Karlsruhe Institute of Technology Institute of Engineering Mechanics University of Paderborn Chair of Engineering Mechanics 25

Frequently, the case of finite strain anisotropy, particularly, the case of transversal isotropy, is applied to biological applications or to model fiber-reinforced composite materials. In this work the multiplicative decomposition of the deformation gradient into one part constrained in the direction of anisotropy (fiber direction) and one part describing the remaining deformation is proposed. Accordingly, a form of additively decomposed strain-energy function is suggested. This leads to a clear assignment of deformation and stress states in the direction of anisotropy and the remaining part. The decomposition is explained and a constitutive model of hyperelasticity for the case of transversal isotropy is proposed. The behavior of the model is investigated analytically at uniaxial tension along and perpendicular to the axis of anisotropy. In addition, the model is investigated numerically using h-version and p-version finite elements, where two examples are considered, one showing the influence of existence of anisotropy and the other showing the influence of orientation of the axis of anisotropy (fiber direction). Multiscale simulation of textiles based on the asymptotic homogenization and dimension reduction Zoufine Bare, Julia Orlik, and Vladimir Shiryaev Fraunhofer Institute for Industrial Mathematics (ITWM), Kaiserslautern, Germany Abstract. Textiles are materials with a periodic microstructure composed by thin and long fibers being in a contact with each other. In different applications, textiles are putting on some surfaces by sliding along them. Our research is devoted to simulate such problems. Mathematically the problem corresponds to the quasi-static contact problem with multiple contact interfaces. Since the structure of textile is periodic, the homogenization method can be applied to the problem to reduce its dimension. The extension of the two-scale analysis to the contact, corresponding corrector (or RVE) problem and the homogenized elasto-plastic problem are presented in [1], [2]. The main phenomenological result is that, the microscopic contact sliding results into the macroscopic plasticity. Furthermore, the structure of the textile can be considered as a network of thin contacting beams. Again, some asymptotic analysis was required to obtain the contact conditions for beams and justify them mathematically. In [3], the frictional forces and Moments for beams are obtained in terms of the 3D friction traction and some cross-sectional characteristics. Further, the network was discretized and contact problem solved numerically by augmented Lagrange method [4], and beam finite elements. Although, the theoretical results were justified only for infinitesimal deformations, large tension of streads was implemented on an incremental way using a Newton method with a continuation [5]. Finally, the quasi-static uni-lateral contact sliding of the textile membrane (consisting of 1D-beams) on a smooth surface was simulated using the obtained results [6]. References [1] D. Cioranescu, A. Damlamian, J. Orlik, Homogenization via unfolding in periodic elasticity with contact on closed and open cracks, Asymptot. Anal., in press (2012). [2] S. Fillep, J. Orlik, Z. Bare, P. Steinmann: Homogenization of elasticity in periodically heterogeneous bodies with contact on the microstructural elements, submitted to MEMOCS (2012). [3] Z. Bare, J. Orlik, G. P. Panasenko: Asymptotic dimension reduction of a Robin-type elasticity boundary value problem in thin beams, submitted to Applicable Analysis (2012). Textiles are materials with a periodic microstructure composed by thin and long fibers being in a contact with each other. In different applications, textiles are putting on some surfaces by sliding along them. Our research is devoted to simulate such problems. Mathematically the problem corresponds to the quasi-static contact problem with multiple contact interfaces. Since the structure of textile is periodic, the homogenization method can be applied to the problem to reduce its dimension. The extension of the two-scale analysis to the contact, corresponding corrector (or RVE) problem and the homogenized elasto-plastic problem are presented in [1], [2]. The main phenomenological result is that, the microscopic contact sliding results into the macroscopic plasticity. Furthermore, the structure of the textile can be considered as a network of thin contacting beams. Again, some asymptotic analysis was required to obtain the contact conditions for beams and justify them mathematically. In [3], the frictional forces and Moments for beams are obtained in terms of the 3D friction traction and some cross-sectional characteristics. Further, the network was discretized and contact problem solved numerically by augmented Lagrange method [4], and beam finite elements. Although, the theoretical results were justified only for infinitesimal deformations, large tension of streads was implemented on an incremental way using a Newton method with a continuation [5]. Finally, the quasi-static uni-lateral contact sliding of the textile membrane (consisting of 1D-beams) on a smooth surface was simulated using the obtained results [6]. References [1] D. Cioranescu, A. Damlamian, J. Orlik, Homogenization via unfolding in periodic elasticity with contact on closed and open cracks, Asymptot. Anal., in press (2012). [2] S. Fillep, J. Orlik, Z. Bare, P. Steinmann: Homogenization of elasticity in periodically heterogeneous bodies with contact on the microstructural elements, submitted to MEMOCS (2012). [3] Z. Bare, J. Orlik, G. P. Panasenko: Asymptotic dimension reduction of a Robin-type elasticity boundary value problem in thin beams, submitted to Applicable Analysis (2012). [4] N. Kikuchi, J. T. Oden: Contact problems in elasticity: A study of variational inequalities and finite elements methods, SIAM, USA, 1988. [5] P. Deuflhard: Newton Methods for Nonlinear Problems, Affine Invariance and Adaptive Algorithms. Springer, Berlin, Heidelberg, New York, London, Milan, Paris, Tokyo, 2004. [6] V. Shiryaev, J. Orlik: Uni-lateral contact sliding of the beam network on a smooth surface of a rigid body. Workshop Evolution problems in damage, plasticity and fracture, (Udine 19-21.09.2012), http://www.wias-berlin.de/people/knees/ workshops/nvyariouhNU87bao8df734wve/slides.html Particle shape effects in ductile matrix composites Helmut J. Böhm Institute of Lightweight Design and Structural Biomechanics, Vienna University of Technology, Vienna, Austria Abstract. Multi-particle unit cells containing a number of randomly positioned and oriented, identical particles of spherical, octahedral, cubic or tetrahedral shape, respectively, are used in modeling the thermoelastoplastic behavior of a ductile matrix composite. The particles are treated as thermoelastic and the matrix is described by J2-plasticity with linear isotropic hardening. Using standard Finite-Element-based periodic homogenization techniques, the macroscopic responses as well as the phase averages, standard deviations and distribution functions of microfield variables are evaluated for uniaxial, shear and thermal load cycles. Results are ensemble averaged over 5 different volume elements per particle shape and over different loading directions. Considerable particle shape effects on the macroscopic responses are predicted for the mechanical load cases, tetrahedral particles leading to considerably stronger strain hardening of the composite than do spherical ones. No comparable behavior is found, however, for thermal cycling. The particle shapes are predicted to influence the microscopic volumetric stresses mainly in terms of the standard deviations in the particle phase. Pronounced differences are obtained between the deviatoric (von Mises) stress fields of composites reinforced by spherical and tetrahedral particles, respectively, both the phase averages and the standard deviations showing markedly higher values for the latter. For thermal load case clear particle shape effects are present for both deviatoric and volumetric microstress fields. The responses obtained for cube-shaped and octahedral particles generally lie between the ones predicted for spheres and tetrahedra. The tendency of the polyhedral particles towards showing high average and local stresses in the particles indicates that such shapes may induce an increased susceptibility to damage due to particle failure. Multi-particle unit cells containing a number of randomly positioned and oriented, identical particles of spherical, octahedral, cubic or tetrahedral shape, respectively, are used in modeling the thermoelastoplastic behavior of a ductile matrix composite. The particles are treated as thermoelastic and the matrix is described by J2-plasticity with linear isotropic hardening. Using standard Finite-Element-based periodic homogenization techniques, the macroscopic responses as well as the phase averages, standard deviations and distribution functions of microfield variables are evaluated for uniaxial, shear and thermal load cycles. Results are ensemble averaged over 5 different volume elements per particle shape and over different loading directions. Considerable particle shape effects on the macroscopic responses are predicted for the mechanical load cases, tetrahedral particles leading to considerably stronger strain hardening of the composite than do spherical ones. No comparable behavior is found, however, for thermal cycling. The particle shapes are predicted to influence the microscopic volumetric stresses mainly in terms of the standard deviations in the particle phase. Pronounced differences are obtained between the deviatoric (von Mises) stress fields of composites reinforced by spherical and tetrahedral particles, respectively, both the phase averages and the standard deviations showing markedly higher values for the latter. For thermal load case clear particle shape effects are present for both deviatoric and volumetric microstress fields. The responses obtained for cube-shaped and octahedral particles generally lie between the ones predicted for spheres and tetrahedra. The tendency of the polyhedral particles towards showing high average and local stresses in the particles indicates that such shapes may induce an increased susceptibility to damage due to particle failure. Dynamical mechanical analysis