>in</strong>er, M. Zaiser, P. Gumbsch, A three-dimensional cont<strong>in</strong>uum theory of dislocation<br />
systems: k<strong>in</strong>ematics and mean-field formulation, Philosophical Magaz<strong>in</strong>e, 87:8-9 (2007),<br />
1261-1282.<br />
[2] S. Sandfeld, T. Hochra<strong>in</strong>er, P. Gumbsch, M. Zaiser, Numerical implementation of a 3D<br />
cont<strong>in</strong>uum theory of dislocation: dynamics and application to micro-bend<strong>in</strong>g, Philosophical<br />
Magaz<strong>in</strong>e, 90:27-28 (2010), 3697-3728.<br />
[3] G.P. Cherepanov et al., Dislocation generation and crack growth under monotonic load<strong>in</strong>g,<br />
J. Appl. Phys., 78(10) (1995), 6249-6264.<br />
Multiscale <strong>modell<strong>in</strong>g</strong> and simulation of micro mach<strong>in</strong><strong>in</strong>g of titan<br />
Richard Lohkamp, Ralf Müller (TU Kaiserslautern)<br />
The topology of micro mach<strong>in</strong>ed surfaces depends strongly on the underly<strong>in</strong>g heterogeneous microstructure<br />
of the material. The crystal structure <strong>in</strong>fluences the deformation and separation<br />
characteristics. In the case of α-titanium the deformation is dictated by the hcp crystal structure<br />
with its specific slip systems. In the crystal plastic deformation it is essential to take self and latent<br />
harden<strong>in</strong>g <strong>in</strong>to account. Furthermore to capture the rate dependent behavior a visco-plastic<br />
evolution law is used. This sett<strong>in</strong>g serves as a framework for more complex constitutive laws, such<br />
as the one given <strong>in</strong> [1].<br />
As a first attempt to model the cutt<strong>in</strong>g process, the fracture mechanisms <strong>in</strong> a crystall<strong>in</strong>e αtitanium<br />
are analysed with<strong>in</strong> the concept of configurational forces. To this end the theory of<br />
configurational forces is presented for a standard dissipative medium and is specialized to the<br />
crystal plasticity sett<strong>in</strong>g. The numerical implementation of the material law and the configurational<br />
forces is done <strong>in</strong> a consistent way with<strong>in</strong> the f<strong>in</strong>ite element method. The application of<br />
configurational forces <strong>in</strong> the crystal plasticity sett<strong>in</strong>g is discussed and demonstrated by illustrative<br />
examples.<br />
S6.4: Polymers and Elastomers II Tue, 16:00–18:00<br />
Chair: Alexander Lion, Joachim Schmitt S1|01–A1<br />
How to approximate the <strong>in</strong>verse Langev<strong>in</strong> function?<br />
Mikhail Itskov, Roozbeh Dargazany, Karl Hörnes (RWTH Aachen)<br />
The <strong>in</strong>verse Langev<strong>in</strong> function directly results from the non-Gaussian theory of rubber elasticity<br />
as the cha<strong>in</strong> force and represents an <strong>in</strong>dispensable <strong>in</strong>gredient of full-network rubber elasticity models.<br />
However, the <strong>in</strong>verse Langev<strong>in</strong> function cannot be represented <strong>in</strong> a closed-form and requires<br />
an approximation as for example a Padé approximation. The Padé approximations can be given
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 9<br />
<strong>in</strong> a relatively simple form and are able to describe the asymptotic behavior of the <strong>in</strong>verse Langev<strong>in</strong><br />
function <strong>in</strong> the vic<strong>in</strong>ity of the maximum cha<strong>in</strong> extensibility. Far away from the asymptotic<br />
area the approximation error can be, however, relatively large. In the present contribution we<br />
compare various Padé approximants with the Taylor power series representation of the <strong>in</strong>verse<br />
Langev<strong>in</strong> function. To this end, a simple recursive procedure calculat<strong>in</strong>g power series coefficients<br />
of the <strong>in</strong>verse function is proposed. The procedure can be applied to any function which can be<br />
expanded <strong>in</strong>to Taylor series. With<strong>in</strong> the convergence radius the result<strong>in</strong>g series of the <strong>in</strong>versed<br />
Langev<strong>in</strong> function demonstrates better agreement with the analytical solution than the Padé approximations.<br />
Phenomenological model<strong>in</strong>g of a polymeric composite<br />
Sebastian Borsch, Albrecht Bertram (Universität Magdeburg)<br />
A composite material consist<strong>in</strong>g of a polymeric matrix material and metallic filler particles is<br />
modeled <strong>in</strong> a phenomenological way. The isotropic viscoplastic constitutive model is formulated<br />
with<strong>in</strong> the theory of f<strong>in</strong>ite deformations. The flow rule is a superposition of two terms. This<br />
approach enables us to simulate the strong backflow behavior dur<strong>in</strong>g unload<strong>in</strong>g, which can be<br />
observed <strong>in</strong> various polymeric materials. A quasi-static f<strong>in</strong>ite-element simulation has been performed<br />
to compare the model with cyclic tension tests as well as a relaxation test.<br />
Modell<strong>in</strong>g of nano<strong>in</strong>dentation of polymers with effects of surface roughness and parameters<br />
identification<br />
Zhaoyu Chen, Stefan Diebels (Universität des Saarlandes)<br />
S<strong>in</strong>ce the nano<strong>in</strong>dentation test<strong>in</strong>g technique can measure the properties of extremely small volumes<br />
with sub-m and sub-N resolution from the cont<strong>in</strong>uously sensed force-displacement curves,<br />
it also became one of the primary test<strong>in</strong>g techniques for polymeric materials and biological tissues.<br />
The analysis of <strong>in</strong>dividual <strong>in</strong>dentation tests us<strong>in</strong>g the conventionally applied Oliver & Pharr<br />
method has limitations to capture the hyperelastic and rate-dependent properties of polymers.<br />
Therefore, an <strong>in</strong>verse method with respect to the experimental test<strong>in</strong>g, based on f<strong>in</strong>ite element<br />
simulation and numerical optimisation has been used and evolved. However, nano<strong>in</strong>dentation is<br />
composed of various error contributions, e. g. friction, adhesion, surface roughness and <strong>in</strong>dentation<br />
process associated factors. These contributions form<strong>in</strong>g the systematic errors between the<br />
numerical model and the experiments will often lead to large errors <strong>in</strong> the parameters identification.<br />
Therefore, basic <strong>in</strong>vestigations and quantification of these <strong>in</strong>fluences are <strong>in</strong>dispensable to<br />
characterise the materials accurately from nano<strong>in</strong>dentation based on the <strong>in</strong>verse method.<br />
In the present contribution, the characterisation of polymers through nano<strong>in</strong>dentation with effects<br />
of the surface roughness based on <strong>in</strong>verse method will be <strong>in</strong>vestigated numerically. The boundary<br />
value problems of nano<strong>in</strong>dentation of polymers are modelled with the FE code ABAQUS R○ .<br />
In contrast to the traditional <strong>in</strong>verse method, virtual experimental data calculated by numerical<br />
simulations with chosen parameters replace the real experimental measurements. Such a procedure<br />
is called parameter re-identification. In this sense, the f<strong>in</strong>ite element code ABAQUS R○ is used as<br />
our virtual laboratory. The model parameters are identified us<strong>in</strong>g an evolution strategy based on<br />
the concept of numerical optimisation. The surface roughness effects are <strong>in</strong>vestigated numerically<br />
based on the approach utiliz<strong>in</strong>g the phenomenological concepts. The surface roughness is chosen<br />
to have a simple representation consider<strong>in</strong>g only one-level of roughness profile described by a<br />
s<strong>in</strong>e function. The <strong>in</strong>fluence of the surface roughness is quantified associated to the s<strong>in</strong>e curve<br />
parameters as well as to the <strong>in</strong>dentation parameters. Moreover, the real surface topography is
10 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
characterised us<strong>in</strong>g multi-level of protuberance-on-protuberance profiles. The effects of the surface<br />
roughness are <strong>in</strong>vestigated with respect to the identified model parameters us<strong>in</strong>g a surface<br />
topography with one-level or multi-level profiles approximated by a s<strong>in</strong>e function. The results are<br />
expected to offer a deep <strong>in</strong>sight <strong>in</strong>to characteris<strong>in</strong>g the real surface roughness numerically.<br />
<strong>Material</strong> force computation for the thermo-mechanical response of dynamically loaded<br />
elastomers<br />
Ronny Behnke, Michael Kaliske (TU Dresden)<br />
Elastomers are widely used <strong>in</strong> our today’s life. The material is characterized by large deformability<br />
upon failure, elastic and time dependent as well as non-time dependent effects which can<br />
be also a function of temperature. In addition, cyclically loaded components show heat built-up<br />
which is due to dissipation. As a result, the temperature evolution of an elastomeric component<br />
can strongly <strong>in</strong>fluence the material properties and durability characteristics. Represent<strong>in</strong>g best<br />
the real thermo-mechanical behaviour of an elastomeric component <strong>in</strong> its design process is one<br />
motivation for the use of sophisticated, coupled material approaches with<strong>in</strong> numerical simulations.<br />
In order to assess the durability characteristics, for example regard<strong>in</strong>g crack propagation, the<br />
material forces (configurational forces) are one possible approach to be applied. In the present<br />
contribution, the implementation of material forces for a thermo-mechanically coupled material<br />
model <strong>in</strong>clud<strong>in</strong>g a cont<strong>in</strong>uum mechanical damage (CMD) approach is demonstrated <strong>in</strong> the context<br />
of the F<strong>in</strong>ite Element Method (FEM). Special emphasis is given to material forces result<strong>in</strong>g<br />
from <strong>in</strong>ternal variables (viscosity and damage variables), temperature field evolution and dynamic<br />
load<strong>in</strong>g. Us<strong>in</strong>g an example of an elastomeric component, for which the material model parameters<br />
have been previously identified by a uniaxial extension test, material forces are evaluated quantitatively.<br />
The <strong>in</strong>fluence of each contribution (<strong>in</strong>ternal variables, temperature field and dynamics)<br />
is illustrated and compared to the overall material force response.<br />
S<strong>in</strong>gle and multiscale aspects of the model<strong>in</strong>g of cur<strong>in</strong>g polymers<br />
Alexander Bartels ∗ , Sandra Kl<strong>in</strong>ge ∗ , Klaus Hackl ∗ , Paul Ste<strong>in</strong>mann ∗∗ (Universität Bochum, Universität<br />
Erlangen-Nürnberg)<br />
With<strong>in</strong> this presentation, the focus is placed on the simulation of the isochoric behavior of polymers<br />
dur<strong>in</strong>g the cur<strong>in</strong>g process. To this end, a model based on the assumption for the free<br />
energy <strong>in</strong> the form of a convolution <strong>in</strong>tegral is applied. S<strong>in</strong>ce this allows the implementation of<br />
the time dependent material parameters, the free energy is <strong>in</strong>terpreted as the total-accumulated<br />
energy. Different from this, the stra<strong>in</strong> energy is related to the current state of deformation and<br />
used to def<strong>in</strong>e the temporary stiffness. In order to avoid volume lock<strong>in</strong>g effects typical for isochoric<br />
materials, the free energy is furthermore split <strong>in</strong>to a volumetric and a deviatoric part. A<br />
multifield description depend<strong>in</strong>g on the displacements, volume change and hydrostatic pressure<br />
is <strong>in</strong>troduced as well. The model is implemented with<strong>in</strong> a s<strong>in</strong>gle- and multiscale FE program<br />
and used to simulate the behavior of homogeneous and microheterogeneous polymers. The ma<strong>in</strong><br />
property of the multiscale concept used here is that the model<strong>in</strong>g of a heterogeneous body is<br />
performed by simultaneously solv<strong>in</strong>g two boundary value problems: one related to the behavior<br />
of the macroscopic body and the other one deal<strong>in</strong>g with the analysis of the representative volume<br />
element.<br />
Influence of nano-particle <strong>in</strong>teractions on the mechanical behavior of colloidal structures<br />
<strong>in</strong> polymeric solutions<br />
Roozbeh Dargazany, Ngoc Khiêm Vu , Mikhail Itskov (RWTH Aachen)<br />
Colloidal structures <strong>in</strong>side solutions are usually considered as rigid bodies or l<strong>in</strong>ear spr<strong>in</strong>gs. Howe-
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 11<br />
ver, recent experimental results show a strongly nonl<strong>in</strong>ear mechanical response of large clusters.<br />
In this contribution, the nonl<strong>in</strong>ear elastic behavior of the colloidal structures <strong>in</strong>side polymeric<br />
solutions is studied. So far, the <strong>in</strong>fluences of <strong>in</strong>itial length and fractal dimension on the elastic response<br />
of colloidal structures have mostly been considered by scal<strong>in</strong>g theory. Here, we additionally<br />
take <strong>in</strong>to account a deformation <strong>in</strong>duced evolution of the aggregate structure which is ma<strong>in</strong>ly <strong>in</strong>fluenced<br />
by <strong>in</strong>ter-particle <strong>in</strong>teractions. To this end, central and lateral (non-central) <strong>in</strong>ter-particle<br />
forces are considered separately. Next, the directional stiffness of the colloidal structure is evaluated<br />
by us<strong>in</strong>g the concept of a backbone cha<strong>in</strong>. The backbone cha<strong>in</strong> is a unique path between two<br />
ends of the colloidal structure that carries the ma<strong>in</strong> portion of load. The mechanical response of<br />
the backbone cha<strong>in</strong> depends on aggregate geometry, deformation history and moreover, on the<br />
nature and the strength of the <strong>in</strong>ter-particle <strong>in</strong>teractions. The aggregate geometry is described by<br />
means of the angular averag<strong>in</strong>g concept. The so-obta<strong>in</strong>ed model can further be generalized for all<br />
types of colloidal structures with central and lateral <strong>in</strong>ter-particle forces.<br />
S6.5: Phase Transformations I Wed, 13:30–15:30<br />
Chair: Markus Lazar, Wolfgang Dreyer S1|01–A03<br />
A thermodynamically consistent framework for martensitic phase transformations<br />
<strong>in</strong>teract<strong>in</strong>g with plasticity<br />
Thorsten Bartel, Andreas Menzel (TU Dortmund)<br />
We propose constitutive relations for martensitic phase transformations at large stra<strong>in</strong>s which<br />
captures the <strong>in</strong>teractions between phase transformations, plasticity and the local heat<strong>in</strong>g of the<br />
