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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.
The present work was devised to address the systematic analysis of samples from a range of Roman non-ferrous metal artefacts from different archaeological contexts and sites in the Roman provinces of Germania Superior. One of the focal points of this study is the provenancing of different lead objects from five important Roman settlements between 15 BC and the beginning of fourth century AD. For this purpose, measurements were made on lead and copper ore samples from the Siegerland, Eifel, Hunsrück and Lahn-Dill area in Germany and supplemented with data from the literature to create a data bank of lead isotope ratios of European deposits. Compositional analysis of lead objects by Electron Microprobe analysis showed that Romans were able to purify lead from ore up to 99%. Multi-Collector Inductively Coupled Plasma Mass-Spectrometry was used to determine the source of lead, which played an important role in nearly all aspects of Roman life. Lead isotope ratios were measured for ore samples from German deposits from the eastern side of the Rhine (Siegerland, Lahn-Dill, Ems) and the western side of the Rhine (Eifel, Hunsrück), which contained enough ore reserves to answer the increasing local demand and are believed to have been mined during the Roman period. This data together with those from Mediterranean ore deposits from the literature was used to establish a data bank. The Mediterranean ore deposits range from Cambrian (high 207Pb/206Pb) to tertiary (lower 207Pb/206Pb) values. In particular, the Cypriot deposits are younger, while the Spanish deposits fall either with the younger Sardic ores or close to the older Cypriot ores. The lead isotope ratios of most German ore deposits fall in between the 208Pb/206Pb vs. 207Pb/206Pb ratios of Sardinia and Cyprus, where the lead isotope signature of ore deposits from France and Britain are also found. Over 240 lead objects were measured from Wallendorf (second century BC to first century AD) Dangstetten (15-8 BC), Waldgirmes (AD 1-10), Mainz (AD 1-300), Martberg (first to fourth centuries AD) & Trier (third to fourth centuries AD). Comparing the lead isotope ratios of lead objects and those from German ores shows that the source of over 85 percent of objects are Eifel ore deposits, but the Roman’s had also imported lead from the Southern Massif Central and from Great Britain. A further topic of this work was the systematic study of the variation of copper isotope ratios in different copper minerals and the mechanisms, which controls copper isotope fractionation in ores deposits. For this purpose, copper isotope analyses were made by Multi-Collector Inductively Coupled Plasma Mass-Spectrometry from a series of hydrothermal copper sulphides and their alteration products. Copper and lead isotope ratios were measured in coexisting phases of chalcopyrite and malachite and also coexisting malachite and azurite. No significant fractionation was observed in malachite-azurite phases, but in chalcopyrite-malachite coexisting phases, malachite always shows a positive fractionation to heavier isotope values. Zhu et al. and Larson et al. showed that isotopic variations in copper principally reflect mass fractionation in response to low temperature processes rather than source heterogeneity. The low temperature ore formation processes are mostly represented by weathering of primary sulphide ores to produce secondary carbonate phases and therefore are usually observed on the surface of ore deposits, which were probably removed during the early Bronze Age. Using this concept, copper isotope ratios were measured in some Early Bronze Age copper alloys and Roman copper alloys. However, no large copper isotope fractionation has been observed. Lead and copper isotope ratios were measured on samples from the Kupferschiefer. Two profiles were investigated; 1) Sangerhausen, which was not directly influenced by the oxidizing brines of Rote Fäule and 2) Oberkatz, where both Rote Fäule-controlled and structure-controlled mineralization were observed. Results from maturation studies of organic matter suggest the maximum temperature affecting the Kupferschiefer did not exceed 130°C. delta-65-Cu ranges between -0.78-+0.58‰, shows a positive correlation with copper concentration. Maximum temperature in the Kupferschiefer profile from Oberkatz is supposed to be around 150°C. delta-65Cu in this profile ranges between -0.71-+0.68‰. The pattern of copper isotope fractionation and copper concentration is same as the for profile of Sangerhausen. Origina lead isotope ratios are strongly overprinted by high concentrations of uranium in bottom of both profiles causing more radiogenic lead.