on long fibre reinforced thermoplasstics (LFT) Barthel Brylka and Thomas Böhlke Institute of Engineering Mechanics, Chair for Continuum Mechanics Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. Discontineous glass fibre reinforced thermoplastics are commonly used for nonstructural parts in automotive applications. Due the versatile possibilities of manufacturing, forming, joining and recycling, thermoplastic matrix based composites are increasingly used also for semistructural parts. Thermoplastics like, e.g., polypropylene show a high temperature and strain-rate dependence. Therefore, for the automotive application sector, material models for a wide range of strain rates and temperatures are needed. Additionally, the influence of the viscoelastic behaviour of the matrix material on the effective material behaviour of the composite is of high interest. The DMA technique is an effective method to investigate the elastic and viscoelastic stiffness response of materials under cyclic loading. After a short introduction into the DMA technique, results for polypropylene and polypropylene based composite material will be presented. The composite under consideration is a long glass fibre reinforced thermoplastic manufactured in compression moulding. This manufacturing process induces an anisotropic fibre distribution and for that reason, the effective properties as well as the temperature and strain rate dependency has been investigated in different material directions. The comparison of the elastic and visocelastic material response of the matrix and the composite will be discussed in detail. References [1] P. Middendorf: Viskoelastisches Verhalten von Polymersystemen, FortschrittBerichte VDI, Reihe 5, VDI Verlag (2002) [2] S. Deng, M. Hou, L. Ye: Temperature-dependent elastic moduli of epoxies measured by DMA and their correlations to mechanical testing data, Polym Test, 26, 803–813 (2007). [3] E. Kontou, A. Kallimanis: Thermo-visco-plastic behaviour of fibre-reinforced polymer composites, Compos. Sci. Technol., 66, 1588–1596 (2006). Discontineous glass fibre reinforced thermoplastics are commonly used for nonstructural parts in automotive applications. Due the versatile possibilities of manufacturing, forming, joining and recycling, thermoplastic matrix based composites are increasingly used also for semistructural parts. Thermoplastics like, e.g., polypropylene show a high temperature and strain-rate dependence. Therefore, for the automotive application sector, material models for a wide range of strain rates and temperatures are needed. Additionally, the influence of the viscoelastic behaviour of the matrix material on the effective material behaviour of the composite is of high interest. The DMA technique is an effective method to investigate the elastic and viscoelastic stiffness response of materials under cyclic loading. After a short introduction into the DMA technique, results for polypropylene and polypropylene based composite material will be presented. The composite under consideration is a long glass fibre reinforced thermoplastic manufactured in compression moulding. This manufacturing process induces an anisotropic fibre distribution and for that reason, the effective properties as well as the temperature and strain rate dependency has been investigated in different material directions. The comparison of the elastic and visocelastic material response of the matrix and the composite will be discussed in detail. References [1] P. Middendorf: Viskoelastisches Verhalten von Polymersystemen, FortschrittBerichte VDI, Reihe 5, VDI Verlag (2002) [2] S. Deng, M. Hou, L. Ye: Temperature-dependent elastic moduli of epoxies measured by DMA and their correlations to mechanical testing data, Polym Test, 26, 803–813 (2007). [3] E. Kontou, A. Kallimanis: Thermo-visco-plastic behaviour of fibre-reinforced polymer composites, Compos. Sci. Technol., 66, 1588–1596 (2006). Modeling of anisotropy at large deformations for polycarbonate Ismail Caylak and Rolf Mahnken Chair of Engineering Mechanics, University of Paderborn, Paderborn, Germany Abstract. In this presentation we develop a model to describe the induced plasticity of polymers at large deformations. Polymers such as stretch films exhibit a pronounced strength in the loading direction. The undeformed state of the films is isotropic, whereas after the uni-axial loading the material becomes anisotropic. In order to consider this induced ansiotropy as an initial anisotropy the yield function can be formulated as a function of the anisotropic tensor, where again the anisotropic tensor is a function of the direction of the stretched polymer chains. A backward EULER scheme is used for updating the evolution equations, and the algorithmic tangent operator is derived. The numerical implementation of the resulting set of constitutive equations is used in a finite element program and for parameter identification. In this presentation we develop a model to describe the induced plasticity of polymers at large deformations. Polymers such as stretch films exhibit a pronounced strength in the loading direction. The undeformed state of the films is isotropic, whereas after the uni-axial loading the material becomes anisotropic. In order to consider this induced ansiotropy as an initial anisotropy the yield function can be formulated as a function of the anisotropic tensor, where again the anisotropic tensor is a function of the direction of the stretched polymer chains. A backward EULER scheme is used for updating the evolution equations, and the algorithmic tangent operator is derived. The numerical implementation of the resulting set of constitutive equations is used in a finite element program and for parameter identification. A Multi-Mechanism Model for Cutting Simulations Combining Visco-plastic Asymmetry and Phase Tranformation Chun Cheng, Rolf Mahnken, Eckart Uhlmann, and Ivan Mitkov Ivanov 1 Chair of Engineering Mechanics (LTM), University of Paderborn, Paderborn, Germany 2 Institute for Machine Tools and Factory Management (IWF), Technical University Berlin, Berlin, Germany Abstract. We develop a multi-mechanism model for strainrateand temperaturedependent asymmetric plastic material behavior accompanied by phase transformations, which are important phenomena in steel production processes. To this end the well-known Johnson-Cook model is extended by the concept of weighting functions [1], and it is combined with a model of transformation-induced plasticity (TRIP) based on the Leblond approach [2]. The bulk model is formulated within a thermodynamic framework at large strains, and it will be specialized and applied to cutting processes in steel production. In this prototype situation we have: Transformation of the martensitic initial state into austenite, then retransformation of martensite. For incorporation of visco-plastic asymmetry we present a model, which consists of a rate dependent flow factor with a rate independent yield function. In the examples parameters are identified for the material DIN 100Cr6, and we illustrate the characteristic effects of our multi-mechanism model, such as strain softening due to temperature, rate dependence and temperature dependence as well as the SD-effect. A finite-element simulation illustrates the different mechanisms for a cutting process. References [1] R. Mahnken: Creep simulation of asymmetric effects at large strains by stress mode decomposition, Comp. Meths. Appl. Mech. Eng., 94, 4221-4243 (2005). [2] J.B. Leblond: Mathematical modelling of transformation plasticity in steels II: Coupling with strain hardening phenomena. Int. J. of Plasticity 5, 537-591 (1989) We develop a multi-mechanism model for strainrateand temperaturedependent asymmetric plastic material behavior accompanied by phase transformations, which are important phenomena in steel production processes. To this end the well-known Johnson-Cook model is extended by the concept of weighting functions [1], and it is combined with a model of transformation-induced plasticity (TRIP) based on the Leblond approach [2]. The bulk model is formulated within a thermodynamic framework at large strains, and it will be specialized and applied to cutting processes in steel production. In this prototype situation we have: Transformation of the martensitic initial state into austenite, then retransformation of martensite. For incorporation of visco-plastic asymmetry we present a model, which consists of a rate dependent flow factor with a rate independent yield function. In the examples parameters are identified for the material DIN 100Cr6, and we illustrate the characteristic effects of our multi-mechanism model, such as strain softening due to temperature, rate dependence and temperature dependence as well as the SD-effect. A finite-element simulation illustrates the different mechanisms for a cutting process. References [1] R. Mahnken: Creep simulation of asymmetric effects at large strains by stress mode decomposition, Comp. Meths. Appl. Mech. Eng., 94, 4221-4243 (2005). [2] J.B. Leblond: Mathematical modelling of transformation plasticity in steels II: Coupling with strain hardening phenomena. Int. J. of Plasticity 5, 537-591 (1989) Simulation of strain induced anisotropy for polymers with weighting functions Christian Dammann and Rolf MahnkenChair of Engineering Mechanics,University of Paderborn, Paderborn, Germany Abstract. The alignment of polymer chains is a well known microstructural evolutioneffect due to straining of polymers [1]. This has a drastic influence on the macroscopicproperties of the initially isotropic material, such as a pronounced strength in theloading direction of stretch films [2]. For modelling of this effect of strain inducedanisotropy, a macroscopic constitutive model is developed in this presentation. Withinthis framework, an additive decomposition of the logarithmic Hencky strain tensorinto elastic and inelastic parts is used to formulate the constitutive equations. In orderto handle the induced anisotropy, weighting functions are introduced to represent astrain-softening-effect for different loading directions. The weighting functions dependon the direction of the stretched polymer chains. Under these circumstances they areapplied to additively decompose direction-dependent material parameters into a sumof weighted direction related quantities. The resulting evolution equations are updatedusing a backward Euler scheme and the algorithmic tangent operator