material due to the <strong>in</strong>elastic processes. For the k<strong>in</strong>ematics of f<strong>in</strong>ite deformations we make use<br />
of logarithmic Hencky-stra<strong>in</strong>s. The total stra<strong>in</strong> is additively decomposed <strong>in</strong>to elastic, plastic and<br />
transformation related parts, where the latter quantities are motivated by crystallographic considerations.<br />
The thermodynamically consistent framework is based on a representative macroscopic<br />
energy density and an <strong>in</strong>elastic potential <strong>in</strong> terms of a dual dissipation functional. With these<br />
quantities at hand, thermodynamical driv<strong>in</strong>g forces as well as rate-<strong>in</strong>dependent evolution equations<br />
are derived <strong>in</strong> a canonical way. In this regard, the proposed model states an alternative to the<br />
models described <strong>in</strong> [1,2]. Referr<strong>in</strong>g to [3], the local heat<strong>in</strong>g of the material is realised by a consistently<br />
derived temperature evolution equation captur<strong>in</strong>g the effect of self heat<strong>in</strong>g. The solution<br />
of the obta<strong>in</strong>ed local system of equations is challeng<strong>in</strong>g and demands a sophisticated algorithmic<br />
treatment. To this end, we present a scheme which avoids cumbersome and time-consum<strong>in</strong>g active<br />
set searches by the use of Fischer-Burmeister NCP functions and furthermore prevents the<br />
occurence of redundant equations by a specific condensation strategy. The numerical examples<br />
emphasize the capabilities of the proposed model which is, among other aspects, exemplified by<br />
a transformation <strong>in</strong>duced anisotropy. Furthermore, special attention is paid to the simulation of<br />
the complex material behaviour of, e.g., TRIP-steels.<br />
[1] T. Bartel, A. Menzel, B. Svendsen, Thermodynamic and relaxation-based model<strong>in</strong>g of the<br />
<strong>in</strong>teraction between martensitic phase transformations and plasticity, J. Mech. Phys. Sol.<br />
Vol. 59, 1004-1019, 2011,<br />
[2] R. Ostwald, T. Bartel, A. Menzel, A one-dimensional computational model for the <strong>in</strong>teraction<br />
of phase-transformations and plasticity, Int. Journal of Structural Changes <strong>in</strong> Solids Vol. 3,<br />
63-82, 2011,<br />
[3] J. C. Simo, C. Miehe, Associative coupled thermoplasticity at f<strong>in</strong>ite stra<strong>in</strong>s: Formulation,<br />
numerical analysis and implementation, Comp. Meth. Appl. Mech. Engrg. Vol. 98, 41-104,
12 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
1992<br />
Deformation <strong>in</strong>duced martensite transformation <strong>in</strong> a cold-worked form<strong>in</strong>g process of<br />
austenitic sta<strong>in</strong>less steel<br />
Tim Dally, Kerst<strong>in</strong> We<strong>in</strong>berg (Universität Siegen)<br />
With<strong>in</strong> the last years the goal of <strong>in</strong>dustrial manufactur<strong>in</strong>g processes - such as tube form<strong>in</strong>g - has<br />
shifted towards an optimization of technological as well as mechanical properties of the manufactured<br />
structures. For example, dur<strong>in</strong>g the form<strong>in</strong>g procedure of sheets made of austenitic sta<strong>in</strong>less<br />
steel X5CrNi18-10, the content of stra<strong>in</strong>-<strong>in</strong>duced martensite needs to be controlled. In order to<br />
achieve optimal structural properties of the manufactured tube with respect to very high-cycle<br />
fatigue (VHCF), a martensite ratio of approximately 25% needs to be obta<strong>in</strong>ed.<br />
On the basis of experimental <strong>in</strong>vestigations our contribution deals with the numerical simulation<br />
of the form<strong>in</strong>g process with special consideration of the martensite ratio c as a function of<br />
temperature and deformation field:<br />
c = c(T, ε p ).<br />
In particular, we study the <strong>in</strong>teraction of process<strong>in</strong>g temperature, friction, plastic deformation<br />
and stress state dur<strong>in</strong>g form<strong>in</strong>g. We will further present different approaches of <strong>modell<strong>in</strong>g</strong> the<br />
martensite evolution as well as the extension of an exist<strong>in</strong>g martensite model on polyaxial states<br />
of stress and compare experimental results and numerical simulations for the modified model.<br />
Additionally a facility to calculate the harden<strong>in</strong>g due to martensitic phase transformation will be<br />
presented.<br />
F<strong>in</strong>ally, we will propose a strategy to control the martensite evolution dur<strong>in</strong>g the tube-form<strong>in</strong>g<br />
process that enables us to achieve the optimal c mentioned above.<br />
Micromechanical model<strong>in</strong>g of ba<strong>in</strong>itic phase transformation<br />
A. Schneidt, R. Mahnken (Universität Paderborn), T. Antretter (Montanuniversität Leoben)<br />
We develop a micromechanical material model for phase transformation from austenite to ba<strong>in</strong>ite<br />
for a polycrystall<strong>in</strong>e low alloys steel. In this material (e.g. 51CrV4) the phase changes from<br />
austenite to perlite-ferrite, ba<strong>in</strong>ite or martensite, respectively. This work is concerned with phase<br />
transformation between austenite and n-ba<strong>in</strong>ite variants <strong>in</strong> different orientated gra<strong>in</strong>s. Characteristic<br />
of ba<strong>in</strong>ite are the comb<strong>in</strong>ation of time-dependent transformation k<strong>in</strong>etics and lattice shear<strong>in</strong>g<br />
<strong>in</strong> the microstructure. These effects are considered on the microscale and by means of homogenisation<br />
scale <strong>in</strong> the polycrystall<strong>in</strong>e macroscale with stochastically orientated gra<strong>in</strong>s. Furthermore, the<br />
numerical implementation of our model with a Newton projection algorithm <strong>in</strong>to a f<strong>in</strong>ite-element<br />
program is presented, based on the algorithm <strong>in</strong> [1].<br />
[1] R. Mahnken and S. Wilmanns, A projected Newton algorithm for simulation of multivariant<br />
textured polycrystall<strong>in</strong>e shape memory alloys. Computational <strong>Material</strong>s Science 50,<br />
25352548, 2011.<br />
Effects of heat treatment on phase transformation <strong>in</strong> powder metallurgical multifunctional<br />
coat<strong>in</strong>g<br />
Reza Kebriaei, Jan Frischkorn, Stefanie Reese (RWTH Aachen)
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 13<br />
Heat treatment is an <strong>in</strong>dispensable part of the manufactur<strong>in</strong>g of metallic products, especially <strong>in</strong><br />
powder coat<strong>in</strong>g process. It provides an efficient way to manipulate the properties of the metal as<br />
e.g. hardness, yield stress and tensile stress by controll<strong>in</strong>g the rate of diffusion and the rate of<br />
cool<strong>in</strong>g with<strong>in</strong> the microstructure.<br />
The process-<strong>in</strong>tegrated powder coat<strong>in</strong>g by radial axial roll<strong>in</strong>g of r<strong>in</strong>gs is a new hybrid production<br />
technique which is <strong>in</strong>troduced <strong>in</strong> [1]. It takes advantage of the high temperatures and high<br />
forces of the r<strong>in</strong>g roll<strong>in</strong>g process not only to <strong>in</strong>crease the r<strong>in</strong>gs diameter, but also to <strong>in</strong>tegrate<br />
the application and compaction of powder metallurgical multi-functional coat<strong>in</strong>gs to the <strong>solid</strong><br />
substrate r<strong>in</strong>gs with<strong>in</strong> the same process [2]. The applied temperatures <strong>in</strong> hot roll<strong>in</strong>g are with<strong>in</strong><br />
the range of austenitiz<strong>in</strong>g temperatures for the <strong>in</strong>vestigated steels. Therefore, controlled cool<strong>in</strong>g<br />
can be conducted directly from process heat subsequent to the deformation process.<br />
The talk is concerned with the f<strong>in</strong>ite element (FE) simulation of the process-<strong>in</strong>tegrated powder<br />
coat<strong>in</strong>g by radial axial roll<strong>in</strong>g of r<strong>in</strong>gs and the <strong>in</strong>tegration of heat treatment of the rolled r<strong>in</strong>g<br />
<strong>in</strong>to the subsequent cool<strong>in</strong>g process. F<strong>in</strong>ally parameter studies are performed to analyse the<br />
temperature profile and phase transformation <strong>in</strong> the r<strong>in</strong>gs cross-section.<br />
[1] J. Frischkorn, S. Reese, Modell<strong>in</strong>g and Simulation of Process-<strong>in</strong>tegrated Powder Coat<strong>in</strong>g by<br />
Radial Axial Roll<strong>in</strong>g of R<strong>in</strong>gs, Archive of Applied Mechanics 81 (2011)<br />
[2] R. Kebriaei, J. Frischkorn, S. Reese, Influence of Geometric Parameters on Residual Porosity<br />
<strong>in</strong> Process-<strong>in</strong>tegrated Powder Coat<strong>in</strong>g by Radial Axial Roll<strong>in</strong>g of R<strong>in</strong>gs, Steel Research<br />
International 163 (2011)<br />
Simulation of phase-transformations based on numerical m<strong>in</strong>imization of <strong>in</strong>tersect<strong>in</strong>g<br />
Gibbs energy potentials<br />
Richard Ostwald, Thorsten Bartel (TU Dortmund), Andreas Menzel (U Dortmund / Lund University)<br />
We present a novel approach for the simulation of <strong>solid</strong> to <strong>solid</strong> phase-transformations <strong>in</strong> polycrystall<strong>in</strong>e<br />
materials. To facilitate the utilization of a non-aff<strong>in</strong>e micro-sphere formulation with<br />
volumetric-deviatoric split, we <strong>in</strong>troduce Helmholtz free energy functions depend<strong>in</strong>g on volumetric<br />
and deviatoric stra<strong>in</strong> measures for the underly<strong>in</strong>g scalar-valued phase-transformation model.<br />
As an extension of aff<strong>in</strong>e micro-sphere models [3], the non-aff<strong>in</strong>e micro-sphere formulation with<br />
volumetric-deviatoric split allows to capture different Young’s moduli and Poisson’s ratios on the<br />
macro-scale [1]. As a consequence, the temperature-dependent free energy assigned to each <strong>in</strong>dividual<br />
phase takes the form of an elliptic paraboloid <strong>in</strong> volumetric-deviatoric stra<strong>in</strong> space, where<br />
the energy landscape of the overall material is obta<strong>in</strong>ed from the contributions of the <strong>in</strong>dividual<br />
constituents.<br />
For the evolution of volume fractions, we use an approach based on statistical physics—tak<strong>in</strong>g<br />
<strong>in</strong>to account actual Gibbs energy barriers and transformation probabilities [2]. The computation<br />
of <strong>in</strong>dividual energy barriers between the phases considered is enabled by numerical m<strong>in</strong>imization<br />
of parametric <strong>in</strong>tersection curves of elliptic Gibbs energy paraboloids. The framework provided<br />
facilitates to take <strong>in</strong>to account an arbitrary number of <strong>solid</strong> phases of the underly<strong>in</strong>g material,<br />
though we restrict ourselves to the simulation of three phases, namely an austenitic parent phase<br />
and a martensitic tension and compression phase. It is shown that the model presented nicely<br />
reflects the temperature-dependent effects of pseudo-elasticity and pseudo-plasticity, and thus<br />
captures experimentally observed behaviour at different temperatures.
14 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
[1] I. Carol and Z. Bažant, Damage and plasticity <strong>in</strong> microplane theory, Int. J. Sol. Struct. 34,<br />
3807–3835 (1997)<br />
[2] S. Gov<strong>in</strong>djee and G.J. Hall, A computational model for shape memory alloys, Int. J. Sol.<br />
Struct. 37, 735–760 (2000)<br />
[3] R. Ostwald, T. Bartel and A. Menzel, A computational micro-sphere model applied to the<br />
simulation of phase-transformations, J. Appl. Math. Mech. 90(7-8), 605–622 (2010)<br />
S6.6: Elasticity, Viscoelasticity, -plasticity I Wed, 13:30–15:30<br />
Chair: Merab Svanadze, Daniel Balzani S1|01–A1<br />
Thermoviscoplasticity deduced from enhanced rheological models<br />
Christoph Bröcker, Anton Matzenmiller (Universität Kassel)<br />
In the concept of rheological models, basic elements like spr<strong>in</strong>gs (ideal elastic), dashpots (ideal<br />
viscous) or friction elements (ideal plastic) are assembed to networks for represent<strong>in</strong>g complex<br />
material behaviour [1]. In case of viscoelastic material models, the phenomenological constitutive<br />
equations are usually deduced directly from a rheological network. However, <strong>in</strong> the case of elastoplasticity,<br />
the rheological models are often used only to visualise the fundamental structure of<br />
the related material model.<br />
In the presentation, a new ideal body is def<strong>in</strong>ed for isotropic harden<strong>in</strong>g besides m<strong>in</strong>or modifications<br />
of some well–known basic elements from the literature [2, 3]. Hence, a rheological model of<br />
thermoviscoplasticity may be assembled with l<strong>in</strong>ear isotropic and k<strong>in</strong>ematic harden<strong>in</strong>g and nonl<strong>in</strong>ear<br />
stra<strong>in</strong> rate sensitivity. The related constitutive equations <strong>in</strong>clud<strong>in</strong>g the yield function and the<br />
flow rule are directly deduced from the k<strong>in</strong>ematics and the stress equilibrium of the rheological<br />
network and results <strong>in</strong> a well–known model. By evaluat<strong>in</strong>g the dissipation <strong>in</strong>equality, the heat<br />
conduction equation is obta<strong>in</strong>ed with the dissipative power term, driven by plastic deformations.<br />
Moreover, nonl<strong>in</strong>ear isotropic and k<strong>in</strong>ematic harden<strong>in</strong>g as well as an improved description<br />
of energy storage and dissipation are accomplished by <strong>in</strong>troduc<strong>in</strong>g several additional dissipative<br />
stra<strong>in</strong> elements <strong>in</strong>to the viscoplastic arrangement of the rheological model [see also 4], which<br />
corresponds to a generalization of an ideal body already used <strong>in</strong> [2, 3]. Aga<strong>in</strong>, the constitutive<br />
equations may be deduced from the rheological network, its k<strong>in</strong>ematics, and the stress equilibrium.<br />
For that purpose, however, the dissipation <strong>in</strong>equality has to be utilized.<br />
[1] M. Re<strong>in</strong>er, Rheologie <strong>in</strong> elementarer Darstellung, Carl Hanser Verlag, 1969.<br />
[2] A. Krawietz, <strong>Material</strong>theorie, Spr<strong>in</strong>ger, 1986.<br />
[3] A. Lion, Constitutive <strong>modell<strong>in</strong>g</strong> <strong>in</strong> f<strong>in</strong>ite thermoviscoplasticity: a physical approach based on<br />
nonl<strong>in</strong>ear rheological models, Int. J. Plast. 16 (2000), 469–494.<br />
[4] A. Matzenmiller, C. Bröcker, Modell<strong>in</strong>g and simulation of coupled thermoplastic and thermoviscous<br />
structur<strong>in</strong>g and form<strong>in</strong>g processes, In: Maier et al. (eds.): Functionally graded<br />
materials <strong>in</strong> <strong>in</strong>dustrial mass production, Verlag Wissenschaftliche Skripten, Auerbach, 2009,<br />
235–250.
