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One possible approach to study systematically the influence of the deformation regime on the geometry of geological structures like folds and boudins is analogue modelling. For a complete understanding of the resulting structures, consideration of the third dimension is required. This PhD study deals with scaled analogue modelling under constriction and plane-strain conditions to improve our knowledge of folding and boudinage of lower crustal rocks in space and time. Plasticine is an appropriate analogue material for rocks in the lower crust. Therefore, this material was used for the experiments. The macroscopic behaviour of most types of plasticine is quite similar to rocks undergoing strain-rate softening and strain hardening regardless of the different microscopic aspects of deformation. Therefore, if one is aware that the stress exponent and viscosity increase with increasing strain, the original plasticine types used with stress exponents ranging from 5.8 to 8.0 are adequate for modelling geologic structures. The same holds for plasticine/oil mixtures. Thus, plasticine and plasticine/oil mixtures can be used to model the viscous flow of different rock types in the lower crust. If climb-accommodated dislocation creep and associated steady-state flow is assumed for the natural rocks, the plasticine/oil mixtures should be used, which flow under steady-state conditions. Three different experimental studies of plane-strain coaxial deformation of stiff layers, with viscosity η2 and stress exponent n2, embedded in a weak matrix, with viscosity η1 and stress exponent n1, have been carried out. The undeformed samples (matrix plus layer) were cubes with an edge length of 12 cm. All experimental runs have been carried out at T = 25 ± 1°C and varying strain rates ė, ranging from 7.9 x 10 high -6 s high -1 to 1.7 x 10 high -2 s high -1, until a finite longitudinal strain of 30% – 40% was achieved. The first experimental study improved the understanding about the evolution of folds and boudins when the layer is oriented perpendicular to the Y-axis of the finite strain ellipsoid. The rock analogues used were Beck’s green plasticine (matrix) and Beck’s black plasticine (competent layer), both of which are strain-rate softening modelling materials with stress exponent n = ca. 8. The effective viscosity η of the matrix plasticine was changed by adding different amounts of oil to the original plasticine. At a strain rate ė of 10 high -3 s high -1 and a finite strain e of 10%, the effective viscosity of the matrix ranges from 1.2 x 10 high 6 to 7.2 x 10 high 6 Pa s. The effective viscosity of the competent layer has been determined as 4.2 x 10 high 7 Pa s. If the viscosity ratio is large (> ca. 20) and the initial thickness of the competent layer is small, both folds and boudins develop simultaneously. Although the growth rate of the folds seems to be higher than the growth rate of the boudins, the wavelength of both structures is approximately the same as is suggested by analytical solutions. A further unexpected, but characteristic, aspect of the deformed competent layer is a significant increase in thickness, which can be used to distinguish plane-strain folds and boudins from constrictional folds and boudins. In the second experimental study, the impact of varying strain rates on growing folds and boudins under plane strain have been investigated. The strain rates used range from 7.9 x 10 high -6 s high -1 to 1.7 x 10 high -2 s high -1. The stiff layer and matrix consist of non-linear viscous Kolb grey and Beck’s green plasticine, respectively, both of which are strain-rate softening modelling materials with power law exponents (n) and apparent viscosities (η) ranging from 6.5 to 7.9 and 8.5 x 10 high 6 to 7.2 x 10 high 6 Pa s, respectively. The effective viscosity (η) of the matrix plasticine was partly modified by adding oil to the original plasticine. At the strain rates used in the experiments the viscosity ratio between layer and matrix ranges between 3 and 10. Different runs have been carried out where the layer was oriented perpendicular to the principal strain axes (X>Y>Z). The results suggest a considerable influence of the strain rate on the geometry of the deformed stiff layer including its thickness. This holds for every type of layer orientation (S ┴ X, S ┴ Y, S ┴ Z). If the stiff layer is oriented perpendicular to the short axis Z of the finite strain ellipsoid, the number of the resulting boudins and the thickness of the stiff layer increase, whereas the length of boudins decreases with increasing strain rate. If the stiff layer is oriented perpendicular to the long axis, X, of the finite strain ellipsoid, enlargement of the strain rate results in increasing wavelength of folds, whereas the number of folds and the degree of thickening of the stiff layer decreased. If the stiff layer is oriented perpendicular to the intermediate Y-axis of the finite strain ellipsoid enlargement of the strain rate results in a decreasing number of boudins and folds associated with increasing wavelengths of both structures. The wavelength of