is derived for thefinite element equilibrium iteration. The numerical implementation of the resulting setof constitutive equations is employed into a finite Element programm to identify theunknown parameters.References[1] Ashby, M.F.; Jones, D.R.H.: Engineering Materials 2, An Introduction to Microstruc-tures, Processing and Design, Pergamon, Elsevier Science, Oxford, 1986[2] Wibbeke, Schoeppner, R. Mahnken: Experimental investigations on the inducedanisotropy of mechanical properties in polycarbonate films, Submitted, 2012[3] R. Mahnken, A.Shaban: Finite elasto-viscoplastic modeling of polymers includingasymmetric effects, Arch Appl Mech, DOI 10.1007/s00419-012-0632-6 (2012) The alignment of polymer chains is a well known microstructural evolutioneffect due to straining of polymers [1]. This has a drastic influence on the macroscopicproperties of the initially isotropic material, such as a pronounced strength in theloading direction of stretch films [2]. For modelling of this effect of strain inducedanisotropy, a macroscopic constitutive model is developed in this presentation. Withinthis framework, an additive decomposition of the logarithmic Hencky strain tensorinto elastic and inelastic parts is used to formulate the constitutive equations. In orderto handle the induced anisotropy, weighting functions are introduced to represent astrain-softening-effect for different loading directions. The weighting functions dependon the direction of the stretched polymer chains. Under these circumstances they areapplied to additively decompose direction-dependent material parameters into a sumof weighted direction related quantities. The resulting evolution equations are updatedusing a backward Euler scheme and the algorithmic tangent operator is derived for thefinite element equilibrium iteration. The numerical implementation of the resulting setof constitutive equations is employed into a finite Element programm to identify theunknown parameters.References[1] Ashby, M.F.; Jones, D.R.H.: Engineering Materials 2, An Introduction to Microstruc-tures, Processing and Design, Pergamon, Elsevier Science, Oxford, 1986[2] Wibbeke, Schoeppner, R. Mahnken: Experimental investigations on the inducedanisotropy of mechanical properties in polycarbonate films, Submitted, 2012[3] R. Mahnken, A.Shaban: Finite elasto-viscoplastic modeling of polymers includingasymmetric effects, Arch Appl Mech, DOI 10.1007/s00419-012-0632-6 (2012) Meso-macro modeling of a coated forming tool includingdamage Johannes Dieker, Kim-Henning Sauerland, and Rolf MahnkenChair of Engineering Mechanics (LTM),University of Paderborn, Paderborn, Germany Abstract. A hybrid forming process is considered where the forming tool is subjectedto cyclic thermal shock loading [1]. The thermal shock results from the contact of theforming tool with the heated workpiece. In order to reduce fatigue phenomena andto improve the tool service life, a multilayer coating system is applied on the tool. Inparticular, a thermal barrier layer (TBL) is used to reduce the impact of the heating.In this contribution, an existing two-scale model for the simulation of the coatedforming tool [2] is extended. On the mesoscale, the different constituents of thecoating system are dissolved within a representative volume element (RVE). Thehomogenized properties are then used to simulate the coating system on themacroscale. Furthermore, a damage model is used on the mesoscale to account fordelamination effects.References[1] I. Özdemir, W.A.M. Brekelmans, M.G.D. Geers: FE computational homogenizationfor the thermo-mechanical analysis of heterogeneous solids, Comp. Methods Appl.Mech. Engrg., 198, 602–613 (2008).[2] K.H. Sauerland, R. Mahnken: Two scale FE simulation of coated forming toolsunder thermo-mechanical loading, Technsiche Mechanik, 32, 84–101 (2012).[3] K. Steinhoff, H.J. Maier, D. Biermann Functionally graded materials in industrial massproduction. Wissenschaftliche Scripten, Auerbach, 2009 A hybrid forming process is considered where the forming tool is subjectedto cyclic thermal shock loading [1]. The thermal shock results from the contact of theforming tool with the heated workpiece. In order to reduce fatigue phenomena andto improve the tool service life, a multilayer coating system is applied on the tool. Inparticular, a thermal barrier layer (TBL) is used to reduce the impact of the heating.In this contribution, an existing two-scale model for the simulation of the coatedforming tool [2] is extended. On the mesoscale, the different constituents of thecoating system are dissolved within a representative volume element (RVE). Thehomogenized properties are then used to simulate the coating system on themacroscale. Furthermore, a damage model is used on the mesoscale to account fordelamination effects.References[1] I. Özdemir, W.A.M. Brekelmans, M.G.D. Geers: FE computational homogenizationfor the thermo-mechanical analysis of heterogeneous solids, Comp. Methods Appl.Mech. Engrg., 198, 602–613 (2008).[2] K.H. Sauerland, R. Mahnken: Two scale FE simulation of coated forming toolsunder thermo-mechanical loading, Technsiche Mechanik, 32, 84–101 (2012).[3] K. Steinhoff, H.J. Maier, D. Biermann Functionally graded materials in industrial massproduction. Wissenschaftliche Scripten, Auerbach, 2009 Micromechanical modeling of bainitic phasetransformation for multi-variant polycrystalline low alloysteels Ulrich Ehlenbröker, Andreas Schneidt, and Rolf MahnkenChair of Engineering Mechanics (LTM),University of Paderborn, Paderborn, Germany Abstract. Metal forming processes are important technologies for the productionof engineering structures. In order to optimize the resulting material properties, itbecomes necessary to simulate the entire forming process by taking into accountphysical effects such as phase transformations.In our work, we develop a micromechanical material model for phase transformationfrom austenite to bainite for a polycrystalline low alloys steel. In this material (e.g.,51CrV4), the phase changes from austenite to perlite-ferrite, bainite or martensite,respectively. The presentation is concerned with phase transformation betweenaustenite and n-bainite variants in N differently orientated grains. The characteristicfeatures of bainite formation are the combination of time-dependent transformationkinetics and lattice shearing in the microstructure. These effects are consideredon the microscale and transferred to the polycrystalline macroscale by means ofhomogenisation of stochastically orientated grains.Furthermore, the numerical implementation of our model with a two-step algorithmis presented. In the first step, we use a projected Newton algorithm, based on thealgorithm in [2], for the calculation of phase transformation. Then, in a second step,a Newton algorithm is used for the calculation of visco-plasticity.References[1] Mahnken, R.; Schneidt, A.; Tschumak, S.; Maier, H.J. (2011), On the simulation ofaustenite to bainite phase transformationIn: Computational Material Science, 50, 1823–1829[2] Mahnken, R.; Wilmanns, S. (2011), A projected Newton algorithm for simulation ofmulti-variant textured polycrystalline shape memory alloysIn: Computational Material Science, 50, 2535–2548[3] Govindjee, S.; Mielke, A.; Hall, G.J. (2003), The free energy of mixing for n-variantmartensitic phase transformations using quasi-convex analysisIn: Journal of the Mechanics and Physics of Solids, 51, 1–26 Metal forming processes are important technologies for the productionof engineering structures. In order to optimize the resulting material properties, itbecomes necessary to simulate the entire forming process by taking into accountphysical effects such as phase transformations.In our work, we develop a micromechanical material model for phase transformationfrom austenite to bainite for a polycrystalline low alloys steel. In this material (e.g.,51CrV4), the phase changes from austenite to perlite-ferrite, bainite or martensite,respectively. The presentation is concerned with phase transformation betweenaustenite and n-bainite variants in N differently orientated grains. The characteristicfeatures of bainite formation are the combination of time-dependent transformationkinetics and lattice shearing in the microstructure. These effects are consideredon the microscale and transferred to the polycrystalline macroscale by means ofhomogenisation of stochastically orientated grains.Furthermore, the numerical implementation of our model with a two-step algorithmis presented. In the first step, we use a projected Newton algorithm, based on thealgorithm in [2], for the calculation of phase transformation. Then, in a second step,a Newton algorithm is used for the calculation of visco-plasticity.References[1] Mahnken, R.; Schneidt, A.; Tschumak, S.; Maier, H.J. (2011), On the simulation ofaustenite to bainite phase transformationIn: Computational Material Science, 50, 1823–1829[2] Mahnken, R.; Wilmanns, S. (2011), A projected Newton algorithm for simulation ofmulti-variant textured polycrystalline shape memory alloysIn: Computational Material Science, 50, 2535–2548[3] Govindjee, S.; Mielke, A.; Hall, G.J. (2003), The free energy of mixing for n-variantmartensitic phase transformations using quasi-convex analysisIn: Journal of the Mechanics and Physics of Solids, 51, 1–26 A mixed variational formulation for nonlinearhomogenization using reduced basis methods Felix FritzenYoung Investigator Group Computer Aided Material ModelingInstitute of Engineering Mechanics, Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. The homogenization of nonlinear micro-heterogeneous materials is acomputationally challenging procedure. While FEM simulations on representativevolume elements can capture the effect of the heterogeneities and the nonlinearitiesto a good extent, the associated computational cost is prohibitively large. In order tosatisfy the demands from industry, it is required to accelerate the simulations by afactor of 104 or more in order to be competitive with heuristic models, which cannotconsider all microstructural effects.A recent proposition that can lead to such gains is the Nonuniform TransformationField Analysis (NTFA) [1, 2]. The method belongs to the class of reduced basis modelorder reduction techniques. Its main feature is a low-dimensional parametrization ofthe plastic strain fields using global ansatz functions referred to as inelastic modes.Unfortunately, the method has some short-comings since the evolution of the internalvariables of the model is derived from a heuristic macroscopic yield criterion.Recently, the author has extended the method for linear visco-elastic materials [4]. Inthe new model the evolution of the internal variables is mircomechanically derivedfrom the dissipative effects on the microscale. In the current contribution the methodis extended to allow for rate-dependent Generalized Standard Materials. The evolutionof the internal variables of the model is based on a mixed incremental variationformulation. Numerical examples for isotropic and anisotropic visco-plasticity modelsare presented.References[1] J.