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 15<br />
Steady vibrations problems <strong>in</strong> the theory of viscoelasticity for Kelv<strong>in</strong>-Voigt materials<br />
with voids<br />
Maia M. Svanadze (Universität Gött<strong>in</strong>gen)<br />
Viscoelastic materials play an important role <strong>in</strong> many branches of eng<strong>in</strong>eer<strong>in</strong>g, technology and<br />
bio<strong>mechanics</strong>. The modern theories of viscoelasticity and thermoviscoelasticity for materials with<br />
microstructure have been a subject of <strong>in</strong>tensive study <strong>in</strong> recent years. Recently, the theory of<br />
thermoviscoelastic materials with voids is constructed by Iesan (2011).<br />
In this paper the l<strong>in</strong>ear theory of viscoelasticity for Kelv<strong>in</strong>-Voigt materials with voids is considered<br />
and the basic <strong>in</strong>ternal and external boundary value problems of steady vibrations are <strong>in</strong>vestigated.<br />
The formulae of <strong>in</strong>tegral representations of regular vectors are obta<strong>in</strong>ed. The s<strong>in</strong>gle-layer,<br />
double-layer and volume potentials are constructed and their basic properties are established.<br />
The uniqueness and existence of regular solutions of the boundary value problems are proved by<br />
means of the potential method.<br />
Modell<strong>in</strong>g of predeformation- and frequency-dependent material behavior of filled<br />
rubber under large predeformations superimposed with harmonic deformations of<br />
small amplitudes<br />
D. Wollscheid, A. Lion (Universität der Bundeswehr München)<br />
Viscoelastic materials show a frequency- and predeformation-dependent behavior under load<strong>in</strong>gs<br />
that consist of large predeformations with superimposed harmonic deformations of small amplitudes.<br />
In order to consider this materialbehavior, some static and dynamic experiments are<br />
developed. Based on Haupt & Lion [1] and Lion, Retka & Rendek [2] we <strong>in</strong>troduce a recently<br />
developed constitutive approach of f<strong>in</strong>ite viscoelasticity <strong>in</strong> the frequency doma<strong>in</strong> that is able to<br />
describe the frequency- and predeformation-dependent materialbehavior with respect to storageand<br />
loss-modulus. The constitutive equations are evaluated <strong>in</strong> the frequency doma<strong>in</strong> and geometrically<br />
l<strong>in</strong>earized <strong>in</strong> the neighbourhood of the predeformation. Furthermore a formulation for<br />
<strong>in</strong>compressible material behavior is <strong>in</strong>troduced and the correspond<strong>in</strong>g dynamic modulus tensors<br />
are derived. Besides constitutive <strong>modell<strong>in</strong>g</strong> and experiments, parameter identification and some<br />
numerical simulations are presented.<br />
[1] P. Haupt, A. Lion, On f<strong>in</strong>ite l<strong>in</strong>ear viscoelasticity of <strong>in</strong>compressible isotropic materials, Acta<br />
Mechanica 159 (2002), 87 – 124.<br />
[2] A. Lion, J.Retka, M.Rendek On the calculation of predeformation-dependent dynamic modulus<br />
tensors <strong>in</strong> f<strong>in</strong>ite nonl<strong>in</strong>ear viscoelasticity, Mechanics Research Communications 36<br />
(2009), 653 – 658.<br />
A multi-scale <strong>modell<strong>in</strong>g</strong> approach for bitum<strong>in</strong>ous asphalt<br />
Thorsten Schüler, Ralf Jänicke, Holger Steeb (Universität Bochum)<br />
Bitum<strong>in</strong>ous asphalt is a standard material e.g. <strong>in</strong> road constructions. However, the term asphalt<br />
<strong>in</strong>volves an extremly broad class of complex multi-scale and multi-phase materials. Typically,<br />
asphalt consists of a m<strong>in</strong>eral filler (e.g. crushed rock), a bitum<strong>in</strong>ous b<strong>in</strong>d<strong>in</strong>g agent (possibly <strong>in</strong>clud<strong>in</strong>g<br />
further additive compounds) and pores. The various constituents are to be adapted for<br />
the particular application.<br />
Nowadays, requirements on noise reduction of road constructions become more and more important.<br />
In our ongo<strong>in</strong>g research activities, we focus on the <strong>solid</strong>-borne acoustic properties of the
16 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
asphalt cover layer, i.e. the top layer of the entire asphalt-construction. In order to predict the<br />
macro-scale effective material properties of asphalt we apply a numerical homogenisation scheme<br />
based on volume averag<strong>in</strong>g techniques. The ma<strong>in</strong> advandtage of this numerical approach is, that<br />
the effective material properties can be determ<strong>in</strong>ed <strong>in</strong> knowledge of the micro-scale properties.<br />
Hence, the first step towards an overall model for bitum<strong>in</strong>ous asphalt is the quantification of<br />
the micro-scale mechanical properties. Aga<strong>in</strong>st the background of <strong>solid</strong>-borne acoustical properties<br />
we restrict ourselves to a geometrically l<strong>in</strong>ear description <strong>in</strong>volv<strong>in</strong>g only small deformations<br />
on both, macro- and micro-scale. Do<strong>in</strong>g so, the l<strong>in</strong>ear-elastic properties of the stiff, granular filler<br />
can be adopted from relevant literature. The viscoelastic behaviour of the bitum<strong>in</strong>ous phase is<br />
characterized by rheological experiments (dynamic shear rheometer with plate-plate geometry).<br />
The numerical implementation on the micro-scale is realized us<strong>in</strong>g a generalized Zener model (3d).<br />
Mak<strong>in</strong>g use of the numerical homogenization approach, the effective viscoelastic properties on<br />
the macro-scale are <strong>in</strong>vestigated with<strong>in</strong> transient experiments (relaxation/creep test). In particular<br />
we are <strong>in</strong>terested <strong>in</strong> the particular relaxation mechanisms and the related characteristic frequencies<br />
to be observed on the macro-scale. The <strong>in</strong>fluence of micro-scale boundary conditions will be<br />
taken <strong>in</strong>to account. In order to study the <strong>in</strong>teraction between micro-constituents as well as their<br />
geometrical morphology on the one hand and the effective viscoelastic properties on the other,<br />
we <strong>in</strong>troduce artificially produced periodic unit cells based on simplified geometries with vary<strong>in</strong>g<br />
volume and surface fractions of the m<strong>in</strong>eral filler.<br />
Jumps of the critical track<strong>in</strong>g load<strong>in</strong>gs for viscoelastic beams with vanisih<strong>in</strong>g <strong>in</strong>ternal<br />
viscosity<br />
S.A.Agafonov (Moscow State Technical University), D.V.Georgievskii (Moscow State University)<br />
Transverse vibrations of a viscoelastic beam under action of a track<strong>in</strong>g load<strong>in</strong>g are considered.<br />
The constitutive relation represents the follow<strong>in</strong>g non-l<strong>in</strong>ear connection of stress σ(t), stra<strong>in</strong> ε(t)<br />
and stra<strong>in</strong> rate ˙ε(t):<br />
σ = Eε +<br />
where E is the Young modulus, k (n)<br />
i<br />
N<br />
n<br />
n=1 i=1<br />
k (n)<br />
i ε2(n−i) ˙ε 2i−1 , N ≥ 1<br />
> 0 are the coefficients of <strong>in</strong>ternal viscosity.<br />
Analytical and numerical <strong>in</strong>vestigation of dynamic stability <strong>in</strong> case N = 3, k (1)<br />
1 = 0, k (2)<br />
1 = 0,<br />
k (1)<br />
2 = 0 shows that if k (3)<br />
α → 0 (k (3)<br />
β<br />
= 0, k(3)<br />
γ = 0; (α, β, γ) may be some permutation of (1, 2, 3))<br />
then three critical values of track<strong>in</strong>g load<strong>in</strong>g correspond<strong>in</strong>g to each nonzero coefficient of viscosity<br />
k (3)<br />
α less than the value for elastic system by a f<strong>in</strong>ite quantity.<br />
Numerical model<strong>in</strong>g of a non-l<strong>in</strong>ear viscous flow <strong>in</strong> order to determ<strong>in</strong>e how parameters<br />
<strong>in</strong> constitutive relations <strong>in</strong>fluence the entropy production<br />
Wolfgang H. Müller, B. Emek Abali (TU Berl<strong>in</strong>)<br />
Some rheological materials like melt<strong>in</strong>g polymers, cosmetic creams, ketchup, toothpaste can be<br />
modeled as non-Newtonian fluids by us<strong>in</strong>g a non-l<strong>in</strong>ear constitutive relation. Flow of this k<strong>in</strong>d<br />
of amorphous matter can be considered as a thermodynamic process, and a solution of pressure,<br />
velocity and temperature fields describe it fully. S<strong>in</strong>ce flow processes are generally irreversible,<br />
entropy is produced lead<strong>in</strong>g to dissipation <strong>in</strong> the system. This energy loss can be measured<br />
<strong>in</strong>directly <strong>in</strong> a cone/plate viscometer which is used to determ<strong>in</strong>e viscosity of a B<strong>in</strong>gham fluid.<br />
While dissipation is a measurable quantity we want to be able to calculate it. Thus the goal of<br />
this work is to expla<strong>in</strong> how to calculate entropy production us<strong>in</strong>g balance equations <strong>in</strong> a spatial
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 17<br />
frame.<br />
Start<strong>in</strong>g from balance of mass, l<strong>in</strong>ear momentum, <strong>in</strong>ternal energy and employ<strong>in</strong>g method<br />
of weighted residuals, we get a non-l<strong>in</strong>ear coupled set of partial differential equations <strong>in</strong> space<br />
and time. A space discretization <strong>in</strong> f<strong>in</strong>ite elements method and a time discretization <strong>in</strong> f<strong>in</strong>ite<br />
difference method leads to an approximation after a successful l<strong>in</strong>earization. We achieve to solve<br />
the problem without any stabilization or usage of specific type of elements and show here the<br />
entropy production and its variation subject to material parameters for the sake of a better<br />
<strong>in</strong>tuitive understand<strong>in</strong>g of dissipation. This may lead to an <strong>in</strong>verse problem where the calculated<br />
dissipation is measured and material parameters are determ<strong>in</strong>ed out of it, which is left to future<br />
research.<br />
S6.7: Phase Transformations II Wed, 16:00–18:00<br />
Chair: Wolfgang Dreyer S1|01–A03<br />
Nons<strong>in</strong>gular Dislocation Loops <strong>in</strong> Gradient Elasticity<br />
Markus Lazar (TU Darmstadt)<br />
This work studies the fundamental problem of nons<strong>in</strong>gular dislocations <strong>in</strong> the framework of the<br />
theory of gradient elasticity. A general theory of nons<strong>in</strong>gular dislocations is developed for l<strong>in</strong>early<br />
elastic, <strong>in</strong>f<strong>in</strong>itely extended, homogeneous, isotropic media. Us<strong>in</strong>g gradient elasticity, we give the<br />
nons<strong>in</strong>gular fields produced by arbitrary dislocation loops. We present the ‘modified’ Mura, Peach-<br />
Koehler and Burgers formulae <strong>in</strong> the framework of gradient elasticity theory. These formulae are<br />
given <strong>in</strong> terms of an elementary function, which regularizes the classical expressions, obta<strong>in</strong>ed<br />
from the Green tensor of generalized Navier equations. Us<strong>in</strong>g the mathematical method of Green’s<br />
functions and the Fourier transform, we found exact, analytical and nons<strong>in</strong>gular solutions. The<br />
obta<strong>in</strong>ed dislocation fields are nons<strong>in</strong>gular due to the regularization of the classical s<strong>in</strong>gular fields.<br />
On a paradox with<strong>in</strong> the phase field model<strong>in</strong>g of storage systems and its resolution<br />
Clemens Guhlke, Wolfgang Dreyer (WIAS Berl<strong>in</strong>)<br />
We study two import storage problems: The storage of lithium <strong>in</strong> an electrode of a lithium-ion<br />
battery and the storage of hydrogen <strong>in</strong> hydrides.<br />
When foreign atoms are reversibly stored <strong>in</strong> a crystal, there may be a regime where two coexist<strong>in</strong>g<br />
phases with low and high concentration of the stored atoms occur. Furthermore hysteretic<br />
behavior can be observed, i.e. the processesof load<strong>in</strong>g and unload<strong>in</strong>g follow different paths.<br />
We apply a viscous Cahn-Hilliard model with mechanical coupl<strong>in</strong>g to calculate the voltagecharge<br />
diagram of the battery, respectively the pressure-charge diagram of a hydrogen system.<br />
The diagrams exhibit phase transition and hysteresis. However, we show that the model can only<br />
describe the observed phenomena for fast but nor for slow load<strong>in</strong>g.<br />
We relate the reason for failure to the microstructure of modern storage systems. In fact these<br />
consist of an ensemble of nano-sized <strong>in</strong>terconnected storage particle. Each particle is described by<br />
a non-monotone chemical potential function but on the time scale of slow load<strong>in</strong>g of the ensemble,<br />
the coexist<strong>in</strong>g phases are unstable with<strong>in</strong> an <strong>in</strong>dividual particle and cannot be observed on the<br />
time scale of the load<strong>in</strong>g.<br />
In the slow load<strong>in</strong>g regime, the occurence of two coexist<strong>in</strong>g phases phases is a many-particle<br />
effect of the ensemble. The nucleation and evolution of the phases is embodied by a nonlocal<br />
conservation law of Fokker-Planck type.<br />
Numerical Simulation of Coarsen<strong>in</strong>g <strong>in</strong> Metallic Alloys<br />
Uli Sack, Carsten Gräser, Ralf Kornhuber (FU Berl<strong>in</strong>)
18 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
Phase separation phenomena <strong>in</strong> alloys, such as sp<strong>in</strong>odal decomposition and Ostwald ripen<strong>in</strong>g<br />
can be described by phasefield models of Cahn-Hilliard-type. Realistic models based on thermodynamically<br />
correct logarithmic free energies conta<strong>in</strong> highly nonl<strong>in</strong>ear and s<strong>in</strong>gular terms as<br />
well as drastically vary<strong>in</strong>g length scales (cf. [1]). We present a globally convergent nonsmooth<br />
Schur-Newton Multigrid method for vector-valued Cahn-Hilliard-type equations ([2, 3]) and a<br />
numerical study of coarsen<strong>in</strong>g <strong>in</strong> a b<strong>in</strong>ary eutectic AgCu alloy tak<strong>in</strong>g <strong>in</strong>to account elastic effects.<br />
Vector-valued Cahn-Hilliard computations open the perspective to multicomponent simulations.<br />
[1] W. Dreyer, W.H. Müller, F. Duderstadt and T. Böhme, “Higher Gradient Theory of Mixtures”,<br />
WIAS-Prepr<strong>in</strong>t No 1286 (2008)<br />
[2] C. Gräser and R. Kornhuber, “Nonsmooth Newton Methods for Set-valued Saddle Po<strong>in</strong>t<br />
Problems”, SIAM J. Numer. Anal. (2009) 47 (2)<br />
[3] C. Gräser, R. Kornhuber, “Schur-Newton Multigrid Methods for Vector-Valued Cahn–Hilliard<br />
Equations”, <strong>in</strong> prep<br />
A Phase Field Model for Martensitc Transformations<br />
Reg<strong>in</strong>a Schmitt, Ralf Müller, Charlotte Kuhn (TU Kaiserslautern)<br />
Consider<strong>in</strong>g the microscopic level of steel, there are different structures with different mechanical<br />