folds is approximately half of the boudins wavelength. This is true for the case where folds and boudins develop simultaneously (S ┴ Y) and for cases where both structures develop independently (folds at S ┴ X and boudins at S ┴ Z). In the third experimental study, scaled analogue experiments have been carried out to demonstrate the growth of plane-strain folds and boudins through space and time. Previous 3D-studies are based only on finite deformation structures. Their results can therefore not be used to prove if both structures grew simultaneously or in sequence. Plane strain acted on a single stiff layer that was embedded in a weak matrix, with the layer oriented perpendicular to the intermediate Y-axis of the finite strain ellipsoid. Two different experimental runs have been carried out using computer tomography (CT) to analyse the results. The first run was carried out without interruption. During the second run, the deformation was stopped in each case at longitudinal strain increments of 10%. Every experiment was carried out at a temperature T of 25°C and a strain rate, ė, of ca. 4 x 10 high -3 s high -1 until a finite longitudinal strain of 40% was achieved with a viscosity contrast m of 18.6 between the non-linear viscous layer (Kolb brown plasticine) and the matrix (Beck’s green plasticine with 150 ml oil kg high -1). The apparent viscosity, η, and the stress exponent, n, for the layer at a strain rate ė = ca. 10 high -3 s high -1 and a finite strain e = 10% are 2.23 x 10 high 7 Pa s and n = 5.8 and for the matrix 1.2 x 10 high 6 Pa s and 10.5. These new data that result from incremental analogue modelling corroborate previous suggestions that folds and boudins are coeval structures in cases of plane-strain coaxial deformation with the stiff layer oriented perpendicular to the intermediate Y-axis of the finite strain ellipsoid. They will be of interest for all workers who are dealing with plane-strain boudins and folds, where the fold axes are parallel to the major axis (X) of the finite strain ellipsoid. As has been demonstrated by the first experimental study, coeval folding and boudinage under plane strain, with S ┴ Y, are associated with a significant increase in the thickness of the competent layer. The latter phenomenon does not occur in other cases of simultaneous folding and boudinage, such as bulk pure constriction. To study the impact of layer thickness on the geometry of folds and boudins under pure constriction, we carried out additional experiments using different types of plasticine for a stiff layer and a weaker matrix to model folding and boudinaging under pure constriction, with the initially planar layer oriented parallel to the Xaxis of the finite strain ellipsoid. The stiff layer and matrix consist of non-linear viscous Kolb brown and Beck’s green plasticine, respectively, both of which are strain-rate softening modelling materials. Six runs have been carried out using thicknesses of the stiff layer of 1, 2, 4, 6, 8 and 10 ± 0.2 mm. All experimental runs were carried out at a temperature T of 30 ± 2°C and a strain rate, ė, of ca. 1.1 x 10 high -4 s high -1 until a finite longitudinal strain of 40% was achieved with a viscosity contrast m of 3.1 between the stiff layer (Kolb brown plasticine) and the matrix (Beck’s green plasticine). The apparent viscosity, η, and the stress exponent, n, for the layer at a strain rate ė = ca. 10 high -3 s high -1 and a finite strain e = 10% are 2.23 x 10 high 7 Pa s and n = 5.8 and for the matrix 7.2 x 10 high 6 Pa s and 7.9. Our results suggest a considerable influence of the initial thickness of the stiff layer on the geometry of the deformed stiff layer. There is no evidence for folding in XY=XZ-sections if the initial thickness of the competent layer is larger than ca. 8 mm. If the initial thickness of the competent layer is set at ca. 10 ± 0.2 mm, both folds and boudins develop simultaneously. However, the growth rate of the boudins seems to be higher than the growth rate of the folds. A further expected, but characteristic, aspect of the deformed competent layer is no change in thickness of the competent layer, which can be used to distinguish plane-strain folds and boudins from constrictional folds and boudins. The model results are important for the analysis and interpretation of deformation structures in rheologically stratified rocks undergoing dislocation creep under bulk constriction. Tectonic settings where constrictional folds and boudins may develop simultaneously are stems of salt diapirs, subduction zones or thermal plumes. To make (paleo) viscosimetric statements possible, the rheological data of the different plasticine types were related to the geometrical data. When comparing the normalized dominant wavelength Wd obtained from the deformed layer of the models with the theoretical dominant wavelength (Ld) calculated using the Smith equation (1977, 1979), the latter probably also holds when folding and boudinage develop simultaneously (S ┴ Y) and when boudins develop independently (S ┴ Z), but can obviously not be applied at very low viscosity ratios as is indicated by the low-strain-rate experiments.