Ingenieurwissenschaften und zugeordnete Tätigkeiten
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The application of epoxy resins is variating from low cost adhesive to high performance plastics. As a result, the choice of monomer, hardener and in particular the curing treatment define the final product properties. For process optimization and ensuring product quality the curing kinetics of epoxy resin needs to be known. This is usually done by use of differential scanning calorimetry (DSC) or rheology measurements.
In the presented study, we will approve the applicability of the heatable near-infrared (NIR) cell 1 as alternative method to determine cure kinetics. This spectroscopic method in the NIR region enables following the cure progress by the characteristic oxirane absorption band 2,3. According to the reactivity of this functional group, the consumption of it should be a key factor for cross linking density and hence the mechanical performance of the material. Kinetic parameters will be provided by non-isothermal heating rates and predicted epoxy conversion for a typical cure treatment (Figure 1). The verification of the investigated cure kinetics is ensured by multiple step curing processes in the in situ NIR heating cell and ex situ on real samples.
In this presentation, we will introduce the heatable near-infrared (NIR) cell to investigate kinetic parameters for various epoxy resins, using diverse curing processes. Advantages and disadvantages of the method will be described as well as the comparison with DSC results.
The nonlinear behaviour of epoxy resins is studied on standard tensile tests. A strain field measurement system is applied (Aramis) in order to monitor local strains. The residual strain is measured by recovering the specimens for up to 68 hours after unloading. The time span the specimen is exposed to load has a large influence on the creeping process and the residual strain after recovering. This is studied by comparison of instantaneous unloading with keeping the specimen under permanent load for thirty minutes. It is shown that moderate differences in the initial strain can lead to large differences in the creep behaviour as well as in the residual strain.
The problems of the limits of continuum mechanics are shown on some examples. The fiber-matrix debonding and subsequent crack propagation in fiber reinforced composites is studied. While Finite Element Analyses predict clear crack surfaces, either following the interface or bridging to the neighbouring fiber forming planes, the actual surfaces are very cliffy. Due to the much larger fracture surfaces and the completely different stress states on the cliffy fracture surfaces the continuum mechanical prediction is far from the actual local behaviour. The phenomenon of local high stresses which re much higher than the macroscopically measured strength of the material is also encountered in general fracture mechanics.
The scale dependency of materials is shown on indentation tests conducted on different scales. From a continuum mechanical point of view it makes no difference if the indentation test is performed on a nano-, micro- or macroscale, because it is a matter of self-similarity. However, in nano- or microindentation tests on a pure polymer using e.g. a Berkovic indentor, the extremely high stress concentrations arising at the indentor tip are domination more or less the whole region around the indentor. In case of a macroscopical test, this zone covers only a small part of the material loaded by the indentor. Accordingly, the results of the different test cannot be scaled up.