properties. Under mechanical deformation the metastable austenitic face-centered cubic phase<br />
transforms <strong>in</strong>to the tetragonal martensitic phase at which transformation <strong>in</strong>duced eigenstra<strong>in</strong><br />
arises. On the other hand, the mircostructure affects the macroscopic mechanical behavior of<br />
the specimen. In order to take the complex <strong>in</strong>teractions <strong>in</strong>to account, a phase field model for<br />
martensitic transformation is developed. With<strong>in</strong> the phase field approach, an order parameter<br />
is <strong>in</strong>troduced to <strong>in</strong>dicate different material phases. Its time derivative is assumed to follow the<br />
time-dependent G<strong>in</strong>zburg-Landau equation. The coupled field equations are solved us<strong>in</strong>g f<strong>in</strong>ite<br />
elements together with an implicit time <strong>in</strong>tegration scheme. With the aid of this model, the effects<br />
of the elastic stra<strong>in</strong> m<strong>in</strong>imization on the formation of microstructure can be studied so that the<br />
evolution of the martensitic phase is predictable. The applicability of the model is illustrated<br />
through different numerical examples.<br />
Investigation of the stra<strong>in</strong> localization behavior with application of the phase transition<br />
approach<br />
M. Ievdokymov, H. Altenbach, V.A. Eremeyev (Universität Magdeburg)<br />
Metal foams found recently many applications <strong>in</strong> civil, airspace and mechanical eng<strong>in</strong>eer<strong>in</strong>g. In<br />
particular, foams have a good energy absorption property. This property relates to the phenomenon<br />
of localization of stra<strong>in</strong>s <strong>in</strong> foams under load<strong>in</strong>g. In porous materials the localization of<br />
stra<strong>in</strong>s leads to change of mass density of material and appearance of areas with low and high<br />
densities separated by sharp <strong>in</strong>terface. This behavior is similar to the phase transitions <strong>in</strong> <strong>solid</strong>s<br />
with sharp <strong>in</strong>terfaces.<br />
In this paper we use the methods of <strong>modell<strong>in</strong>g</strong> of phase transitions <strong>in</strong> <strong>solid</strong>s to the description of<br />
stra<strong>in</strong> localization <strong>in</strong> foams. We assume that the foam consist of two phases with different densities<br />
and mechanical properties. The results of <strong>modell<strong>in</strong>g</strong> of one- and two-dimensional problems are<br />
discussed. The calculations are performed by Abaqus and script language Python.<br />
S6.8: Elasticity, Viscoelasticity, -plasticity II Wed, 16:00–18:00<br />
Chair: Ismail Caylak S1|01–A1
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 19<br />
A New Cont<strong>in</strong>uum Approach to the Coupl<strong>in</strong>g of Shear Yield<strong>in</strong>g and Craz<strong>in</strong>g with<br />
Fracture <strong>in</strong> Glassy Polymers<br />
Lisa Schänzel, Christian Miehe (Universität Stuttgart)<br />
Over the past decades, considerable effort was made to develop constitutive models that account<br />
for f<strong>in</strong>ite viscoplasticity and failure <strong>in</strong> glassy polymers. Recently, we developed a new model<br />
of ductile thermoviscoplasticity of glassy polymers <strong>in</strong> the logarithmic stra<strong>in</strong> space [1]. However,<br />
depend<strong>in</strong>g on thermal and load<strong>in</strong>g rate conditions to which the material is subjected, the response<br />
might change from ductile to brittle. This brittle response is characterized by <strong>in</strong>elastically deformed<br />
zones, so-called crazes, hav<strong>in</strong>g the thickness of micrometers and spann<strong>in</strong>g at some fractions of<br />
a millimeter [2]. The craz<strong>in</strong>g is associated with considerable dilatational plasticity, conta<strong>in</strong><strong>in</strong>g a<br />
dense array of fibrils <strong>in</strong>terspersed with elongated voids. The shear yield<strong>in</strong>g and craz<strong>in</strong>g are not<br />
completely <strong>in</strong>dependent exclud<strong>in</strong>g each other. In this lecture, we outl<strong>in</strong>e an extension of the ductile<br />
plasticity model [1] towards the description of (i) volumetric directional plasticity effect due to<br />
craz<strong>in</strong>g and (ii) the model<strong>in</strong>g of the local failure due to fracture. To this end, the first extension<br />
accounts for a (i) dilatational plastic deformation mechanism <strong>in</strong> the direction of the maximum<br />
pr<strong>in</strong>ciple tensile stress. The ultimate amount of this volumetric plastic craze stra<strong>in</strong> is bounded<br />
by a limit<strong>in</strong>g value, where failure occurs. Then, <strong>in</strong> a second step, the (ii) model<strong>in</strong>g of subsequent<br />
failure mechanisms is realized by the <strong>in</strong>troduction of a fracture phase field, characteriz<strong>in</strong>g via an<br />
auxiliary variable the crack topology. Here, we adopt structures of a recently developed cont<strong>in</strong>uum<br />
phase field model of fracture <strong>in</strong> brittle <strong>solid</strong>s [3], and modify it for a fracture driv<strong>in</strong>g term related<br />
to the volumetric plastic deformation of the crazes. We demonstrate the performance of proposed<br />
formulation by means of representative boundary value problems.<br />
[1] Miehe, C.; Mendez, J.; Göktepe, S.; Schänzel, L. [2011]: Coupled thermoviscoplasticity of<br />
glassy polymers <strong>in</strong> the logarithmic stra<strong>in</strong> space based on the free volume theory. International<br />
Journal of Solids and Structures, 48: 1799–1817.<br />
[2] Kramer, E. J.[1983]:Microscopic and Molecular Fundamentals of Craz<strong>in</strong>g. Advances <strong>in</strong> Polymer<br />
Science, 52/53: 1–56.<br />
[3] Miehe, C; Hofacker, M.; Welsch<strong>in</strong>ger, F. [2010]: A phase field model for rate-<strong>in</strong>dependent<br />
crack propagation: Robust algorithmic implementation based on operator splits. Computer<br />
Methods <strong>in</strong> Applied Mechanics and Eng<strong>in</strong>eer<strong>in</strong>g, 199: 2765-2778.<br />
Anisotropic f<strong>in</strong>ite stra<strong>in</strong> hyperelasticity based on the multiplicative decomposition of<br />
the deformation gradient<br />
Raad Al-K<strong>in</strong>ani, Kaveh Talebam, Stefan Hartmann (TU Clausthal)<br />
Frequently, the case of f<strong>in</strong>ite stra<strong>in</strong> anisotropy, particularly, the case of transversal isotropy, is<br />
applied to biological applications or to model fiber-re<strong>in</strong>forced composite materials. In this article<br />
the multiplicative decomposition of the deformation gradient <strong>in</strong>to one part constra<strong>in</strong>ed <strong>in</strong> the direction<br />
of the axis of anisotropy and one part describ<strong>in</strong>g the rema<strong>in</strong><strong>in</strong>g deformation is proposed.<br />
Accord<strong>in</strong>gly, a form of additively decomposed stra<strong>in</strong>-energy function is proposed. This leads to a<br />
clear assignment of deformation and stress states <strong>in</strong> the direction of anisotropy and the rema<strong>in</strong><strong>in</strong>g<br />
part. The decomposition of the case of transversal isotropy is expla<strong>in</strong>ed. The behavior of the<br />
model is <strong>in</strong>vestigated at different simple analytical examples, such as uniaxial tension along and<br />
perpendicular to the axis of anisotropy, and simple shear. In addition, the model is also studied for<br />
the case of a thick-walled tube under <strong>in</strong>ternal pressure, where a second order ord<strong>in</strong>ary differential
20 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
equation (two-po<strong>in</strong>t boundary-value problem) is obta<strong>in</strong>ed.<br />
Experimental characterization of the viscoelastic behaviour of discont<strong>in</strong>uous glass<br />
fibre re<strong>in</strong>forced thermoplastics<br />
B. Brylka, T. Böhlke (KIT)<br />
In automotive applications short and long glass fibre re<strong>in</strong>forced thermoplastics are commonly used<br />
for non-structural parts. Due the versatile possibilities of manufactur<strong>in</strong>g, form<strong>in</strong>g, jo<strong>in</strong><strong>in</strong>g and<br />
recycl<strong>in</strong>g, thermoplastic matrix based composites are <strong>in</strong>creas<strong>in</strong>gly used also for semi-structural<br />
parts. Thermoplastics like e.g. polypropylene show a high temperature and stra<strong>in</strong>-rate dependency,<br />
especially <strong>in</strong> the temperature and stra<strong>in</strong>-rate ranges which are relevant for automotive<br />
applications. Additionally, the non-l<strong>in</strong>ear <strong>in</strong>fluence of the viscoelastic behaviour of the matrix<br />
material on the effective material behaviour of the composite is of high <strong>in</strong>terest.<br />
The dynamic mechanical analysis (DMA) technique is an effective method to <strong>in</strong>vestigate the<br />
elastic and viscoelastic stiffness response of materials under cyclic load<strong>in</strong>g. After a short <strong>in</strong>troduction<br />
<strong>in</strong>to the DMA technique, experimental results for a polypropylene and polypropylene based<br />
composite material will be presented. The composite under consideration is an discont<strong>in</strong>uous glass<br />
fibre re<strong>in</strong>forced polypropylene. In the manufactur<strong>in</strong>g process, which is commonly compression or<br />
<strong>in</strong>jection mould<strong>in</strong>g, the flow of the mould <strong>in</strong>duces an heterogeneous and anisotropic distribution<br />
of fibre orientations. Therefore, the effective properties as well as the temperature and stra<strong>in</strong>-rate<br />
dependency has been <strong>in</strong>vestigated tak<strong>in</strong>g <strong>in</strong>to account an anisotropic material behaviour. The<br />
comparison of the elastic and viscoelastic material response of the matrix and the composite will<br />
be discussed <strong>in</strong> detail. Additionally, a parameter identification for common viscoelastic material<br />
models will be presented.<br />
[1] Middendorf, P.: Viskoelastisches Verhalten von Polymersystemen, Fortschritt-Berichte VDI,<br />
Reihe 5, VDI Verlag (2002).<br />
[2] Deng, S., Hou, M., Ye, L.: Temperature-dependent elastic moduli of epoxies measured by<br />
DMA and their correlations to mechanical test<strong>in</strong>g data, Polym. Test., 26, 803-813 (2007).<br />
[3] Schledjewski, R., Karger-Kocsis, J.: Dynamic mechanical analysis of glass mat-re<strong>in</strong>forced<br />
polypropylene (GMT-PP), J. Thermoplast. Compos., 7, 270-277 (1994).<br />
A <strong>solid</strong>-shell f<strong>in</strong>ite element for fibre re<strong>in</strong>forced composites<br />
J.-W. Simon, B. Stier, S. Reese (RWTH Aachen)<br />
Fibre re<strong>in</strong>forced composites are typically characterized by high Young’s modulus at low density,<br />
which makes them very attractive for lightweight constructions. The fibre composites considered<br />
here consist of several layers, each of which is composed of a woven fabric embedded <strong>in</strong> a matrix<br />
material. This structure makes the constitutive behavior of fibre composites anisotropic. Moreover,<br />
it is generally highly nonl<strong>in</strong>ear, and the materials’ response <strong>in</strong> tension and compression can<br />
differ significantly. In order to describe this rather complex behavior, we use a modification of<br />
a micromechanically motivated model proposed by Reese [1]. There<strong>in</strong>, an anisotropic model has<br />
been presented for the hyperelastic material behavior of membranes re<strong>in</strong>forced with roven-woven<br />
fibres, which is particularly suitable for the present fibre re<strong>in</strong>forced composites.<br />
The use of a fully three-dimensional material model strongly suggests us<strong>in</strong>g <strong>solid</strong> elements.<br />
On the other hand, fibre composites are mostly applied <strong>in</strong> th<strong>in</strong> shell-like structures, where shell
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 21<br />
elements should usually be preferred. Therefore, we use a <strong>solid</strong>-shell element presented by Schwarze<br />
and Reese [2] which comb<strong>in</strong>es the advantages of both <strong>solid</strong> elements and shell elements at the<br />
same time. This element allows for display<strong>in</strong>g realistically the three-dimensional geometry while<br />
still provid<strong>in</strong>g the suitable shape for th<strong>in</strong> structures.<br />
In addition, the present <strong>solid</strong>-shell formulation utilizes a reduced <strong>in</strong>tegration scheme with<strong>in</strong> the<br />
shell plane us<strong>in</strong>g one <strong>in</strong>tegration po<strong>in</strong>t, whereas a full <strong>in</strong>tegration is used <strong>in</strong> thickness direction.<br />
Thus, an arbitrary number of <strong>in</strong>tegration po<strong>in</strong>ts can be chosen over the shell thickness. Thereby,<br />
different fibre orientations of the layers can be taken <strong>in</strong>to account easily, s<strong>in</strong>ce the material<br />
parameters can be def<strong>in</strong>ed for each <strong>in</strong>tegration po<strong>in</strong>t separately.<br />
Moreover, the proposed <strong>solid</strong>-shell formulation removes all potential lock<strong>in</strong>g phenomena. In<br />
particular, volumetric lock<strong>in</strong>g <strong>in</strong> case of (nearly) <strong>in</strong>compressible materials as well as Poisson<br />
thickness lock<strong>in</strong>g <strong>in</strong> bend<strong>in</strong>g problems of shell-like structures are elim<strong>in</strong>ated by use of the enhanced<br />
assumed stra<strong>in</strong> (EAS) concept. In addition, to cure the transverse shear lock<strong>in</strong>g which is present<br />
<strong>in</strong> standard eight-node hexahedral elements, the assumed natural stra<strong>in</strong> (ANS) method is applied.<br />
[1] S. Reese. A micromechanically motivated material model for the thermo-viscoelastic material<br />
behaviour of rubber-like polymers, Int J Plast, 19, 909–940, 2003.<br />
[2] M. Schwarze, S. Reese. A reduced <strong>in</strong>tegration <strong>solid</strong>-shell f<strong>in</strong>ite element based on the EAS and<br />
the ANS concept - large deformation problems, Int J Numer Methods Engng, 85, 289–329,<br />
2011.<br />
On consistent tangent operator derivation and comparative study of rubber-like material<br />
models at f<strong>in</strong>ite stra<strong>in</strong>s<br />
Mokarram Hossa<strong>in</strong>, Paul Ste<strong>in</strong>mann (Universität Erlangen-Nürnberg)<br />
The overall micro-structure of rubber-like materials can be idealized by cha<strong>in</strong>-like macromolecules<br />
which are connected to each other at certa<strong>in</strong> po<strong>in</strong>ts via entanglements or cross-l<strong>in</strong>ks. Such<br />
special structure leads to a completely random three-dimensional network [2,3]. To model the<br />
mechanical behaviour of such randomly-oriented micro-structure, several phenomenological and<br />
micro-mechanically motivated network models for nearly <strong>in</strong>compressible hyperelastic polymeric<br />
materials have been proposed <strong>in</strong> the literature. To implement these models for polymeric material<br />