-C. Michel, P. Suquet: Nonuniform Transformation Field Analysis, InternationalJournal of Solids and Structures, 2003.[2] F. Fritzen, T. Böhlke: Three-dimensional finite element implementation of thenonuniform transformation field analysis, International Journal for NumericalMethods in Engineering, 84, 803–829, 2010.[3] F. Fritzen, T. Böhlke: Reduced basis homogenization of viscoelastic composites,submitted.[4] F. Fritzen, M. Leuschner: Reduced basis computational homogenization based on amixed incremental formulation, submitted. The homogenization of nonlinear micro-heterogeneous materials is acomputationally challenging procedure. While FEM simulations on representativevolume elements can capture the effect of the heterogeneities and the nonlinearitiesto a good extent, the associated computational cost is prohibitively large. In order tosatisfy the demands from industry, it is required to accelerate the simulations by afactor of 104 or more in order to be competitive with heuristic models, which cannotconsider all microstructural effects.A recent proposition that can lead to such gains is the Nonuniform TransformationField Analysis (NTFA) [1, 2]. The method belongs to the class of reduced basis modelorder reduction techniques. Its main feature is a low-dimensional parametrization ofthe plastic strain fields using global ansatz functions referred to as inelastic modes.Unfortunately, the method has some short-comings since the evolution of the internalvariables of the model is derived from a heuristic macroscopic yield criterion.Recently, the author has extended the method for linear visco-elastic materials [4]. Inthe new model the evolution of the internal variables is mircomechanically derivedfrom the dissipative effects on the microscale. In the current contribution the methodis extended to allow for rate-dependent Generalized Standard Materials. The evolutionof the internal variables of the model is based on a mixed incremental variationformulation. Numerical examples for isotropic and anisotropic visco-plasticity modelsare presented.References[1] J.-C. Michel, P. Suquet: Nonuniform Transformation Field Analysis, InternationalJournal of Solids and Structures, 2003.[2] F. Fritzen, T. Böhlke: Three-dimensional finite element implementation of thenonuniform transformation field analysis, International Journal for NumericalMethods in Engineering, 84, 803–829, 2010.[3] F. Fritzen, T. Böhlke: Reduced basis homogenization of viscoelastic composites,submitted.[4] F. Fritzen, M. Leuschner: Reduced basis computational homogenization based on amixed incremental formulation, submitted. Thermodynamic consistent modelling of polymer curingcoupled to visco-elasticity at large strains Frederik Hankeln and Rolf MahnkenChair of Engineering Mechanics,University of Paderborn, Paderborn, Germany Abstract. We develop a macroscopic constitutive model for temperature-dependentvisco-elastic effects accompanied by curing of polymeric matrix material, which areimportant phenomena in production processes. Within a thermodynamic frameworkwe use an additive ternary decomposition of the logarithmic Hencky strain tensorinto mechanical, thermal and chemical parts. Based on the concept of stoichiometricmass fractions for resin, curing agent and solidified material the bulk compressionmodulus as well as the bulk heatand shrinking dilatation coeffcients are derived andcompared with ad hoc assumptions from the literature [1, 2]. Moreover, we use theamount of heat generated during dynamic scanning until completion of the chemicalreactions, to define the chemical energy. As a major result, the resulting latent heatof curing occurring in the heat-conduction equation derived in our approach revealsan ad hoc approach from the literature as a special case. In addition, thermodynamicconsistency of the model will be proved, and the numerical implementation of theconstitutive equations into a finite-element program is described. In the examples weillustrate the characteristic behaviour of the model, such as shrinking due to curingand temperature dependence [3] and simulate the deep drawing of a spherical partwith the finite-element-method.References[1] P.J. Halley, M.E. Mackay : Chemorheology of thermosets, an overview, Polym EngSci 36(5), 593–609 (1996)[2] A. Lion, P. Höfer, On the phenomenological representation of curing phenomena incontiuum mechanics Archive of Mechanics, 59, 59–89 (2007)[3] J.E. Martin, D.B. Adolf: Constitutive equation for cure-induced stresses in aviscoelastic material, Macromolecules, 23, 5014–50191 (1990) We develop a macroscopic constitutive model for temperature-dependentvisco-elastic effects accompanied by curing of polymeric matrix material, which areimportant phenomena in production processes. Within a thermodynamic frameworkwe use an additive ternary decomposition of the logarithmic Hencky strain tensorinto mechanical, thermal and chemical parts. Based on the concept of stoichiometricmass fractions for resin, curing agent and solidified material the bulk compressionmodulus as well as the bulk heatand shrinking dilatation coeffcients are derived andcompared with ad hoc assumptions from the literature [1, 2]. Moreover, we use theamount of heat generated during dynamic scanning until completion of the chemicalreactions, to define the chemical energy. As a major result, the resulting latent heatof curing occurring in the heat-conduction equation derived in our approach revealsan ad hoc approach from the literature as a special case. In addition, thermodynamicconsistency of the model will be proved, and the numerical implementation of theconstitutive equations into a finite-element program is described. In the examples weillustrate the characteristic behaviour of the model, such as shrinking due to curingand temperature dependence [3] and simulate the deep drawing of a spherical partwith the finite-element-method.References[1] P.J. Halley, M.E. Mackay : Chemorheology of thermosets, an overview, Polym EngSci 36(5), 593–609 (1996)[2] A. Lion, P. Höfer, On the phenomenological representation of curing phenomena incontiuum mechanics Archive of Mechanics, 59, 59–89 (2007)[3] J.E. Martin, D.B. Adolf: Constitutive equation for cure-induced stresses in aviscoelastic material, Macromolecules, 23, 5014–50191 (1990) Damage in rubber-toughened polymers: modeling andexperiments Martin Helbig and Thomas SeeligInstitute of Mechanics,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. Distributed Crazing seems to be the most important mechanism underlyingthe inelastic behaviour of rubber toughened polymers such as acrylonitrile-butadiene-styrene (ABS). A micromechanics based constitutive model focussing on thismechanism is developed and presented here. It is based on the idea that theformation of distributed crazes (i.e. cohesive crack-like surfaces) give rise to an overallinelastic strain in the direction of maximum principal stress. This concept is usedin a homogenized model for ABS which explicitely accounts for microstructuralparameters such as the rubber content and the rubber particle size. Tensile tests underdifferent loading conditions are used to determined the material parameters of theconstitutive model.Numerical simulations as well as experiments are conducted on a Single Edge NotchedTensile (SENT) specimen in order to validate the model and analyze the fracturebehaviour of ABS. The distributed crazing model proves successful in reproducingthe characteristic elongated shape of the plastic zone in front of a notch in ABS. Distributed Crazing seems to be the most important mechanism underlyingthe inelastic behaviour of rubber toughened polymers such as acrylonitrile-butadiene-styrene (ABS). A micromechanics based constitutive model focussing on thismechanism is developed and presented here. It is based on the idea that theformation of distributed crazes (i.e. cohesive crack-like surfaces) give rise to an overallinelastic strain in the direction of maximum principal stress. This concept is usedin a homogenized model for ABS which explicitely accounts for microstructuralparameters such as the rubber content and the rubber particle size. Tensile tests underdifferent loading conditions are used to determined the material parameters of theconstitutive model.Numerical simulations as well as experiments are conducted on a Single Edge NotchedTensile (SENT) specimen in order to validate the model and analyze the fracturebehaviour of ABS. The distributed crazing model proves successful in reproducingthe characteristic elongated shape of the plastic zone in front of a notch in ABS. FE modelling of composite plates Cécile Helfen and Stefan DiebelsChair of Applied Mechanics,Saarland University, Saarbrücken, Germany Abstract. Nowadays, composite plates, such as hybrid laminates and sandwich plates,present an interesting issue for the transport industry, because of their good mechanicalproperties at relatively limited weight. In the present communication, a multi-scalemodelling of the mechanical behaviour of composite plates is proposed. The principleof the FE method [1-4] is to consider two scales: on the macroscale, a FE computationof a homogeneous plate is performed. But instead of using the constitutive law of theplate, the deformations are projected in an accurate way from each integration point ofthe macroscale to the boudaries of an RVE on the mesocale. In the mesoscale, anotherFE computation of the resulting Dirichlet boundary value problem for a RepresentativeVolume Element (RVE) is defined. Finally, a modified Hill-Mandel condition enablesthe compution of the macroscopic stress resultants. In this work, special attention ispaid to the definition of an analytical tangent and to the consideration of non-linearmaterial behaviour.Further improvements concerning the modeling of complicated structures, as forinstance of the interface between metallic and polymeric layers, will be handled ina forthcoming work.References[1] M. G. D. Geers, E. W. C. Coenen, and V. G. Kouznetsova: Multi-scale computationalhomogenization of structured thin sheets, Modelling Simul. Mater. Sci. Eng., 15, 393–404 (2007)[2] M. Landervik and R. Larsson: A higher-order stress-resultant shell formulationbased on multiscale homogenization In: Modeling of foams for impact simulation(Ph.D.