arXiv subjects

S. Korte-Kerzel

Publications and source records attributed to S. Korte-Kerzel.

10 recordsLinked to original sources

arXiv2024

Origins of limited non-basal plasticity in the μ-phase at room temperature

We unveil a new non-basal slip mechanism in the μ-phase at room temperature using nanomechanical testing, transmission electron microscopy and atomistic simulation. The (1-105) planar faults with a displacement vector of 0.07[-5502] can be formed by dislocation glide. They do not disrupt the Frank-Kasper packing and therefore enable the accommodation of plastic strain at low temperatures without requiring atomic diffusion. The intersections between the (1-105) planar faults and basal slip result in stress concentration and crack nucleation during loading.

cond-mat.mtrl-sci↗

arXiv2023

Exploring Solute Behavior and Texture Selection in Magnesium Alloys at the Atomistic Level

This study advances our understanding of how chemical binding and solute distribution impact grain boundary segregation behavior and subsequent annealing texture modification in lean Mg-X-Zn alloys (X = RE or Ca). Notably, differences in Ca and Gd solute behavior at grain boundaries were revealed, where Ca exhibited stronger binding to vacancy sites than Gd, resulting in elevated Ca segregation and an RD-TD-type texture. The introduction of Zn showed significant synergistic effects on solute clustering, with Gd-Zn pairs forming more favorably than Ca-Zn pairs, leading to a strong synergy between Zn and Gd. This promoted their co-segregation and high concentration at the grain boundary, generating a unique TD-spread texture. In contrast, weaker binding in Ca-Zn pairs did not affect Ca segregation but influenced Zn segregation, which underscores the importance of solute binding behavior in alloy design concepts. Additionally, the combined atomicscale experiments and ab initio predictions provide strong evidence that selective texture development in Mg alloys is tied to heterogeneous solute-boundary interactions, where the sensitivity of the binding energy to volumetric strain affects solute segregation at grain boundaries, resulting in varying grain boundary mobilities and specific texture component growth. It also emphasizes that solute behavior in clustering and segregation is influenced not only by atomic size but also by chemical binding strength with vacancies or co-added Zn.

cond-mat.mtrl-sci↗

arXiv2023

Metallurgical synthesis methods for Mg-Al-Ca scientific model materials

Mg-based alloys are industrially used for structural applications, both as solid solutions alloys and as composites containing intermetallic compounds. However, a further development in terms of mechanical properties requires the investigation of underlying causalities between synthesis, processing and microstructure to adjust the mechanical and the corrosion properties, ideally down to the near atomic scale. Such fundamental scientific investigations with high resolution characterisation techniques require model materials of exceptionally high purity and strictly controlled microstructure e.g. with respect to grain size, morphology, chemical homogeneity as well as content and size of oxide inclusions. In this context, the Mg-Al-Ca system appears exceptionally challenging from a metallurgical perspective due to the high reactivity and high vapor pressures, so that conventional industrial techniques cannot be successfully deployed. Here, we demonstrate the applicability of various scientific synthesis methods from arc melting over solution growth to diffusion couples, extending to effects and parameters for thermo-mechanical processing. Suitable pathways to overcome the specific challenges of the Mg-Al-Ca system are demonstrated, as well as the persistent limitations of the current state of the art laboratory metallurgy technology.

cond-mat.mtrl-sci↗

arXiv2023

Strengthening of Mg-Al-Ca alloys with C15 and C36 Laves phases

The Laves phase skeleton in cast Mg-Al-Ca alloys is known to provide considerable strengthening. Laves phases such as CaMg$_2$ (C14), Ca(Al,Mg)$_2$ (C36), and CaAl2 (C15) have high melting points, high hardness at room and elevated temperatures, but unfortunately are inherently brittle. Mg-Al-Ca alloys thus have good creep properties but limited ductility. An understanding of the co-deformation behaviour of $α$-Mg and Laves phases is essential for optimising the strength-ductility balance of these alloys. Here, we study the mechanical behaviour of a Mg-4.65Al-2.82Ca alloy using micropillar compression in the $α$-Mg matrix, at $α$-Mg/C36 and $α$-Mg/C15 interfaces and in the C15 phase in combination with scanning electron microscopy (SE imaging), electron backscatter diffraction (EBSD), transmission Kikuchi diffraction (TKD), and low-kV scanning transmission electron microscopy (STEM). We show that both, C15 and C36, Laves phases provide considerable strengthening to the $α$-Mg matrix by delaying the onset of basal slip and extension twinning, while only the C36 phase appears to allow a certain extent of slip transfer/ plastic co-deformation, in spite of its greater anisotropy compared with the cubic C15 phase. We therefore conclude based on these results that strengthening of the $α$-Mg matrix by the C36 Laves phase is preferable given that it combines easy skeleton formation with some co-deformation and considerable stability at common application temperatures of magnesium alloys.

cond-mat.mtrl-sci↗

arXiv2023

Plasticity of the Nb-rich μ-Co7Nb6 phase at room temperature and 600 °C

The μ-phase is a common precipitation phase in superalloys and it exists in a wide composition and temperature range. As such, we study the influences of composition and temperature on its plasticity by micropillar compression tests and transmission electron microscopy. The micropillars of the μ-Co7Nb6 phase deform plastically by basal slip at either room temperature or 600 oC. At room temperature, the Co-49Nb and Co-52Nb micropillars show high yield stresses and an abrupt large strain burst at the onset of yielding regardless of orientation, whereas the Co-54Nb micropillars oriented for basal slip yield at much lower stresses and show intermittent small strain bursts during plastic deformation. While the Co-49Nb micropillars deform by full dislocation slip on the basal plane at room temperature, the Co-54Nb micropillars deform by partial dislocation slip on the basal plane. At 600 oC, the Co-49Nb micropillars oriented for basal slip show stable and continuous plasticity and their critical resolved shear stress decreases dramatically. The plastic deformation of the Co-49Nb micropillars occurs via partial dislocation slip on the basal plane at 600 oC. Based on the geometric γ-surfaces for all potential basal slip planes, we explore where and why the glide of full and partial dislocations on the basal plane occurs in the μ-Co7Nb6 phase.