(undoubtedly with widespread eng<strong>in</strong>eer<strong>in</strong>g applications) <strong>in</strong> f<strong>in</strong>ite element method, one would<br />
require two important <strong>in</strong>gredients, e.g. the stress tensor and the consistent fourth-order tangent<br />
operator where the latter is the result of l<strong>in</strong>earization of the former.<br />
In this contribution, an extensive overview on several hyperelastic rubber-like material models<br />
has been presented. Special focus is given particularly to derive the accurate stress tensors and<br />
tangent operators which yield quadratic convergence when the govern<strong>in</strong>g nonl<strong>in</strong>ear equations for<br />
a boundary value problem are solved by the Newton-like iterative schemes. A simple but efficient<br />
algorithm will be demonstrated to testify the correctness of the tangent operator locally of a<br />
particular model without go<strong>in</strong>g <strong>in</strong>to details of the f<strong>in</strong>ite element implementation [1].<br />
[1] Ste<strong>in</strong>mann P, Hossa<strong>in</strong> M, Possart G (2011), Hyperelastic models for rubber-like materials:<br />
Consistent tangent operators and suitability for Treloar’s data. Archive of Applied Mechanics,<br />
In review (2011)<br />
[2] Boyce MC, Arruda EM (2000), Constitutive models of rubber elasticity: a review. Rubber<br />
Chemistry and Technology, 73: 504-523, 2000
22 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
[3] Marckmann G, Verron E (2006), Comparison of hyperelastic models for rubber-like materials.<br />
Rubber Chemistry and Technology, 79 (2006) 835-858<br />
Accelerat<strong>in</strong>g constitutive model<strong>in</strong>g by automatic tangent generation<br />
Steffen Rothe, Stefan Hartmann (TU Clausthal)<br />
Nowadays models become more and more complex. With<strong>in</strong> the framework of f<strong>in</strong>ite elements a<br />
material, i.e. consistent, tangent is required for the overall Newton-like method. Obta<strong>in</strong><strong>in</strong>g these<br />
derivatives is time consum<strong>in</strong>g and error-prone which contradicts to the goal of chang<strong>in</strong>g the model<br />
dur<strong>in</strong>g the develop<strong>in</strong>g process. On the one hand the calculation by hand can be very expensive<br />
and on the other hand also the implementation has to be done with high diligence. Therefore, a<br />
fast and safe way of consistent tangent generation will be presented with the help of automatic<br />
differentiation (AD) techniques.<br />
Analytical tangents have the advantage that they are exact. However dur<strong>in</strong>g the constitutive<br />
model<strong>in</strong>g process a change of the model is natural. Thus, the effort is very high to calculate<br />
the derivative after every modification. Numerical tangents computed by f<strong>in</strong>ite differences are<br />
easy to compute, but can lead to a significant slowdown or even to a failure of the simulation<br />
due to numerical errors. Tangents generated by OpenAD have no round-off errors and are easily<br />
computed by the help of automatic differentiation.<br />
These three methods (analytical, numerical and automatic differentiation) for tangent generation<br />
will be analyzed concern<strong>in</strong>g the simulation time and applicability for a number of different<br />
constitutive models.<br />
S6.9: Microheterogeneous <strong>Material</strong>s Thu, 13:30–15:30<br />
Chair: Johannes Schnepp, Eleni Agiasofitou S1|01–A03<br />
The boundary value problems of the full coupled theory of poroelasticity for materials<br />
with double porosity<br />
Merab Svanadze (Ilia State University, Tbilisi)<br />
Porous materials play an important role <strong>in</strong> many branches of eng<strong>in</strong>eer<strong>in</strong>g, e.g., the petroleum <strong>in</strong>dustry,<br />
chemical eng<strong>in</strong>eer<strong>in</strong>g, geo<strong>mechanics</strong>, and, <strong>in</strong> recent years, bio<strong>mechanics</strong>. The construction<br />
and the <strong>in</strong>tensive <strong>in</strong>vestigation of the theories of cont<strong>in</strong>ua with microstructures arise by the wide<br />
use of porous materials <strong>in</strong>to eng<strong>in</strong>eer<strong>in</strong>g and technology.<br />
The general 3D theory of poroelasticity for materials with s<strong>in</strong>gle porosity was formulated by<br />
Biot (1941). The double porosity model was first proposed by Barenblatt and coauthors (1960).<br />
The quasi-static theory of poroelasticity for materials with double porosity <strong>in</strong> the framework of<br />
mixture theory was presented by Aifantis and his co-workers (1982).<br />
In this paper the full coupled theory of poroelasticity for materials with double porosity is<br />
presented. This theory unifies the earlier proposed quasi-static model of Aifantis of con<strong>solid</strong>ation<br />
with double porosity. The boundary value problems (BVPs) of the steady vibrations are <strong>in</strong>vestigated.<br />
The fundamental solution of system of equations of steady vibrations is constructed. The<br />
basic properties of plane waves and the radiation conditions for regular vector are established. The<br />
uniqueness theorems of the <strong>in</strong>ternal and external BVPs of steady vibrations are proved. The basic<br />
properties of elastopotentials are established. The representation of general solution of equations<br />
of steady vibrations is obta<strong>in</strong>ed. The existence of regular solution of the BVPs by means of the<br />
boundary <strong>in</strong>tegral method and the theory of s<strong>in</strong>gular <strong>in</strong>tegral equations are proved.
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 23<br />
Application of an anisotropic growth and re<strong>modell<strong>in</strong>g</strong> formulation to computational<br />
topology optimisation<br />
Tobias Waffenschmidt (TU Dortmund), Andreas Menzel (TU Dortmund / Lund University)<br />
A classical topology optimisation problem consists of a problem-specific objective function which<br />
has to be m<strong>in</strong>imised <strong>in</strong> consideration of particular constra<strong>in</strong>ts with respect to design and state<br />
variables. In this contribution we present a conceptually different approach for the optimisation or<br />
rather improvement of the topology of a structure which is not based on a classical optimisation<br />
technique. Instead, we establish a constitutive micro-sphere-framework <strong>in</strong> comb<strong>in</strong>ation with an<br />
energy-driven anisotropic microstructural growth formulation, which was orig<strong>in</strong>ally proposed for<br />
the simulation of adaptation and re<strong>modell<strong>in</strong>g</strong> phenomena <strong>in</strong> hard biological tissues such as bones.<br />
The key aspect of this contribution is to <strong>in</strong>vestigate this anisotropic growth formulation with<br />
a special emphasis on its topology-optimis<strong>in</strong>g characteristics or rather topology-improv<strong>in</strong>g properties.<br />
To this end, several illustrative three-dimensional benchmark-type boundary value problems<br />
are discussed and compared qualitatively with the results obta<strong>in</strong>ed by classic topologyoptimisation<br />
strategies. The simulation results capture the densification effects and clearly identify<br />
the ma<strong>in</strong> load bear<strong>in</strong>g regions. It turns out, that even though mak<strong>in</strong>g use of this conceptually<br />
different growth formulation as compared to the procedures used <strong>in</strong> the more classic topologyoptimisation<br />
context, we identify qualitatively very similar topologies. Moreover, <strong>in</strong> contrast to<br />
common topology optimisation strategies, which mostly aim to optimise merely the structure,<br />
i.e. size, shape or topology, our formulation also conta<strong>in</strong>s the optimisation or improvement of the<br />
material itself, whichapart from the structural improvementresults <strong>in</strong> the generation of problemspecific<br />
local material anisotropy and textured evolution.<br />
Amplification damp<strong>in</strong>g properties of multiphase composites with spherical and fibers<br />
<strong>in</strong>clusions<br />
Sergey Lurie (Institute of Applied Mechanics, RAS), Natalia Tuchkova (Dorodnicyn Comput<strong>in</strong>g<br />
Centre, RAS), Juri Soliaev (Institute of Applied Mechanics, RAS)<br />
We consider composite materials re<strong>in</strong>forced with spherical and fibrous <strong>in</strong>clusions coated with a<br />
layer of lossy viscoelastic material. For the coat<strong>in</strong>g layers, typical viscoelastic properties of a polymer<br />
at and well above the glass transition region are assumed. It is shown that the remarkable loss<br />
amplification mechanism is also operative <strong>in</strong> such particulate-morphology materials. The aim of<br />
our study is to determ<strong>in</strong>e the effective loss modulus composites, which formally def<strong>in</strong>es the rate<br />
of energy dissipation per unit volume. We use a comb<strong>in</strong>ation of model<strong>in</strong>g and numerical tools<br />
to study composite materials consist<strong>in</strong>g of a matrix filled with spherical and fibrous <strong>in</strong>clusions<br />
coated with a layer of lossy viscoelastic material.<br />
The method of the four phases is used to describe the damp<strong>in</strong>g properties of composites<br />
filled with multiphase spherical <strong>in</strong>clusions and monolayer with multiphase fibrous <strong>in</strong>clusions. The<br />
constituent phases are supposed to be isotropic. Us<strong>in</strong>g the Eshelby method the effective moduli<br />
are determ<strong>in</strong>ed self-consistently, by requir<strong>in</strong>g that the average stra<strong>in</strong> <strong>in</strong> the composite <strong>in</strong>clusion<br />
is the same as the macroscopic stra<strong>in</strong> imposed at <strong>in</strong>f<strong>in</strong>ity. The analytical solution of this problem<br />
were received. The effective dynamic modulus and loss modulus were found us<strong>in</strong>g a viscoelastic<br />
analogy.<br />
It is shown[1] that the analytical give very similar, practically <strong>in</strong>dist<strong>in</strong>guishable predictions<br />
from the numerical solutions which were received us<strong>in</strong>g f<strong>in</strong>ite element method. Hence, when<br />
study<strong>in</strong>g such systems one can rely on the predictions of the four-phase sphere model, which<br />
are much easier to achieve than the f<strong>in</strong>ite element ones. a polymer at and well above the glass<br />
transition region are assumed. It is shown that by optimiz<strong>in</strong>g the thickness of the layers, one can<br />
achieve multiphase materials with effective loss characteristics significantly exceed<strong>in</strong>g those of the
24 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
<strong>in</strong>dividual materials constituents. It was found that for the considered composites have place the<br />
additional peak damp<strong>in</strong>g properties, which is realized for very small thicknesses of the viscoelastic<br />
phase. This peak is still about a factor 20 or so compared to the loss modulus of the pure matrix.<br />
We demonstrated that by <strong>in</strong>troduc<strong>in</strong>g th<strong>in</strong> layers of a viscoelastic material, one can significantly<br />
<strong>in</strong>crease the loss characteristics of discrete morphology multiphase materials. The layered fibers<br />
composites are also considered. It is shown that for such materials may be implemented at the<br />
same time as high elastic properties, and abnormally high damp<strong>in</strong>g properties.<br />
[1] A.A.Gusev , S.A. Lurie, Loss amplification effect <strong>in</strong> multiphase materials with viscoelastic<br />
<strong>in</strong>terfaces. Macromolecules (2009) 42,14, 5372 – 5377.<br />
Model<strong>in</strong>g of composite structural elements made from aramid fiber us<strong>in</strong>g the method<br />
of features objects<br />
Michał Majzner, Andrzej Baier (Silesian University of Technology)<br />
The use of modern materials such as composite materials, enabl<strong>in</strong>g the production of new or modify<strong>in</strong>g<br />
exist<strong>in</strong>g design solutions, improve their technical characteristics, while use <strong>in</strong> the process<br />
of design and eng<strong>in</strong>eer<strong>in</strong>g and manufactur<strong>in</strong>g, will allow the modification of endurance, physical<br />
and chemical properties to match the features and functionality that are comply with. In research<br />
studies, it is proposed to systematize and formalize elementary objects <strong>in</strong> the context of model<strong>in</strong>g<br />
and fabrication of objects created on the basis of structural fiber composites. Application of features<br />
objects methods was shows on an example of model<strong>in</strong>g the structural element, <strong>in</strong> the form<br />
of an exist<strong>in</strong>g manufactured from steel, which was modified and converted with aramid fiber. It<br />
was necessary to carry out research <strong>in</strong> the form of numerical analysis, exam<strong>in</strong><strong>in</strong>g the strength of<br />
the modified object.<br />
On the fibres shape effect for non-l<strong>in</strong>ear and unidirectional stationary heat conduction<br />
<strong>in</strong> two-phase hollow cyl<strong>in</strong>der with radially graded material properties<br />
Piotr Ostrowski (Technical University of Lodz)<br />
The ma<strong>in</strong> aim of this paper is to consider unidirectional and stationary heat conduction <strong>in</strong> the<br />
<strong>in</strong>fnite two-phase hollow cyl<strong>in</strong>der with temperature dependent material properties. The determ<strong>in</strong>istic<br />
microstructure of this composite is periodic (for a fixed radius) along the angular axis<br />
and has slowly vary<strong>in</strong>g effective properties <strong>in</strong> the radial direction. Therefore, we deal here with<br />
a special case of functionally graded materials, FGM, c.f. Suresh, Mortensen (1998). One of the<br />
components is called fibre, which is arranged <strong>in</strong> considered hollow cyl<strong>in</strong>der with circular pattern.<br />
The physical phenomenon of the heat transfer is described by well known Fourier’s equation<br />
c ˙ θ − ∇(K∇θ) = 0, (1)<br />
which conta<strong>in</strong>s temperature dependent (<strong>in</strong> this case), highly oscillat<strong>in</strong>g and discont<strong>in</strong>uous coefficients<br />
of K = K(θ) - heat conduction tensor, and c = c(θ) - specific heat. To this macroscopic<br />
model the tolerance averag<strong>in</strong>g approximation will be used, cf. Wozniak, Wierzbicki (2000). The<br />
general approach to the description of longitud<strong>in</strong>ally graded stratified media can be found <strong>in</strong><br />
[Wozniak, Michalak, Jedrysiak 2008]. The fibres width function g = g(r) of radius r will be exam<strong>in</strong>ed<br />
and its effects on the temperature field. The averaged differential equation has smooth<br />
and slowly vary<strong>in</strong>g coefficients, hence <strong>in</strong> some special cases, for boundary value problem, analytical<br />
solution can be obta<strong>in</strong>ed. In other cases, numerical methods have to be used. This model<br />
takes <strong>in</strong>to account the effect of microstructure size on the overall heat transfer behaviour.