-thesis), paper D, Chalmers University of Technology, Schweden, 2008[3] E. W. C. Coenen, V. G. Kouznetsova, and M. G. D. Geers: Computationalhomogenization for heterogeneous thin sheets, Int. J. Numer. Meth. Eng., 83(8-9),1180–1205 (2010)[4] C. Helfen, S. Diebels, Numerical Multiscale Modelling of Sandwich Plates.Technische Mechanik, 32(2-5), 251–264 (2012) Nowadays, composite plates, such as hybrid laminates and sandwich plates,present an interesting issue for the transport industry, because of their good mechanicalproperties at relatively limited weight. In the present communication, a multi-scalemodelling of the mechanical behaviour of composite plates is proposed. The principleof the FE method [1-4] is to consider two scales: on the macroscale, a FE computationof a homogeneous plate is performed. But instead of using the constitutive law of theplate, the deformations are projected in an accurate way from each integration point ofthe macroscale to the boudaries of an RVE on the mesocale. In the mesoscale, anotherFE computation of the resulting Dirichlet boundary value problem for a RepresentativeVolume Element (RVE) is defined. Finally, a modified Hill-Mandel condition enablesthe compution of the macroscopic stress resultants. In this work, special attention ispaid to the definition of an analytical tangent and to the consideration of non-linearmaterial behaviour.Further improvements concerning the modeling of complicated structures, as forinstance of the interface between metallic and polymeric layers, will be handled ina forthcoming work.References[1] M. G. D. Geers, E. W. C. Coenen, and V. G. Kouznetsova: Multi-scale computationalhomogenization of structured thin sheets, Modelling Simul. Mater. Sci. Eng., 15, 393–404 (2007)[2] M. Landervik and R. Larsson: A higher-order stress-resultant shell formulationbased on multiscale homogenization In: Modeling of foams for impact simulation(Ph.D.-thesis), paper D, Chalmers University of Technology, Schweden, 2008[3] E. W. C. Coenen, V. G. Kouznetsova, and M. G. D. Geers: Computationalhomogenization for heterogeneous thin sheets, Int. J. Numer. Meth. Eng., 83(8-9),1180–1205 (2010)[4] C. Helfen, S. Diebels, Numerical Multiscale Modelling of Sandwich Plates.Technische Mechanik, 32(2-5), 251–264 (2012) Computational Homogenization of Short FiberReinforced Thermoplastic MaterialsSven Hoffmann, Markus André, and Ralf Müller1 CC/PJ-HEV1, CR/APP2Robert Bosch GmbH, Germany2 Institute of Applied MechanicsUniversity of Kaiserslautern, Kaiserslautern, Germany Abstract. In this work an anisotropic failure criterion for short fiber reinforcedthermoplastic materials is developed. The basis for the computational homogenizationof the material is the representative volume element (RVE) method, see [1]. In orderto increase the accuracy of the computational homogenization process, an exactgeneration of fibre orientation in the RVE is desired. Therefore, an iterative algorithmfor fiber orientation generation is presented. The algorithm allows the generationof a set of fibers that exactly satisfy a given target orientation tensor within theRVE. The development of a failure criterion starts with the identification of thedominating damage mechanisms. FESEM analyses of fracture surfaces suggest thatthe fiber matrix coupling is strong and interface damage (delamination) does notoccur. Fiber fracture and matrix damage are the dominating failure mechanisms. Afterintroduction of suitable material and damage models for the fiber and matrix material,the experimental results from tension tests could be successfully simulated by RVEcomputations, see [2]. On this basis a failure criterion for the composite is developed.Computational examples are given for a composite material with two different fiberorientation distributions.References[1] S. Hoffmann, M. André, A. Rodríguez Sánchez, R. Mueller: A new and efficientapproach for modeling short fiber reinforced materials within RVEs using anembedded element technique, Proc. Appl. Math. Mech., 10, 413–414 (2010)[2] S. Hoffmann, M. André, A. Rodríguez Sánchez, R. Mueller: A RVE-based micromechanical model for short fiber reinforced plastic materials including matrixdamage and fiber fracture, Proc. Appl. Math. Mech., 11, 155-156 (2011) In this work an anisotropic failure criterion for short fiber reinforcedthermoplastic materials is developed. The basis for the computational homogenizationof the material is the representative volume element (RVE) method, see [1]. In orderto increase the accuracy of the computational homogenization process, an exactgeneration of fibre orientation in the RVE is desired. Therefore, an iterative algorithmfor fiber orientation generation is presented. The algorithm allows the generationof a set of fibers that exactly satisfy a given target orientation tensor within theRVE. The development of a failure criterion starts with the identification of thedominating damage mechanisms. FESEM analyses of fracture surfaces suggest thatthe fiber matrix coupling is strong and interface damage (delamination) does notoccur. Fiber fracture and matrix damage are the dominating failure mechanisms. Afterintroduction of suitable material and damage models for the fiber and matrix material,the experimental results from tension tests could be successfully simulated by RVEcomputations, see [2]. On this basis a failure criterion for the composite is developed.Computational examples are given for a composite material with two different fiberorientation distributions.References[1] S. Hoffmann, M. André, A. Rodríguez Sánchez, R. Mueller: A new and efficientapproach for modeling short fiber reinforced materials within RVEs using anembedded element technique, Proc. Appl. Math. Mech., 10, 413–414 (2010)[2] S. Hoffmann, M. André, A. Rodríguez Sánchez, R. Mueller: A RVE-based micromechanical model for short fiber reinforced plastic materials including matrixdamage and fiber fracture, Proc. Appl. Math. Mech., 11, 155-156 (2011) Fast Numerical Computation of Precise Bounds ofEffective Elastic Moduli Matthias Kabel and Heiko AndräDepartment Flow and Material SimulationFraunhofer ITWM, Kaiserslautern, Germany Abstract. A fast numerical solver to compute precise bounds of effective propertiesof multi-phase elastic composites is presented in contrast to analytical estimates likeHashin-Shtrikman bounds.Analytical homogenization methods fulfil the requirements (with respect to accuracy,computational effort and generality of the microstructures) for predicting effectiveproperties of multi-phase elastic composites only for simple shaped inclusions. Curvedfibers and even more complex non-convex inclusions cannot be considered or leadto bad approximations at least for higher stiffness ratios. Furthermore, the usage ofanalytical homogenization on base of micro-tomographies often requires additionalimage processing and image analysis steps. Since micro-tomographies become moreand more mainstream in material science, numerical homogenization as additional toolfor image processing software is qualified for highly precise predictions directly fromthree-dimensional segmented images.For numerical homogenization the equations of elasticity are formulated as integralequations of Lippmann-Schwinger type [6, 4], which can be efficiently solved by usingFast Fourier Transformations (FFT). This approach is particularly suited for digitalimages (CT images) of complex microstructures and needs much less computationaleffort than finite element schemes to predict the effective properties [1, 2]. Althoughthis method is well-known [5, 3], the usage of this method to compute lower and upperbounds is new.A first numerical test for a simple microstructure demonstrates the numericalconvergence with respect to the resolution of the microstructure. The quality of the newbounds is compared with analytical bounds. The second numerical example examinesthe linear visco-elastic behaviour of laminates as used by the automotive industry.References[1] H. Andrä, N. Combaret, J. Dvorkin, E. Glatt, J. Han, M. Kabel, Y. Keehm, F.Krzikalla, M. Lee, C. Madonna, M. Marsh, T. Mukerji, E.H. Saenger, R. Sain, N.Saxena, S. Staub, A. Wiegmann, and X. Zhan. Digital rock physics benchmarks PartI: Imaging and segmentation. Computers & Geosciences, In Press, Available online 5.Oct. 2012. A fast numerical solver to compute precise bounds of effective propertiesof multi-phase elastic composites is presented in contrast to analytical estimates likeHashin-Shtrikman bounds.Analytical homogenization methods fulfil the requirements (with respect to accuracy,computational effort and generality of the microstructures) for predicting effectiveproperties of multi-phase elastic composites only for simple shaped inclusions. Curvedfibers and even more complex non-convex inclusions cannot be considered or leadto bad approximations at least for higher stiffness ratios. Furthermore, the usage ofanalytical homogenization on base of micro-tomographies often requires additionalimage processing and image analysis steps. Since micro-tomographies become moreand more mainstream in material science, numerical homogenization as additional toolfor image processing software is qualified for highly precise predictions directly fromthree-dimensional segmented images.For numerical homogenization the equations of elasticity are formulated as integralequations of Lippmann-Schwinger type [6, 4], which can be efficiently solved by usingFast Fourier Transformations (FFT). This approach is particularly suited for digitalimages (CT images) of complex microstructures and needs much less computationaleffort than finite element schemes to predict the effective properties [1, 2]. Althoughthis method is well-known [5, 3], the usage of this method to compute lower and upperbounds is new.A first numerical test for a simple microstructure demonstrates the numericalconvergence with respect to the resolution of the microstructure. The quality of the newbounds is compared with analytical bounds. The second numerical example examinesthe linear visco-elastic behaviour of laminates as used by the automotive industry.References[1] H. Andrä, N. Combaret, J. Dvorkin, E. Glatt, J. Han, M. Kabel, Y. Keehm, F.Krzikalla, M. Lee, C. Madonna, M. Marsh, T. Mukerji, E.H. Saenger, R. Sain, N.Saxena, S. Staub, A. Wiegmann, and X. Zhan. Digital rock physics benchmarks PartI: Imaging and segmentation. Computers & Geosciences, In Press, Available online 5.Oct. 2012. [2] H. Andrä, N. Combaret, J. Dvorkin, E. Glatt, J. Han, M. Kabel, Y. Keehm, F.Krzikalla, M. Lee, C. Madonna, M. Marsh, T. Mukerji, E.H. Saenger, R. Sain, N.Saxena, S. Staub, A. Wiegmann, and X. Zhan. Digital rock physics benchmarks -Part II: Computing effective properties. Computers & Geosciences, In Press, Availableonline 5. Oct. 2012.