cond-mat.mtrl-sci↗

arXiv2021

Plasticity of the Al$_{2}$Cu θ-phase from ambient temperature to 300°C

The investigation of the deformation behaviour of intermetallic phases is mostly limited to high temperatures due to their low ductility at ambient temperature. Therefore, within this study, nanoindentation experiments on the Al$_{2}$Cu phase were performed from ambient temperature up to 300°C in conjunction with TEM investigations of the deformed material. It was found that the Al$_{2}$Cu phase starts to soften from temperatures above 150°C. The low temperature deformation behaviour was dominated by serrated yielding and transitioned towards a smooth deformation behaviour above 150°C. No slip traces were observed in the vicinity of the indents in both temperature regimes. The predominant dislocations observed after ambient temperature deformation and elevated temperature deformation are assumed to belong to the same operating slip systems. Therefore, the underlying deformation mechanism for both temperatures appears to be the same and thermally activated.

cond-mat.mtrl-sci↗

arXiv2021

Co-deformation Between the Metallic Matrix and Intermetallic Phases in a Creep-Resistant Mg-3.68Al-3.8Ca Alloy

The microstructure of Mg-Al-Ca alloys consists of a hard intra- and intergranular eutectic Laves phase network embedded in a soft $α$-Mg matrix. For such heterogeneous microstructures, the mechanical response and co-deformation of both phases under external load are not yet fully understood. We therefore used nano- and microindentation in combination with electron microscopy to study the deformation behaviour of an Mg-3.68Al-3.8Ca alloy. We found that the hardness of the Mg$_2$Ca phase was significantly larger than the $α$-Mg phase and stays constant within the measured temperature range. The strain rate sensitivity of the softer $α$-Mg phase and of the interfaces increased while activation volume decreased with temperature. The creep deformation of the Mg$_2$Ca Laves phase was significantly lower than the $α$-Mg phase at 170 $^{\circ}$C. Moreover, the deformation zone around and below microindents depends on the matrix orientation and is influenced by the presence of Laves phases. Most importantly, slip transfer from the $α$-Mg phase to the (Mg,Al)$_2$Ca Laves phase occurred, carried by the basal planes. Based on the observed orientation relationship and active slip systems, a slip transfer mechanism from the soft $α$-Mg phase to the hard Laves phase is proposed. Further, we present implications for future alloy design strategies.

cond-mat.mtrl-sci↗

arXiv2021

Dislocation-mediated plasticity in the Al$_{2}$Cu θ-phase

The deformation behaviour of the intermetallic Al$_{2}$Cu-phase was investigated using atomistic simulations and micropillar compression, where slip on the unexpected {211} and {022} slip planes was revealed. Additionally, all possible slip systems for the intermetallic phases were further evaluated and a preference for the activation of slip systems based on their effective interplanar distances as well as the effective Burgers vector is proposed. The effective interplanar distance corresponds to the manually determined interplanar distance, whereas the effective Burgers vector takes a potential dislocation dissociation into account. This new order is: {211}1/2<111>, {022}1/2<111> and {022}<100>, {110}<001>, {310}<001>, {022}<011>, {110}1/2<111>, {112}<110> and {112}1/2<111> from high to low ratio of deff/beff. Also, data on the critical resolved shear stresses of several of these slip systems were measured.

cond-mat.mtrl-sci↗

arXiv2019

Mechanical Characterisation of the Protective Al$_2$O$_3$ Scale in Cr$_2$AlC MAX phases

MAX phases have great potential under demands of both high-temperature and high-stress performance, with their mixed atomic bonding producing the temperature and oxidation resistance of ceramics with the mechanical resilience of metals. Here, we measure the mechanical properties up to 980C by nanoindentation on highly dense and pure Cr$_2$AlC, as well as after oxidation with a burner rig at 1200C for more than 29 hours. Only modest reductions in both hardness and modulus up to 980C were observed, implying no change in deformation mechanism. Furthermore, micro-cantilever fracture tests were carried out at the Cr$_2$AlC/Cr$_7$C$_3$ and Cr$_7$C$_3$/Al$_2$O$_3$ interfaces after the oxidation of the Cr$_2$AlC substrates with said burner rig. The values are typical of ceramic-ceramic interfaces, below 4 MPa/m, leading to the hypothesis that the excellent macroscopic behaviour is due to a combination of low internal strain due to the match in thermal expansion coefficient as well as the convoluted interface.

physics.app-ph↗

arXiv2019

Investigation of the electroplastic effect using nanoindentation

A promising approach to deform metallic-intermetallic composite materials is the application of electric current pulses during the deformation process to achieve a lower yield strength and enhanced elongation to fracture. This is known as the electroplastic effect. We developed a novel setup to study the electroplastic effect during nanoindentation on individual phases and well-defined interfaces. Using a eutectic Al- Al2Cu alloy as a model material, we compare the electroplastic nanoindentation results to macroscopic electroplastic compression tests. The results of the micro- and macroscopic investigations reveal current induced displacement shifts and stress drops, respectively, with the first displacement shift / stress drop being higher than the subsequent ones. A higher current intensity, higher loading rate and larger pulsing interval all cause increased displacement shifts. This observation, in conjunction with the fact that the first displacement shift is highest, strongly indicates that de-pinning of dislocations from obstacles dominates the mechanical response, rather than solely thermal effects.

cond-mat.mtrl-sci↗