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 25<br />
[1] S. SURESH, A. MORTENSEN, Fundamentals of functionally graded materials, Cambridge,<br />
The University Press, 1998.<br />
[2] Cz. WOZNIAK, B. MICHALAK, J. JEDRYSIAK (eds), Thermo<strong>mechanics</strong> of micro-heterogeneous<br />
<strong>solid</strong>s and structures. Tolerance averag<strong>in</strong>g approach, Wydawnictwo Politechniki Lodzkiej,<br />
Lodz, 2008.<br />
S6.10: Elasticity, Viscoelasticity, -plasticity III Thu, 13:30–15:30<br />
Chair: Daniel Balzani S1|01–A1<br />
Network evolution model: thermodynamics consistency, parameter identification and<br />
f<strong>in</strong>ite element implementation<br />
Vu Ngoc Khiêm, Roozbeh Dargazany, Mikhail Itskov (RWTH Aachen)<br />
In this contribution, the previously proposed network evolution model [1] for carbon black filled<br />
elastomers is further studied. First, we show that the model does not contradict the second law of<br />
thermodynamics and is thus thermodynamically consistent. On the basis of new experimental data<br />
the <strong>in</strong>fluence of filler concentration on the material parameters is further exam<strong>in</strong>ed. Accord<strong>in</strong>gly,<br />
this <strong>in</strong>fluence concerns only three material parameters and is approximated by phenomenological<br />
relations. These relations enable one to simulate rubbers based on the same compound with<br />
various filler concentrations. F<strong>in</strong>ally, the model is implemented to the FE-Software ABAQUS and<br />
illustrated by a number of numerical examples. The examples demonstrate good agreement with<br />
experimental results with respect to the Mull<strong>in</strong>s-Effect, permanent set and <strong>in</strong>duced anisotropy.<br />
[1] R. Dargazany and M. Itskov, A network evolution model for the anisotropic Mull<strong>in</strong>s effect<br />
<strong>in</strong> carbon black filled rubbers, International Journal of Solids and Structures 46 (2009),<br />
2967–2977.<br />
Shakedown analysis of periodic composites with k<strong>in</strong>ematic harden<strong>in</strong>g material model<br />
M<strong>in</strong> Chen, A. Hachemi, D. Weichert (RWTH Aachen)<br />
Lower-bound limit and shakedown analysis of periodic composites with the consideration of k<strong>in</strong>ematic<br />
harden<strong>in</strong>g are <strong>in</strong>vestigated on the representative volume element. With the comb<strong>in</strong>ation of<br />
homogenization theory, the homogenized macroscopic admissible load<strong>in</strong>g doma<strong>in</strong>s are evaluated.<br />
Furthermore, the strengths of periodic composites of elastic-perfectly plastic, unlimited and l<strong>in</strong>ear<br />
limited k<strong>in</strong>ematic harden<strong>in</strong>g material models are calculated and compared <strong>in</strong> this paper.<br />
Theory of mixture based material model<strong>in</strong>g - An <strong>in</strong>elastic material model for a 12%chromium<br />
steel<br />
Andreas Kutschke, Konstant<strong>in</strong> Naumenko, Holm Altenbach (Universität Magdeburg)<br />
Components composed of advanced heat resistant steels face a complex load<strong>in</strong>g of mechanical and<br />
thermal stresses under cyclic and long-term conditions. Additionally, a failure of these components<br />
usually has serious outcome, because of the extreme work<strong>in</strong>g conditions. From this follows the<br />
need of a reliable material model for the construction process.<br />
Classical technical guidel<strong>in</strong>es are historically grown and the experience of eng<strong>in</strong>eers contributed<br />
to their development, but it turns out that these classical guidel<strong>in</strong>es face their limit of use. Recently<br />
more sophisticated material models are developed to reach the real limit of the materials and to<br />
predict their behavior with more accuracy.
26 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
Start<strong>in</strong>g with the theoretical concept of Prandtl, who <strong>in</strong>troduced the idea of a harden<strong>in</strong>g<br />
substance <strong>in</strong> a material, and the <strong>in</strong>vestigations of Mughrabi, who established a composite model<br />
for chromium steels, the advanced steels are treated as a composition of at least two cont<strong>in</strong>ua, <strong>in</strong><br />
the sense of the theory of mixture.<br />
Therefore the general balance equations for a mixture will be presented. The example of a<br />
12% chromium steel will be used to illustrate this approach and to derive a material model for<br />
a mixture of two constituents. It will be shown that the model predicts tension-, compression-,<br />
cyclic-creep, uniaxial monotonic tension und low-cycle-fatigue load<strong>in</strong>g <strong>in</strong> a satisfy<strong>in</strong>g manner <strong>in</strong><br />
comparison with experimental results.<br />
Zur Abtragssimulation beim Strömungsschleifen (AFM)<br />
Joachim Schmitt, Stefan Diebels (Universität des Saarlandes)<br />
Im Zuge konkurrenzfähiger Produktionsverfahren werden seit e<strong>in</strong>igen Jahren schwer zugängliche<br />
Kanten im Inneren von komplex aufgebauten Fertigungsteilen (wie beispielsweise die Gehäuse von<br />
E<strong>in</strong>spritzanlagen) mittels des Strömungsschleifens (Abrasive flow mach<strong>in</strong><strong>in</strong>g - AFM) verrundet<br />
bzw. oberflächenvergütet. Dazu wird e<strong>in</strong>e mit Schleifpartikeln versetzte Silikonpaste mehrfach<br />
durch das Bauteil gepresst. Das viskose Verhalten der Paste ist dabei für die effektive Wirkung<br />
dieses Verfahrens sehr wichtig. Beim Überströmen von Kanten steigt die Schergeschw<strong>in</strong>digkeit und<br />
damit auch die Viskosität je nach <strong>Material</strong>modell überproportional an. Die so geänderten Druckund<br />
Geschw<strong>in</strong>digkeitsverhältnisse an der Bauteiloberfläche verändern auch den <strong>Material</strong>abtrag<br />
durch die Schleifpaste.<br />
Im Rahmen dieser Studie werden zunächst die viskosen Eigenschaften der Paste anhand von<br />
Experimenten untersucht und die Modellparameter bestimmt. Im zweiten Teil wird die Paste<br />
h<strong>in</strong>sichtlich ihrer abrasiven Eigenschaften vorgestellt und e<strong>in</strong>e Abschätzung des <strong>Material</strong>abriebs<br />
vorgenommen. E<strong>in</strong> daraus gebildetes e<strong>in</strong>faches Abtragsmodell wird mittels e<strong>in</strong>er FEM-Simulation<br />
an elementaren Bauteilgeometrien umgesetzt und qualitativ überprüft.<br />
<strong>Material</strong> parameter identification us<strong>in</strong>g model reduction to uniaxial tensile tests<br />
Stephan Krämer, Steffen Rothe, Stefan Hartmann (TU Clausthal)<br />
Uniaxial tensile tests are commonly used for material parameter identification. It is also common<br />
to use one-dimensional formulations of a constitutive model to identify the correspond<strong>in</strong>g<br />
material constants, although these material parameters are not necessarily identical to the material<br />
parameters <strong>in</strong> the three-dimensional material model. We present an easy way to reduce a<br />
three-dimensional material rout<strong>in</strong>e to the case of uniaxial tension and to use the reduced form<br />
to derive material parameters us<strong>in</strong>g common trust-region algorithms. With this approach one<br />
is able to use the full three-dimensional model for parameter identification. Instead of us<strong>in</strong>g a<br />
full f<strong>in</strong>ite element software, one is able to use the material driver rout<strong>in</strong>e, which leads to a more<br />
straight forward calculation of material parameters. In this respect, it is shown that the classical<br />
structure of stress algorithms and consistent tangent operators are necessary with<strong>in</strong> the threeto<br />
one-dimensional problem reduction. This procedure is also extendable to further homogeneous<br />
stress- and stra<strong>in</strong>-states.<br />
Systematic representation of the yield criteria for isotropic materials<br />
Vladimir A. Kolupaev (DKI Darmstadt), Holm Altenbach (Universität Magdeburg)<br />
The theory of plasticity operates with different flow criteria of <strong>in</strong>compressible material behavior.<br />
These criteria have hexagonal symmetry <strong>in</strong> the π-plane and do not dist<strong>in</strong>guish between tension<br />
and compression (non-SD-effect). Many tasks <strong>in</strong> the eng<strong>in</strong>eer<strong>in</strong>g practice are treated on the basis
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 27<br />
of these criteria and the flow rule.<br />
Selection of an appropriate criterion for a specific material is challeng<strong>in</strong>g. The models of Tresca<br />
and Schmidt-Ishl<strong>in</strong>sky, represent<strong>in</strong>g two regular hexagons <strong>in</strong> the π-plane, def<strong>in</strong>e accord<strong>in</strong>gly the<br />
lower and the upper limit of convexity. The criteria of Sokolovskij and Ishl<strong>in</strong>sky-Ivlev describe<br />
the regular dodecagons <strong>in</strong> the π-plane and have only geometrical mean<strong>in</strong>g. In difference to these<br />
four criteria, the model of von Mises has no s<strong>in</strong>gular corners and delivers unique results by the<br />
stra<strong>in</strong> rates calculation.<br />
The evaluation of the measurements shows that the material behavior differs from the idealized<br />
models. The models proposed by Drucker, Dodd-Naruse, Edelman-Drucker and Hershey aim to<br />
better adapt the flow surface. These models are the functions of one parameter. They have no<br />
claims on the generality and are used only for the approximation of the measurements.<br />
Three models with one parameter are known as generalized models: Unified Yield Criterion<br />
(UYC) of Yu, Bi-Cubic Model (BCM), and Multiplicative Ansatz (MA) [1]. These models <strong>in</strong>clude<br />
the models of Tresca and Schmidt-Ishl<strong>in</strong>sky. They allow approximat<strong>in</strong>g of exist<strong>in</strong>g measurements<br />
better than other models.<br />
This work compares the flow criteria. For this aim their geometries <strong>in</strong> the π-plane will be<br />
considered <strong>in</strong> polar coord<strong>in</strong>ates R and ϕ. The radii of the surface at the angles of ϕ = 15 and<br />
30 ◦ are related to the radius at ϕ = 0 ◦ : h = R(15 ◦ )/R(0 ◦ ), k = R(30 ◦ )/R(0 ◦ ). On the basis of<br />
these two relations, well-known criteria will be systematized and shown <strong>in</strong> the h − k–diagram.<br />
New criteria will be <strong>in</strong>troduced. The convexity limits for them will be stated.<br />
From the h−k–diagram, it is clear that UYC and MA set left and right boundary of convexity.<br />
Thus, the extreme solutions for parts can be found. The two models UYC and MA are the<br />
functions of the parameter k. The l<strong>in</strong>ear comb<strong>in</strong>ation of UYC and MA provides a universal model<br />
with two parameters k and ξ ∈ [0, 1] describ<strong>in</strong>g all convex surfaces of <strong>in</strong>compressible material<br />
behavior of hexagonal symmetry <strong>in</strong> the π-plane.<br />
The proposed consideration of the flow criteria simplifies the selection of the model and is<br />
suitable for didactic purposes. All known and new flow criteria can be described by universal<br />
model, and thus can be omitted.<br />
[1] Kolupaev, V. A., Altenbach, H.: Considerations on the unified strength theory due to Mao-<br />
Hong Yu, Forschung im Ingenieurwesen 74(3), (2010).<br />
S6.11: Special Methods <strong>in</strong> <strong>Material</strong> Model<strong>in</strong>g Thu, 16:00–18:00<br />
Chair: Bernhard Eidel, Markus Scholle S1|01–A03<br />
Model<strong>in</strong>g of Carbon Nanotubes by Molecular Mechanics<br />
Oliver Eberhardt, Thomas Wallmersperger (TU Dresden)<br />
Carbon Nanotubes (CNTs) are structures <strong>in</strong> the nanoscale consist<strong>in</strong>g of carbon atoms which are<br />
arranged <strong>in</strong> a hexagonal lattice. Hence, they can be imag<strong>in</strong>ed as a plane sheet of graphene rolled<br />
<strong>in</strong>to a seamless tube. By do<strong>in</strong>g so we obta<strong>in</strong> a so called S<strong>in</strong>gle Wall Carbon Nanotube (SWCNT).<br />
Besides S<strong>in</strong>gle Wall Carbon Nanotubes also Double Wall Carbon Nanotubes (DWCNT) and, <strong>in</strong><br />
general, Multi Wall Carbon Nanotubes (MWCNT) exist. Their high stiffness and active deformation<br />
of approx. 1 % at applied low electric voltages (approx. 1 V) make the Carbon Nanotubes a<br />
very promis<strong>in</strong>g material for applications e.g. <strong>in</strong> new classes of composites and actuators/sensors.<br />
In this research the approach to model Carbon Nanotubes is made by us<strong>in</strong>g molecular <strong>mechanics</strong>.<br />
The aim of these efforts is to determ<strong>in</strong>e the mechanical properties, for example the Young’s
28 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
modulus. The Molecular Mechanics method orig<strong>in</strong>ates <strong>in</strong> the <strong>in</strong>vestigation of the properties of<br />
big molecules which due to their size cannot be handled by quantum mechanical methods. In<br />
Molecular Mechanics the behavior of the covalent bonds <strong>in</strong> a S<strong>in</strong>gle Wall Carbon Nanotube is<br />
represented by a set of potentials. Here every s<strong>in</strong>gle potential expression describes a correspond<strong>in</strong>g<br />
bond deformation. As a result of the description of the bonds by potentials, the force act<strong>in</strong>g<br />
between the atoms can be calculated as the derivatives of the potentials with respect to their<br />
correspond<strong>in</strong>g displacement variable. Hence, the Carbon Nanotube is modeled by po<strong>in</strong>t masses<br />
represent<strong>in</strong>g the carbon atoms and a set of spr<strong>in</strong>gs or beam elements represent<strong>in</strong>g the bonds. Regard<strong>in</strong>g<br />
Multi Wall Carbon Nanotubes this model can be extended by add<strong>in</strong>g the van-der-Waals<br />
<strong>in</strong>teractions, described by another potential.<br />
Dur<strong>in</strong>g the process of model<strong>in</strong>g and also dur<strong>in</strong>g the evaluation of the results we have to rise<br />
several challenges. S<strong>in</strong>ce the Molecular Mechanics method is a so called semi-empiric method we<br />
have to choose between different sets of potentials. Some of these potentials - lead<strong>in</strong>g to l<strong>in</strong>ear<br />
or nonl<strong>in</strong>ear behavior of the <strong>in</strong>teraction forces between the atoms - are <strong>in</strong>vestigated regard<strong>in</strong>g<br />
their advantages and disadvantages. In order to illustrate this we compare the (theoretical) results<br />
available <strong>in</strong> literature with our numerical results, which we obta<strong>in</strong> by us<strong>in</strong>g the model to<br />
conduct a virtual tensile test. The dependance of the Young’s modulus on type and diameter of<br />
the Carbon Nanotubes is discussed.<br />
Dislocation Dynamics <strong>in</strong> Quasicrystals<br />
Eleni Agiasofitou, Markus Lazar (TU Darmstadt), Helmut Kirchner (Leibniz Institut für neue<br />
<strong>Material</strong>ien, Saarbrücken)<br />
In this work, we present a theoretical framework of dislocation dynamics <strong>in</strong> quasicrystals [1] accord<strong>in</strong>g<br />
to the cont<strong>in</strong>uum theory of dislocations. Quasicrystals have been discovered by Shechtman<br />
et al [2] <strong>in</strong> 1982 open<strong>in</strong>g a new <strong>in</strong>terdiscipl<strong>in</strong>ary research field. A comprehensive presentation of<br />
the current state of the art of this research field, focused on the mathematical theory of elasticity,<br />
can be found <strong>in</strong> the recently published book of Fan [3].<br />