[3] S. Brisard and L. Dormieux. FFT-based methods for the mechanics of composites:A general variational framework. Computational Materials Science, 49(3), 663–671(2010).[4] E. Kröner. Bounds for effective elastic moduli of disordered materials. Journal of theMechanics and Physics of Solids, 25(2), 137 – 155 (1977).[5] H. Moulinec and P. Suquet. A numerical method for computing the overall responseof nonlinear composites with complex microstructure. Computer Methods in AppliedMechanics and Engineering, 157(12), 69 – 94 (1998).[6] R. Zeller and P. H. Dederichs. Elastic constants of polycrystals. Physica Status Solidi(b), 55(2), 831–842 (1973). Modelling and simulation of the temperature-dependentbehaviour of supported polymer films Alexander Lion, Michael Johlitz, Christoph Mittermeier, and Christoph LieblInstitute of Mechanics,Universität der Bundeswehr München, Neubiberg, Germany Abstract. In order to comprehend the thermomechanical behaviour of glass-formingpolymer films which are deposited on thermally deformable substrates it isindispensable to take the lateral geometric constraints into account. They are causedby differences in the thermal expansion behaviour between the substrate and the filmand provoke the evolution of stresses. Since these stresses depend on the temperatureprocess, they influence the specific heat of the film and change during physical ageing. In order to comprehend the thermomechanical behaviour of glass-formingpolymer films which are deposited on thermally deformable substrates it isindispensable to take the lateral geometric constraints into account. They are causedby differences in the thermal expansion behaviour between the substrate and the filmand provoke the evolution of stresses. Since these stresses depend on the temperatureprocess, they influence the specific heat of the film and change during physical ageing. Fig. 1. Sketch of the geometry and cooling rate-dependent lateral stresses in the film In the presentation, a novel constitutive approach is applied and adapted to simulateand to analyse the temperature rate-dependent response behaviour of constrainedthermoviscoelastic films. The focus of the presentation is the physical understandingof the film behaviour and the interpretation of the simulated results. The theory is justshortly discussed. The highlights of this study can be summarized as follows:• Explicit relations are obtained for the specific heat of the supported film, the normalstrain and the lateral stress.• The magnitude of the lateral stress at temperatures below the glass transitiondepends strongly on the cooling rate (see Fig. 1).• The specific heat of the supported film is principally different from the isobaricspecific heat of the stress-free bulk material. • The glass transition temperatures of the constrained film and the stress-free bulkmaterial are nearly equal.If the model is reduced to the special case of linear thermoelastic films, then simplerelations for the specific heat of the film (is the isobaric specific heat of the free polymerfilm), the lateral stress and the normal strain can be derived: σ =−E0 (κ0 − κs)1− ν0θ, 2 =(κ0 +2 ν01− ν0(κ0 − κs))θ cF =(1 +θθref)(cp0 − 2E0 κ0 θrefρ(1− ν0)(κ0 − κs))(1) As it can be seen, all these quantities depend on the difference between the thermalexpansion coefficients of the substrate and the film. Numerical modeling of a hydrogel diffraction grating ona substrate used for pH sensingMaïté Marchant, Florence Labesse-Jied, Nikolay Gippius, and Yuri Lapusta1 Clermont Université, Université Blaise Pascal, Institut Pascal, Aubière cedex, France2 Clermont Université, Université Blaise Pascal, IUT d’Allier, Institut Pascal, Montluçon, France3 Institut Pascal, UMR 6602 CNRS, Université Blaise Pascal, Aubière, France4 French Institute of Advanced Mechanics, Institut Pascal / IFMA / CNRS / Clermont Université, Aubière Cedex,France Abstract. Many engineering applications involve stimuli-responsive hydrogels thatswell under the constraint of hard materials or substrates. The hydrogels are networksof polymers that can imbibe a solution and swell under the action of different stimulisuch as light, temperature, magnetic field or pH. One of numerous applications ofa pH-sensitive hydrogel is a diffractometric biochemical sensor reported in [1]. It iscomposed of a hydrogel diffraction grating situated on a hard substrate. The aim ofthe present study is to develop a numerical model of such a bi-material device. Adiffraction grating on a substrate is analysed. The grating is made of a pH-sensitivehydrogel that is capable of swelling or shrinking with pH changes. The system ismodeled using the approach proposed in [2]. Note that measurement of pH of asolution is possible by comparing the photonic properties of smart hydrogel gratingsbefore and after swelling due to the pH changes. In other words, it is possible tolink the reflected beam measurement with the pH value. First, the hydrogel gratingdeformation is calculated as a function of the pH. Further, the diffraction intensitiesare analysed for different hydrogel grating deformations. A comparison between thenumerical results and experimental measurements from the literature [1] is carried outto validate the developed model. The proposed model allows studying and predictingthe mechanical and photonics behavior of the smart hydrogel gratings connected tosubstrates for pH-detection.References[1] C.-L. Chang, Z. Ding, V. N. L. R. Patchigolla, B. Ziaie, and C. A. Savran,Diffractometric Biochemical Sensing with Smart Hydrogels, IEEE SENSORS 2010Conference, 1617-1621[2] R. Marcombe, S. Q. Cai, W. Hong, X. H. Zhao, Y. Lapusta and Z. G. Suo: A theoryof constrained swelling of a pH-sensitive hydrogel, Soft Matter 6, 784-793 (2010) Many engineering applications involve stimuli-responsive hydrogels thatswell under the constraint of hard materials or substrates. The hydrogels are networksof polymers that can imbibe a solution and swell under the action of different stimulisuch as light, temperature, magnetic field or pH. One of numerous applications ofa pH-sensitive hydrogel is a diffractometric biochemical sensor reported in [1]. It iscomposed of a hydrogel diffraction grating situated on a hard substrate. The aim ofthe present study is to develop a numerical model of such a bi-material device. Adiffraction grating on a substrate is analysed. The grating is made of a pH-sensitivehydrogel that is capable of swelling or shrinking with pH changes. The system ismodeled using the approach proposed in [2]. Note that measurement of pH of asolution is possible by comparing the photonic properties of smart hydrogel gratingsbefore and after swelling due to the pH changes. In other words, it is possible tolink the reflected beam measurement with the pH value. First, the hydrogel gratingdeformation is calculated as a function of the pH. Further, the diffraction intensitiesare analysed for different hydrogel grating deformations. A comparison between thenumerical results and experimental measurements from the literature [1] is carried outto validate the developed model. The proposed model allows studying and predictingthe mechanical and photonics behavior of the smart hydrogel gratings connected tosubstrates for pH-detection.References[1] C.-L. Chang, Z. Ding, V. N. L. R. Patchigolla, B. Ziaie, and C. A. Savran,Diffractometric Biochemical Sensing with Smart Hydrogels, IEEE SENSORS 2010Conference, 1617-1621[2] R. Marcombe, S. Q. Cai, W. Hong, X. H. Zhao, Y. Lapusta and Z. G. Suo: A theoryof constrained swelling of a pH-sensitive hydrogel, Soft Matter 6, 784-793 (2010) Micromechanical modeling of short fiber reinforcedcomposites with orientation dataViktor Müller, Thomas Böhlke, Felix Dillenberger, and Stefan Kolling1 Institute of Engineering Mechanics,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany2 Mechanics and Simulation,Fraunhofer-LBF, Darmstadt, Germany Abstract. Nowadays, short fiber reinforced plastics play a crucial role in theconstruction process. By using this class of material, the design engineer can notonly benefit from the advantageous ratio of stiffness to weight in comparison tothe pure materials like polypropylene or glass but also from the possibility of alow-cost manufacturing. Components made of short fiber reinforced plastics areusually fabricated by an injection or compression molding process.Apart from the orientation distribution of the reinforcing fibers, the particularmanufacturing process influences as well the geometry and spatial distribution of thefibers. With respect to the microstructural properties, short-fiber reinforced polymersshow, therefore, heterogeneities on different length scales which results in a topologicaldependence of the mechanical properties [1].The variation of the microstructural parameters like orientation and aspect ratio ofa single fiber requires a consideration of these characteristics in the context of amicromechanical approach. Hence, besides a two step approach, the self-consistentmethod is utilized to get the elastic properties of several microstructures. For thatreason, specific artificial microstructures are considered which statistically representdifferent positions of a part fabricated by injection molding [2].Furthermore, for an experimentally determined orientation distribution, the effectiveelastic properties are calculated and the local fiber stresses are discussed.References[1] Shao-Yun Fu, Bernd Lauke: Effects of fiber length and fiber orientation distributionson the tensile strength of short-fiber-reinforced polymers, Composites Science andTechnology, 56, 1179–1190 (1996).