We start present<strong>in</strong>g the fundamental theory of mov<strong>in</strong>g dislocations <strong>in</strong> quasicrystals giv<strong>in</strong>g<br />
the dislocation density tensors and <strong>in</strong>troduc<strong>in</strong>g the dislocation current tensors for the phonon<br />
and phason fields, <strong>in</strong>clud<strong>in</strong>g the Bianchi identities. In the literature, there exist different versions<br />
of generalized l<strong>in</strong>ear elasticity theory of quasicrystals. The difference of these versions lies <strong>in</strong> the<br />
dynamics of phonon and phason fields. In the present work, we deal with the elastodynamic as well<br />
as the elasto-hydrodynamic model of quasicrystals. Accord<strong>in</strong>g to the first model, the equations of<br />
motion are of wave-type for both phonons and phasons while accord<strong>in</strong>g to the second model the<br />
equations of motion for the phonons are equations of wave-type and for the phasons are equations<br />
of diffusion-type. Therefore, we give the equations of motion for the <strong>in</strong>compatible elastodynamics<br />
as well as for the <strong>in</strong>compatible elasto-hydrodynamics of quasicrystals.<br />
We cont<strong>in</strong>ue with the derivation of the balance law of pseudomomentum thereby obta<strong>in</strong><strong>in</strong>g<br />
the generalized forms of the Eshelby stress tensor, the pseudomomentum vector, the dynamical<br />
Peach-Koehler force density and the Cherepanov force density for quasicrystals. Moreover, we<br />
deduce the balance law of energy that gives rise to the generalized forms of the field <strong>in</strong>tensity<br />
vector and the elastic power density of quasicrystals. The above balance laws are produced for<br />
both models. The differences between the two models and their consequences are revealed. The<br />
<strong>in</strong>fluences of the phason fields as well as of the dynamical terms are also discussed.<br />
[1] E. Agiasofitou, M. Lazar and H. Kirchner, Generalized dynamics of mov<strong>in</strong>g dislocations <strong>in</strong><br />
quasicrystals, J. Phys.: Condens. Matter 22 (2010), 495401 (8pp).<br />
[2] D. Shechtman, I. Blech, D. Gratias and J. W. Cahn, Metallic phase with long-range orienta-
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 29<br />
tional order and no translational symmetry, Phys. Rev. Lett. 53 (1984), 1951 – 1953.<br />
[3] T. Fan, Mathematical Theory of Elasticity of Quasicrystals and its Applications, Science<br />
Press Beij<strong>in</strong>g and Spr<strong>in</strong>ger-Verlag Berl<strong>in</strong>, 2011.<br />
On <strong>in</strong>verse form f<strong>in</strong>d<strong>in</strong>g based on an ALE formulation<br />
Sandr<strong>in</strong>e Germa<strong>in</strong>, Paul Ste<strong>in</strong>mann (Universität Erlangen-Nürnberg)<br />
A challenge <strong>in</strong> the design of functional parts <strong>in</strong> form<strong>in</strong>g processes is the determ<strong>in</strong>ation of the<br />
<strong>in</strong>itial, undeformed shape such that under a given load a part will obta<strong>in</strong> the desired deformed<br />
shape. Two numerical methods might be used to solve this problem, which is <strong>in</strong>verse to the<br />
standard k<strong>in</strong>ematic analysis <strong>in</strong> which the undeformed shape is known and the deformed shape<br />
unknown.<br />
The first method deals with the formulation of an <strong>in</strong>verse mechanical problem, where the<br />
spatial (deformed) configuration and the mechanical loads are given. Hence the objective is to<br />
f<strong>in</strong>d the <strong>in</strong>verse deformation map that determ<strong>in</strong>es the (undeformed) material configuration.<br />
The second method deals with shape optimization that predicts the <strong>in</strong>itial shape <strong>in</strong> the sense<br />
of an <strong>in</strong>verse problem via successive iterations of the direct problem. In [1] a nodes-based shape<br />
optimization approach for elastoplastic materials based on logarithmic stra<strong>in</strong>s is presented. An<br />
update of the reference configuration is considered <strong>in</strong> order to avoid mesh distortions, which often<br />
occur <strong>in</strong> nodes-based optimization problems. The pr<strong>in</strong>cipal drawback is the high computational<br />
costs. An alternative is an Arbitrary-Lagrangian-Eulerian (ALE) formulation [2,3], which is neither<br />
purely Lagrangian (the nodes are not attached to the material) nor purely Eulerian (the nodes<br />
are not fixed <strong>in</strong> space). The nodes are free to move <strong>in</strong> space <strong>in</strong>dependently of the material.<br />
In this contribution we review the ALE formulation [2,3] for anisotropic hyperelastic materials<br />
and its application <strong>in</strong> shape optimization. Several examples illustrate the ALE approach <strong>in</strong><br />
hyperelasticity. Results and computational costs are compared with the ones obta<strong>in</strong>ed with the<br />
approach <strong>in</strong> [1].<br />
This work is supported by the German Research Foundation (DFG) with<strong>in</strong> the Collaborative<br />
Research Centre SFB Transregio 73.<br />
[1] S. Germa<strong>in</strong> and P. Ste<strong>in</strong>mann. Towards form f<strong>in</strong>d<strong>in</strong>g methods for a sheet-bulk-metal (DC04),<br />
15th ESAFORM, Key Eng<strong>in</strong>eer<strong>in</strong>g <strong>Material</strong>s submitted (<strong>2012</strong>).<br />
[2] E. Kuhl et al., An ALE formulation based on spatial and material sett<strong>in</strong>gs of cont<strong>in</strong>uum<br />
<strong>mechanics</strong>. Part 1: Generic hyperelastic formulation, Comput. Methods Appl. Mech. Engrg.<br />
193 (2004), 4207 – 4222.<br />
[3] H. Askes et al., An ALE formulation based on spatial and material sett<strong>in</strong>gs of cont<strong>in</strong>uum<br />
<strong>mechanics</strong>. Part 2: Classification and applications, Comput. Methods Appl. Mech. Engrg.<br />
193 (2004), 4223 – 4245.<br />
On the direct connection of rheological elements <strong>in</strong> nonl<strong>in</strong>ear cont<strong>in</strong>uum <strong>mechanics</strong><br />
Ralf Landgraf, Jörn Ihlemann (TU Chemnitz)<br />
The direct connection of rheological elements is a widely used concept to develop material models<br />
for one-dimensional deformation processes at small stra<strong>in</strong>s. This concept is based on the decomposition<br />
of the total stra<strong>in</strong> <strong>in</strong>to several subparts and the formulation of s<strong>in</strong>gle material laws for
30 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
idealized phenomena (e.g. nonl<strong>in</strong>ear elastic behaviour and viscous or plastic yield<strong>in</strong>g). Several<br />
of those elements are then assembled to one complex material model. This can be achieved by<br />
enforc<strong>in</strong>g the equilibrium of stresses on the connect<strong>in</strong>g po<strong>in</strong>ts between rheological elements.<br />
With<strong>in</strong> the scope of nonl<strong>in</strong>ear cont<strong>in</strong>uum <strong>mechanics</strong> there also exists the concept of rheological<br />
elements. The k<strong>in</strong>ematics is described by the deformation gradient which gets multiplicatively<br />
decomposed <strong>in</strong>to several sub deformation gradients. For the def<strong>in</strong>ition of the material behaviour,<br />
a common approach is to formulate a free energy function as a sum of sub free energy functions<br />
attributed to the def<strong>in</strong>ed sub deformation gradients. By the evaluation of the Clausius-Duhem<strong>in</strong>equality<br />
and under consideration of constitutive assumptions a system of equations describ<strong>in</strong>g<br />
a thermodynamically consistent material behaviour can be derived. Depend<strong>in</strong>g on particular def<strong>in</strong>itions,<br />
those materials can <strong>in</strong>clude a mixture of elastic, viscous and plastic material behaviour.<br />
An alternative approach has been presented by Ihlemann (2006). It is based on the additive<br />
decomposition of the stress power density and leads to a system of equations for the derivation<br />
of the stress equilibrium on def<strong>in</strong>ed <strong>in</strong>termediate configurations as well as the derivation of the<br />
total stresses. Special attention has to be given to the def<strong>in</strong>ition of accurate stress measures on<br />
the <strong>in</strong>termediate configurations. By this approach, a formal procedure for the direct connection of<br />
s<strong>in</strong>gle elements at large deformation processes can be obta<strong>in</strong>ed. The procedure itself is <strong>in</strong>dependent<br />
of the concrete material behaviour.<br />
The concept of direct connection of rheological elements <strong>in</strong> nonl<strong>in</strong>ear cont<strong>in</strong>uum <strong>mechanics</strong><br />
and some examples for its application will be presented. Furthermore, a numerical strategy for<br />
the direct implementation of this concept will be demonstrated.<br />
[1] J. Ihlemann (2006), Beobachterkonzepte und Darstellungsformen der nichtl<strong>in</strong>earen Kont<strong>in</strong>uumsmechanik,<br />
Habilitation, Universität Hannover<br />
A stochastic model for the direct and the <strong>in</strong>verse problem of adhesive materials<br />
N. Nörenberg, R. Mahnken (Universität Paderborn)<br />
This work deals with the generation of artificial data [1] based on experimental data for adhesive<br />
materials and the application of this data to the <strong>in</strong>verse and the direct problem. In reality there are<br />
only a very limited number of experimental data available. Therefore, the prediction of material<br />
behaviour is difficult and a statistical analysis with a stochastic proved thesis is nearly impossible.<br />
In order to <strong>in</strong>crease the number of tests a method of stochastic simulation based on time series<br />
analysis [2] is applied. With artificial data an arbitrary number of data is available and the<br />
process of the parameter identification can be statistically analysed. Additionally, two examples<br />
are shown, which adapt the analysed material parameter to the direct problem. The stochastic<br />
f<strong>in</strong>ite element method [3] is used to take <strong>in</strong>to account the distribution and deviation of the fracture<br />
stra<strong>in</strong>.<br />
[1] S. Schwan, Identifikation der Parameter <strong>in</strong>elastischer Werkstoffmodelle: Statistische Analyse<br />
und Versuchsplanung. Diss. Shaker, 2000.<br />
[2] P. J. Brockwell and R. A. Davis, Time series: theory and methods. Spr<strong>in</strong>ger, 2009<br />
[3] I. Babuška, R. Tempone and G. E. Zouraris, Galerk<strong>in</strong> f<strong>in</strong>ite element approximations of stochastic<br />
elliptic partial differential equations. SIAM Journal on Numerical Analysis 42(2)<br />
(2005), 800 – 825
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 31<br />
Analysis of nano<strong>in</strong>dentation experiments by means of rheological models<br />
Holger Worrack, Wolfgang H. Müller (TU Berl<strong>in</strong>)<br />
The nano<strong>in</strong>dentation technique, which is similar to the <strong>in</strong>strumented <strong>in</strong>dentation hardness accord<strong>in</strong>g<br />
to MARTENS, is established <strong>in</strong> the field of material characterization at small dimensions.<br />
It is daily practice to analyze nano<strong>in</strong>dentation data with an almost classical formula based on<br />
the publications by Oliver and Pharr and Fischer-Cripps. In this formula the gradient at the<br />
beg<strong>in</strong>n<strong>in</strong>g of the unload<strong>in</strong>g curve is used to determ<strong>in</strong>e Youngs modulus of the tested material,<br />
which is one of the material parameters of <strong>in</strong>terest.<br />
The procedure works well for elastic time-<strong>in</strong>dependent plastic material behavior, for example<br />
copper and the calibration material fused silica, even at higher test temperatures. However, low<br />
melt<strong>in</strong>g solder materials are susceptible to creep behavior, especially at the higher <strong>in</strong>dentation<br />
temperatures where the homologous temperature is > 0.5. As a result of the creep effects the<br />
beg<strong>in</strong>n<strong>in</strong>g of the unload<strong>in</strong>g curve often shows a bulge. This discrepancy from the ideal unload<strong>in</strong>g<br />
curve complicates the correct determ<strong>in</strong>ation of the unload<strong>in</strong>g stiffness and f<strong>in</strong>ally yields to<br />
<strong>in</strong>correct results for Youngs modulus.<br />
For this reason, additional analysis procedures are required to determ<strong>in</strong>e the material parameters<br />
more precisely. In this paper the authors want to give an <strong>in</strong>troduction to an enhanced<br />
analysis of nano<strong>in</strong>dentation data based on rheological models, which are often used to describe<br />
the time-dependence of material response. Two examples of such models are the MAXWELL- and<br />
the KELVIN-body. In these models spr<strong>in</strong>gs and dashpots connected <strong>in</strong> series and/or <strong>in</strong> parallel are<br />
used to describe the time-dependent material response. The viscous parameters, determ<strong>in</strong>ed from<br />
the recorded data dur<strong>in</strong>g the nano<strong>in</strong>dentation experiment, can be used to identify the mechanical<br />
material parameters. The authors present miscellaneous viscoeleastic and viscoplastic rheological<br />
models <strong>in</strong> connection with the correspond<strong>in</strong>g equations which are used to extract the material<br />
properties from the recorded data. Results of the analysis are presented and discussed <strong>in</strong> context<br />
with the results from the classical Oliver and Pharr procedure and with the material parameters<br />
published <strong>in</strong> the literature. F<strong>in</strong>ally, the models are assessed by their applicability of model<strong>in</strong>g the<br />
time-dependent material response of low melt<strong>in</strong>g solder materials.<br />
S6.12: Special <strong>Material</strong> Behavior Thu, 16:00–18:00<br />
Chair: Lurie Sergey, Jaan-Willem Simon S1|01–A1<br />
Carbon Fibre Prepregs: Simulation of a Thermo-Mechanical-Chemical Coupled Problem<br />
F. Hankeln, R. Mahnken (Universität Paderborn)<br />
In automotive <strong>in</strong>dustry research is done to replace high strength steel by comb<strong>in</strong>ations of steel<br />
and carbon-fibre prepregs (pre-impregnated fibres). It is planned to form both steel and uncured<br />
prepregs <strong>in</strong> one step followed by the cur<strong>in</strong>g process under pressure <strong>in</strong> the form<strong>in</strong>g die [1]. The<br />
ability to simulate the mechanical behaviour dur<strong>in</strong>g form<strong>in</strong>g and cur<strong>in</strong>g would allow more economical<br />
processes. The simulation of prepregs must regard highly anisotropic, viscoelastic and<br />
thermal- chemical properties. For this the model is split <strong>in</strong>to an anisotropic elastic part, which<br />
represents the fibre fraction and an isotropic, viscoelastic part, represent<strong>in</strong>g the matrix. This part<br />
also conta<strong>in</strong>s cur<strong>in</strong>g, caus<strong>in</strong>g a dependency on time and temperature. Dur<strong>in</strong>g deep-draw<strong>in</strong>g large<br />
deformations are occurr<strong>in</strong>g, so a large stra<strong>in</strong> model regard<strong>in</strong>g anisotropy[2], viscoelasticity [3]<br />
and cur<strong>in</strong>g [4] has been developed. Also experiments were made to validate this model. Current<br />
progress is the identification of material parameters.