[2] Mahesh Gupta, K.K. Wang: Fiber Orientation and Mechanical Properties ofShort-Fiber-Reinforced Injection-Molded Composites: Simulated and ExperimentalResults, Polymer Composites, 14, 367–382 (1993). Nowadays, short fiber reinforced plastics play a crucial role in theconstruction process. By using this class of material, the design engineer can notonly benefit from the advantageous ratio of stiffness to weight in comparison tothe pure materials like polypropylene or glass but also from the possibility of alow-cost manufacturing. Components made of short fiber reinforced plastics areusually fabricated by an injection or compression molding process.Apart from the orientation distribution of the reinforcing fibers, the particularmanufacturing process influences as well the geometry and spatial distribution of thefibers. With respect to the microstructural properties, short-fiber reinforced polymersshow, therefore, heterogeneities on different length scales which results in a topologicaldependence of the mechanical properties [1].The variation of the microstructural parameters like orientation and aspect ratio ofa single fiber requires a consideration of these characteristics in the context of amicromechanical approach. Hence, besides a two step approach, the self-consistentmethod is utilized to get the elastic properties of several microstructures. For thatreason, specific artificial microstructures are considered which statistically representdifferent positions of a part fabricated by injection molding [2].Furthermore, for an experimentally determined orientation distribution, the effectiveelastic properties are calculated and the local fiber stresses are discussed.References[1] Shao-Yun Fu, Bernd Lauke: Effects of fiber length and fiber orientation distributionson the tensile strength of short-fiber-reinforced polymers, Composites Science andTechnology, 56, 1179–1190 (1996).[2] Mahesh Gupta, K.K. Wang: Fiber Orientation and Mechanical Properties ofShort-Fiber-Reinforced Injection-Molded Composites: Simulated and ExperimentalResults, Polymer Composites, 14, 367–382 (1993). Modelling the deformation behaviour of atwill-weave-reinforced thermoplast using the anglebisector frameworkAndreas Rösner, Kay Weidenmann, Luise Kärger, and Frank Henning1 Institute for Vehicle System Technology,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany2 Institute for Applied Materials,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. Twill-weave-reinforcements offer a good compromise regarding structuralperformance, handling and draping behaviour. Therefore, they are well suited for loadcarrying structures based on fiber-reinforced polymers with complex 3D geometries.Being formed into 3D geometries the twill weave deforms permanently by localchanges in fiber angle. This manufacturing effect has a significant impact on the local,as well as overall mechanical behaviour of the resulting composite structure and has,therefore, to be considered within finite element simulation. Aiming at describing thedeformation behaviour efficiently while taking into account local changes in fiberangle, the angle bisector framework has been identified as a suitable basis for thematerial formulation. Regardless of the local fiber angle, it offers the possibility todescribe each layer of the woven composite as a homogenized orthotropic continuum.However, material properties such as stiffness and strength vary with the change inangle and have, therefore, to be formulated in relation to the fiber angle. Within thiswork the deformation behaviour of a carbon fiber twill-weave-reinforced polyamide 6has been characterized in order to evaluate the ability of the angle bisector frameworkto model this behaviour accurately and efficiently. Therefore, quasi-static tension andcompression tests have been carried out in different material directions and at differentloading speeds to investigate the visco-elastic-plastic behaviour and to determine theelastic constants of the orthotropic material system. Furthermore, tensile tests featuringloading-unloading cycles have been carried out in the angle bisector directions in orderto determine the influence of fiber rotation effects under loading. Twill-weave-reinforcements offer a good compromise regarding structuralperformance, handling and draping behaviour. Therefore, they are well suited for loadcarrying structures based on fiber-reinforced polymers with complex 3D geometries.Being formed into 3D geometries the twill weave deforms permanently by localchanges in fiber angle. This manufacturing effect has a significant impact on the local,as well as overall mechanical behaviour of the resulting composite structure and has,therefore, to be considered within finite element simulation. Aiming at describing thedeformation behaviour efficiently while taking into account local changes in fiberangle, the angle bisector framework has been identified as a suitable basis for thematerial formulation. Regardless of the local fiber angle, it offers the possibility todescribe each layer of the woven composite as a homogenized orthotropic continuum.However, material properties such as stiffness and strength vary with the change inangle and have, therefore, to be formulated in relation to the fiber angle. Within thiswork the deformation behaviour of a carbon fiber twill-weave-reinforced polyamide 6has been characterized in order to evaluate the ability of the angle bisector frameworkto model this behaviour accurately and efficiently. Therefore, quasi-static tension andcompression tests have been carried out in different material directions and at differentloading speeds to investigate the visco-elastic-plastic behaviour and to determine theelastic constants of the orthotropic material system. Furthermore, tensile tests featuringloading-unloading cycles have been carried out in the angle bisector directions in orderto determine the influence of fiber rotation effects under loading. In-situ study of compressive damage evolution inmetal/ceramic composites based on freeze-cast ceramicpreforms Siddhartha Roy, Jan Frohnheiser, Kay André Weidenmann, and Alexander WannerInstitute for Applied Materials,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. Metal/ceramic composites fabricated by infiltrating freeze-cast ceramicpreforms have a random domain structure in the plane orthogonal to the preformfreezing direction. Within each domain the alternating metallic and ceramic lamellaelie almost parallel to each other. The aim of this study is to investigate the effectof orientation of the domains with respect to the direction of compressive stressapplication on the mechanism of damage evolution. Compression tests were carriedout on samples having one, two and multiple domains in-situ inside a scanningelectron microscope. The extent of damage was measured by counting the numberof cracks at specific locations on the sample surface at various applied stresses. Resultsshow that the orientation of the lamellae with respect to the loading direction stronglyinfluences the composite behavior. When loaded parallel to the lamellae the compositeis strong and brittle; however, when the lamellae orientation is more than 30 ◦ thecomposite is soft and ductile and shows a metallic alloy controlled behavior. In sampleshaving two and multiple domains the damage predominantly occurs in regionswith softer orientations. The following primary damage modes have been identified:longitudinal cracking of the ceramic lamellae at 0-10◦, interfacial shear failure at 10-30◦ and transverse cracking of the ceramic lamellae and shear cracks within the metalliclamellae joining two transverse ceramic cracks at lamellae orientations 30-90. Metal/ceramic composites fabricated by infiltrating freeze-cast ceramicpreforms have a random domain structure in the plane orthogonal to the preformfreezing direction. Within each domain the alternating metallic and ceramic lamellaelie almost parallel to each other. The aim of this study is to investigate the effectof orientation of the domains with respect to the direction of compressive stressapplication on the mechanism of damage evolution. Compression tests were carriedout on samples having one, two and multiple domains in-situ inside a scanningelectron microscope. The extent of damage was measured by counting the numberof cracks at specific locations on the sample surface at various applied stresses. Resultsshow that the orientation of the lamellae with respect to the loading direction stronglyinfluences the composite behavior. When loaded parallel to the lamellae the compositeis strong and brittle; however, when the lamellae orientation is more than 30 ◦ thecomposite is soft and ductile and shows a metallic alloy controlled behavior. In sampleshaving two and multiple domains the damage predominantly occurs in regionswith softer orientations. The following primary damage modes have been identified:longitudinal cracking of the ceramic lamellae at 0-10◦, interfacial shear failure at 10-30◦ and transverse cracking of the ceramic lamellae and shear cracks within the metalliclamellae joining two transverse ceramic cracks at lamellae orientations 30-90. A cell model study of ternary polymer blends Konrad Schneider and Thomas SeeligInstitute of Mechanics,Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany Abstract. Like many engineering materials, polymer blends have a heterogenousmicrostructure that affects the macroscopic behaviour. The polymer blend underconsideration here is PC/ABS (polycarbonate/acrylonitrile-butadiene-styrene), awidley used industrial thermoplastic. A remarkable benefit of PC/ABS blends istheir enhanced fracture toughness which accrues from complex micromechanicaldeformation processes. To gain a better understanding of these processes inperspective of predicting macroscopic effects like fracture and failure, a cell modelstudy of the fully resolved three-phase microstructure is conducted. While the twothermoplastic constituents, polycarbonate and styrene-acrylonitrile, are individuallydescribed utilizing the visco-plastic Boyce model, the soft rubber particles (butadiene)are treated as voids. From the cell model subjected to uniform macroscopic loading,the effect of the composition on microscale deformation processes is analyzednumerically. Furthermore, results in terms of local as well as macroscopic quantitiesare qualitatively interpreted with respect to the macroscopic failure behaviour. Like many engineering materials, polymer blends have a heterogenousmicrostructure that affects the macroscopic behaviour. The polymer blend underconsideration here is PC/ABS (polycarbonate/acrylonitrile-butadiene-styrene), awidley used industrial thermoplastic. A remarkable benefit of PC/ABS blends istheir enhanced fracture toughness which accrues from complex micromechanicaldeformation processes. To gain a better understanding of these processes inperspective of predicting macroscopic effects like fracture and failure, a cell modelstudy of the fully resolved three-phase microstructure is conducted. While the twothermoplastic constituents, polycarbonate and styrene-acrylonitrile, are individuallydescribed utilizing the visco-plastic Boyce model, the soft rubber particles (butadiene)are treated as voids. From the cell model subjected to uniform macroscopic loading,the effect of the composition on microscale deformation processes is analyzednumerically. Furthermore, results in terms of local as well as macroscopic quantitiesare qualitatively interpreted with respect to the macroscopic failure behaviour. Numerical Evaluation of Fiber Composites Accountingfor Delamination Jaan-Willem Simon, Bertram Stier, and Stefanie ReeseInstitute of Applied Mechanics,RWTH Aachen University, Aachen, Germany Abstract. In this paper, we consider fiber composites consisting of several layers, eachof which is composed of a woven fabric embedded in a matrix material. The accordingconstitutive behavior is anisotropic and typically highly nonlinear. Furthermore, thematerial’s response in tension and compression can differ significantly. In order tocapture this rather complex behavior, we use a micromechanically motivated modeldeveloped by Reese [1]. In this model, the directions of the fibers are represented usingthe concept of structural tensors, making it particularly suitable for fiber reinforcedcomposites.The use of a fully three-dimensional material model strongly suggests using solidelements. On the other hand, fiber composites are mostly applied in thin shell-likestructures, where shell elements should usually be preferred. Therefore, we use thesolid-shell element proposed by Schwarze et al. in [2], which combines the advantagesof both solid elements and shell elements at the same time.In addition, a reduced integration scheme is used within the shell plane, whereas a fullintegration is used in thickness direction. Thus, an arbitrary number of integrationpoints can be chosen over the shell thickness. This is advantageous, because itallows an accurate prediction of the stress distribution in thickness direction, whichis important if delamination of different layers of the composite shall be considered.Therefore, the proposed element is especially suitable, since the through-the-thicknessstress distribution can be computed accurately even in thin shell-like structures.References[1] S. Reese: Meso-macro modelling of fiber-reinforced rubber-like compositesexhibiting large elastoplastic deformation, Int J Solids & Struct, 40, 951–980, (2003).[1] M. Schwarze, S. Reese: A reduced integration solid-shell finite element based onthe EAS and the ANS concept large deformation problems, Int J Numer MethodsEngng, 85, 289–329, (2011). In this paper, we consider fiber composites consisting of several layers, eachof which is composed of a woven fabric embedded in a matrix material. The accordingconstitutive behavior is anisotropic and typically highly nonlinear. Furthermore, thematerial’s response in tension and compression can differ significantly. In order tocapture this rather complex behavior, we use a micromechanically motivated modeldeveloped by Reese [1]. In this model, the directions of the fibers are represented usingthe concept of structural tensors, making it particularly suitable for fiber reinforcedcomposites.The use of a fully three-dimensional material model strongly suggests using solidelements. On the other hand, fiber composites are mostly applied in thin shell-likestructures, where shell elements should usually be preferred. Therefore, we use thesolid-shell element proposed by Schwarze et al. in [2], which combines the advantagesof both solid elements and shell elements at the same time.In addition, a reduced integration scheme is used within the shell plane, whereas a fullintegration is used in thickness direction. Thus, an arbitrary number of integrationpoints can be chosen over the shell thickness. This is advantageous, because itallows an accurate prediction of the stress distribution in thickness direction, whichis important if delamination of different layers of the composite shall be considered.Therefore, the proposed element is especially suitable, since the through-the-thicknessstress distribution can be computed accurately even in thin shell-like structures.References[1] S. Reese: Meso-macro modelling of fiber-reinforced rubber-like compositesexhibiting large elastoplastic deformation, Int J Solids & Struct, 40, 951–980, (2003).[1] M. Schwarze, S. Reese: A reduced integration solid-shell finite element based onthe EAS and the ANS concept large deformation problems, Int J Numer MethodsEngng, 85, 289–329, (2011). Modeling of the Deformation and Fracture Behavior ofShort Fiber Reinforced Plastics Potential andLimitations Markus Stommel and Jan-Martin KaiserChair for Polymer Materials,Saarland University, Saarbrücken, Germany Abstract. In the last decade, several authors have successfully predicted damage andstrength of composite materials with mean-field homogenization models (e.g., [1, 2,3]). These micromechanical models are based on the Eshelby solution for sphericalinclusions embedded in a matrix and they allow the calculation of the mean stressesand strains in the constituents. These mean values are commonly the starting point forprogressive damage and failure modeling. In the authors ́ contribution an incrementalmean-field approach is chosen to calculate the elasto-plastic behavior of compositeswith arbitrarily dimensioned inclusions. Furthermore, the implemented model offersthe possibility to consider a non-unidirectional composite as a composition ofweighted unidirectional sub-domains. The authors show, that the mean values forstresses and strains of the constituents of a representative volume element are in goodaccordance with the results achieved by the chosen mean-field homogenization model.As a new feature, the implementation is extended to be able to consider the existingstrain and stress distribution based on the calculated mean values, the inclusionsdimension and orientation as previously shown in [4]. Since it is well known, thatthis distribution and especially the local maximums are dominant for failure and theplastic composite behavior, they are of special interest in engineering applications likestrength prediction. Hence, the developed model is applied to a short-fiber reinforcedpolymer composite in combination with known failure models.References[1] F. Desrumaux, F. Meraghni, L. Benzeggagh: Micromechanical Modelling Coupledto a Reliability Approach for Damage Evolution Prediction in Composite Materials,Appl. Compos. Mater., 7, 231–250 (2000).[2] H. K. Lee, S. Simunovic: Modeling of Progressive Damage in Aligned andRandomly Oriented Discontinuous Fiber Polymer Matrix Composites, CompositesPart B, 31, 77–86 (2000).[3] B. N. Nguyen, V. Kunc: An Elastic-Plastic Damage Model for Long-FiberThermoplastics, Int. J. Damage Mech., 19, 691–725 (2010).[4] J.-M. Kaiser, M. Stommel: Micromechanical Modeling and Strength Prediction ofShort Fiber Reinforced Polymers, J. Polymer Eng., 32, 43–52 (2012). In the last decade, several authors have successfully predicted damage andstrength of composite materials with mean-field homogenization models (e.g., [1, 2,3]). These micromechanical models are based on the Eshelby solution for sphericalinclusions embedded in a matrix and they allow the calculation of the mean stressesand strains in the constituents. These mean values are commonly the starting point forprogressive damage and failure modeling. In the authors ́ contribution an incrementalmean-field approach is chosen to calculate the elasto-plastic behavior of compositeswith arbitrarily dimensioned inclusions. Furthermore, the implemented model offersthe possibility to consider a non-unidirectional composite as a composition ofweighted unidirectional sub-domains. The authors show, that the mean values forstresses and strains of the constituents of a representative volume element are in goodaccordance with the results achieved by the chosen mean-field homogenization model.As a new feature, the implementation is extended to be able to consider the existingstrain and stress distribution based on the calculated mean values, the inclusionsdimension and orientation as previously shown in [4]. Since it is well known, thatthis distribution and especially the local maximums are dominant for failure and theplastic composite behavior, they are of special interest in engineering applications likestrength prediction. Hence, the developed model is applied to a short-fiber reinforcedpolymer composite in combination with known failure models.References[1] F. Desrumaux, F. Meraghni, L. Benzeggagh: Micromechanical Modelling Coupledto a Reliability Approach for Damage Evolution Prediction in Composite Materials,Appl. Compos. Mater., 7, 231–250 (2000).[2] H. K. Lee, S. Simunovic: Modeling of Progressive Damage in Aligned andRandomly Oriented Discontinuous Fiber Polymer Matrix Composites, CompositesPart B, 31, 77–86 (2000).[3] B. N. Nguyen, V. Kunc: An Elastic-Plastic Damage Model for Long-FiberThermoplastics, Int. J. Damage Mech., 19, 691–725 (2010).[4] J.-M. Kaiser, M. Stommel: Micromechanical Modeling and Strength Prediction ofShort Fiber Reinforced Polymers, J. Polymer Eng., 32, 43–52 (2012). Participants TitleNameInstitutionE-Mail-Address M.Sc.R.Al-KinaniInstituteofEngineeringMechanics TechnischeUniversitätClausthal,[email protected] Prof.Dr.-Ing.T.BöhlkeInstituteofEngineeringMechanics(ContinuumMechanics) KarlsruheInstituteofTechnology(KIT) Karlsruhe,[email protected] Prof.H.J.BöhmInstituteofLightweightDesignandStructuralBiomechanics ViennaUniversityofTechnology,[email protected] Dipl.-Ing.B.BrylkaInstituteofEngineeringMechanics(ContinuumMechanics) KarlsruheInstituteofTechnology(KIT) Karlsruhe,[email protected] Dipl.-Ing.I.CaylakChairofEngineeringMechanics(LT) UniversityofPaderborn Paderborn,[email protected] M.Sc.C.ChengChairofEngineeringMechanics(LT) UniversityofPaderborn Paderborn,[email protected] Dipl.-Math.C.DammannChairofEngineeringMechanics(LT) UniversityofPaderborn Paderborn,[email protected]