32 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
[1] Homberg, W., Dau, J., Damerow, U. Comb<strong>in</strong>ed Form<strong>in</strong>g of Steel Blanks with Local CFRP<br />
Re<strong>in</strong>forcement, <strong>in</strong>: G. Hirt, A. E. Tekkaya (Eds.), steel research <strong>in</strong>t., Special Edition: Proceed<strong>in</strong>gs<br />
of the 10th International Conference on Technology of Plasticity, Wiley-VCH,<br />
We<strong>in</strong>heim, 2011, pp. 441-446<br />
[2] Menzel, A., Modell<strong>in</strong>g and Computation of Geometrically Nonl<strong>in</strong>ear Anisotropic Inelasticity,<br />
Dissertation, University of Kaiserlautern, 2002<br />
[3] Tschoegl, N.W. The Phenomenologial Theory of L<strong>in</strong>ear Viscoelastic Behaviour, Spr<strong>in</strong>ger<br />
Verlag, 1989<br />
[4] Lion, A. and Höfer, P., On the phenomenological representation of cur<strong>in</strong>g phenomena <strong>in</strong><br />
cont<strong>in</strong>uum <strong>mechanics</strong>, Arch. Mech. 59, 2007<br />
On the axially compressed multiple walled carbon nanotubes<br />
Ligia Munteanu (Institute of Solid Mechanics of Romanian Academy)<br />
A new approach is proposed <strong>in</strong> this paper, which comb<strong>in</strong>es elements of Toup<strong>in</strong>-M<strong>in</strong>dl<strong>in</strong> stra<strong>in</strong><br />
gradient theory and the Molecular Mechanics to <strong>in</strong>clude the <strong>in</strong>layer van der Waals atomistic<br />
<strong>in</strong>teractions for axially compressed multiple walled carbon nanotubes. The neighbor<strong>in</strong>g walls of<br />
a multiwalled nanotube are coupled through van der Waals <strong>in</strong>teractions, and the shell buckl<strong>in</strong>g<br />
would <strong>in</strong>itiate <strong>in</strong> the outermost shell, when nanotubes are short. The load-unloaded-displacement<br />
curve, the critical buckl<strong>in</strong>g and the appropriate values for elastic moduli are obta<strong>in</strong>ed. The theoretical<br />
results obta<strong>in</strong>ed show a good agreement with the experimental data reported by Waters,<br />
Gudury, Jouzi and Xu (2005). The size dependence of the hardness with respect to the depth<br />
and the radius of the <strong>in</strong>denter is also <strong>in</strong>vestigated. Results show a peculiar size <strong>in</strong>fluence on the<br />
hardness, which is expla<strong>in</strong>ed via the shear resistance between the neighbor<strong>in</strong>g walls dur<strong>in</strong>g the<br />
buckl<strong>in</strong>g of the multiwalled nanotubes. The present method can be further extended to <strong>in</strong>vestigate<br />
the stress-stra<strong>in</strong> relations and the fracture behaviors of S/MWCNT<br />
From vortices to dislocations: How fluid <strong>mechanics</strong> can <strong>in</strong>spire <strong>solid</strong> <strong>mechanics</strong><br />
Markus Scholle (Hochschule Heilbronn)<br />
Although it is known for nearly a century that production and movement of dislocations are the<br />
elementary processes responsible for the plastic deformation of a <strong>solid</strong> body, all attempts to derive<br />
a cont<strong>in</strong>uum theory of plasticity from the discrete micro–theory of dislocations did not succeed<br />
<strong>in</strong> universally valid field equations like e.g. Navier–Stokes equations <strong>in</strong> fluid dynamics.<br />
In this paper an approach is presented based on an analogy between dislocations and vortex<br />
l<strong>in</strong>es <strong>in</strong> fluid flow. S<strong>in</strong>ce the dynamics of the latter ones is well understood <strong>in</strong> terms of the Navier–<br />
Stokes equations, it is near at hand to make use of this analogy <strong>in</strong> order to establish a k<strong>in</strong>d of<br />
’Navier–Stokes equations for the distorsion tensor’.<br />
Start<strong>in</strong>g from Clebsch’s variational formulation for <strong>in</strong>viscid flow, a relation beween the symmetries<br />
of the Lagrangian and the balance of vorticity result<strong>in</strong>g from it is shown giv<strong>in</strong>g rise for<br />
the construction of another Lagrangian from which the respective dislocation balance results.<br />
The present state of the theory is discussed.<br />
On the connection of dissipation and deviatoric stress <strong>in</strong> the cont<strong>in</strong>uum theory of<br />
defects<br />
Johannes Schnepp (RWTH Aachen)
<strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong> 33<br />
Cont<strong>in</strong>uous distributions of defects (e. g. dislocations) can be described as differential geometric<br />
properties of the material manifold. <strong>Material</strong> forces and the Eshelby tensor are also quantities<br />
<strong>in</strong> this three-dimensional material space. The relation to defects has been treated often <strong>in</strong> the<br />
literature and various theories for the dynamics of defects have been proposed.<br />
Mov<strong>in</strong>g defects lead to differential geometric quantities chang<strong>in</strong>g with time. This has motivated<br />
some authors to augment the three space-like coord<strong>in</strong>ates <strong>in</strong> the material space by a time-like<br />
coord<strong>in</strong>ate. In this way one gets a four-dimensional material space-time manifold, analogous to<br />
the four-dimensional physical space-time <strong>in</strong> the theory of relativity. A connection of a time-like<br />
material coord<strong>in</strong>ate to temperature can be found <strong>in</strong> the literature on relativistic elasticity. These<br />
ideas will be brought together <strong>in</strong> this contribution and some implications will be developed.<br />
A time-like vector field <strong>in</strong> the material space-time can be associated with temperature and<br />
heat flux. Together with the three lattice vectors a tetrad field is def<strong>in</strong>ed and this field determ<strong>in</strong>es<br />
the differential geometric properties of the material manifold. If a variational formulation<br />
for a hyper-elastic <strong>solid</strong> is adopted, the derivatives of the Lagrangian density with respect to the<br />
components of the tetrad can be arranged <strong>in</strong> a four-dimensional second-order tensor. This tensor<br />
unifies the <strong>in</strong>formation about the three-dimensional Eshelby tensor (material momentum current),<br />
the entropy current, and the entropy density. The time-like component of the divergence of this<br />
tensor is the entropy production. Besides the entropy production due to heat transfer the theory<br />
yields entropy production due to defect movement which is proportional to deviatoric stress.<br />
Stress Reduction Factor of Ceramic Plate to Thermal Shock<br />
Weiguo Li, Tianbao Cheng (College of Resources and Environmental Science, Chongq<strong>in</strong>g), Da<strong>in</strong><strong>in</strong>g<br />
Fang (Pek<strong>in</strong>g University)<br />
In this work, through <strong>in</strong>troduc<strong>in</strong>g the analytical solution to transient conduction problem for the<br />
th<strong>in</strong> rectangular plate with convection <strong>in</strong>to the thermal stress field model of the elastic plate, the<br />
stress reduction factor which is useful <strong>in</strong> determ<strong>in</strong><strong>in</strong>g the thermal stresses <strong>in</strong> the ceramic plate<br />
subjected to thermal shock was presented <strong>in</strong> the dimensionless form. The properties and appropriate<br />
conditions of the stress reduction factor were analyzed. Then the def<strong>in</strong>itions, orig<strong>in</strong>s and<br />
limitations of the first and second thermal stress fracture resistance parameters which characterize<br />
the thermal shock resistance of brittle ceramics were discussed. Because of the demands <strong>in</strong><br />
the calculation of thermal stress, a new stress reduction factor was def<strong>in</strong>ed and compared with<br />
the previous one. For the given Biot number, the previous stress reduction factor first <strong>in</strong>creases<br />
and then reaches a maximum value, and afterwards decreases as the Fourier number <strong>in</strong>creases.<br />
However, the new stress reduction factor decreases as the Fourier number <strong>in</strong>creases. The new<br />
factor is more convenient for calculat<strong>in</strong>g the thermal stress <strong>in</strong> the plate subjected to thermal<br />
shock. The presented results are useful for the calculat<strong>in</strong>g of the thermal stress and choos<strong>in</strong>g of<br />
the appropriate thermal stress fracture resistance parameter when the ceramic plate is subjected<br />
to thermal shock.<br />
Model<strong>in</strong>g Deformation Tw<strong>in</strong>n<strong>in</strong>g <strong>in</strong> FeMn Alloys<br />
Shyamal Roy, Ra<strong>in</strong>er Glüge, Albrecht Bertram (Universität Magdeburg)<br />
Multiple tw<strong>in</strong>n<strong>in</strong>g [1] <strong>in</strong> s<strong>in</strong>gle crystals is modeled by study<strong>in</strong>g the response at each material<br />
po<strong>in</strong>t <strong>in</strong> order to understand micro-structural evolution and mechanical properties of FeMn<br />
(TWIP steel). Here the m<strong>in</strong>imum elastic stra<strong>in</strong> energy approach is used. It is well known that the<br />
elastic stra<strong>in</strong> energy of an <strong>in</strong>dividual material is convex. S<strong>in</strong>ce tw<strong>in</strong>n<strong>in</strong>g leads to isomorphic structures,<br />
the elastic stra<strong>in</strong> energy of a tw<strong>in</strong> material is convex too and hence, forms a non-convex<br />
energy landscape. A smooth stra<strong>in</strong> energy landscape is constructed to avoid the discont<strong>in</strong>uity<br />
at the transition po<strong>in</strong>t from parent to tw<strong>in</strong> material. A controlled viscous relaxation scheme is
34 <strong>Section</strong> 6: <strong>Material</strong> <strong>modell<strong>in</strong>g</strong> <strong>in</strong> <strong>solid</strong> <strong>mechanics</strong><br />
<strong>in</strong>corporated s<strong>in</strong>ce the boundary value problem of the non-convex energy function is ill posed [2].<br />
Deal<strong>in</strong>g with multiple energy wells is numerically very challeng<strong>in</strong>g. The solution is not determ<strong>in</strong>istic<br />
as any tw<strong>in</strong> configuration can be activated from the parent configuration, which is unknown<br />
<strong>in</strong>itially. Therefore, to have a complete energy landscape <strong>in</strong> hand at the beg<strong>in</strong>n<strong>in</strong>g is impossible.<br />
The material response is <strong>in</strong>stantaneously calculated depend<strong>in</strong>g on which tw<strong>in</strong> configuration is<br />
activated. However, the m<strong>in</strong>imum stra<strong>in</strong> energy approach faces its limitation because of elastic<br />
stra<strong>in</strong> energy <strong>in</strong>variance, which occurs due to the crystallographic equivalence of possible tw<strong>in</strong><br />
configurations. Hav<strong>in</strong>g identified the preferred tw<strong>in</strong> configuration, the secondary and, hence, the<br />
multiple tw<strong>in</strong>n<strong>in</strong>g are modeled.<br />
[1] Christian J. W., Mahajan S., Deformation Tw<strong>in</strong>n<strong>in</strong>g, Prog Mat Sci, 39, 1-157 (1995)<br />
[2] Carstensen C., Ten Remarks on Non-convex M<strong>in</strong>imization for Phase Transition Simulations,<br />
Comp Meth App Mech Eng, 194, 169-193 (2005)