Mixed mode (I and II) crack tip fields in bulk metallic glasses

Stationary crack tip fields in bulk metallic glasses under mixed mode (I and II) loading are studied through detailed finite element simulations assuming plane strain, small scale yielding conditions. The influence of internal friction or pressure sensitivity on the plastic zones. notch deformation, stress and plastic strain fields is examined for different mode mixities. Under mixed mode loading, the notch deforms into a shape such that one part of its surface sharpens while the other part blunts. Increase in mode If component of loading dramatically enhances the normalized plastic zone size, lowers the stresses but significantly elevates the plastic strain levels near the notch tip. Higher internal friction reduces the peak tangential stress but increases the plastic strain and stretching near the blunted part of the notch. The simulated shear bands are straight and extend over a long distance ahead of the notch tip under mode II dominant loading. The possible variations of fracture toughness with mode mixity corresponding to failure by brittle micro-cracking and ductile shear banding are predicted employing two simple fracture criteria. The salient results from finite element simulations are validated by comparison with those from mixed mode (I and II) fracture experiments on a Zr-based bulk metallic glass.

Stationary crack tip fields in elastic-plastic solids: an overview of recent numerical simulations

In this paper, an overview of some recent numerical simulations of stationary crack tip fields in elastic-plastic solids is presented. First, asymptotic analyses carried out within the framework of 2D plane strain or plane stress conditions in both pressure insensitive and pressure sensitive plastic solids are reviewed. This is followed by discussion of salient results obtained from recent computational studies. These pertain to 3D characteristics of elastic-plastic near-front fields under mixed mode loading, mechanics of fracture and simulation of near-tip shear banding process of amorphous alloys and influence of crack tip constraint on the structure of near-tip fields in ductile single crystals. These results serve to illustrate several important features associated with stress and strain distributions near the crack tip and provide the foundation for understanding the operative failure mechanisms. The paper concludes by highlighting some of the future prospects for this field of study.

Hot deformation behaviour of Mg–3Al alloy—A study using processing map

The hot deformation behaviour of Mg–3Al alloy has been studied using the processing-map technique. Compression tests were conducted in the temperature range 250–550 °C and strain rate range 3 × 10−4 to 102 s−1 and the flow stress data obtained from the tests were used to develop the processing map. The various domains in the map corresponding to different dissipative characteristics have been identified as follows: (i) grain boundary sliding (GBS) domain accommodated by slip controlled by grain boundary diffusion at slow strain-rates (<10−3 s−1) in the temperature range from 350 to 450 °C, (ii) two different dynamic recrystallization (DRX) domains with a peak efficiency of 42% at 550 °C/10−1 s−1 and 425 °C/102 s−1 governed by stress-assisted cross-slip and thermally activated climb as the respective rate controlling mechanisms and (iii) dynamic recovery (DRV) domain below 300 °C in the intermediate strain rate range from 3 × 10−2 to 3 × 10−1 s−1. The regimes of flow instability have also been delineated in the processing map using an instability criterion. Adiabatic shear banding at higher strain rates (>101 s−1) and solute drag by substitutional Al atoms at intermediate strain rates (3 × 10−2 to 3 × 10−1 s−1) in the temperature range (350–450 °C) are responsible for flow instability. The relevance of these mechanisms with reference to hot working practice of the material has been indicated. The processing maps of Mg–3Al alloy and as-cast Mg have been compared qualitatively to elucidate the effect of alloying with aluminum on the deformation behaviour of magnesium.

Sydämen hypertrofian ja kroonisen vajaatoiminnan farmakologinen hoito

Sydämen krooninen vajaatoiminta on merkittävä maailmanlaajuinen ongelma. Se on erilaisten sydän- ja verisuonisairauksien aiheuttama monimuotoinen oireyhtymä. Sydämen vasemman kammion hypertrofia eli sydämen seinämien paksuuntuminen on yksi keskeinen tekijä, joka voi olla sydämen vajaatoiminnan taustalla. Kohonnut verenpaine on yleisin syy, joka johtaa sydänlihaksen paksuuntumiseen. Tämä johtaa sydämen pumppaustoiminnan häiriintymiseen, erilaisten neurohormonaalisten mekanismien aktivaatioon ja edelleen sydämen vajaatoimintaan. Sydämen vajaatoiminnan neurohormonaalisista mekanismeista tärkeimmät ovat reniini-angiotensiini-aldosteroni-järjestelmän ja sympaattisen hermoston aktivaatio, sydämen rakenteiden uudelleenmuovautuminen, sydänlihassolujen apoptoosi ja systeeminen tulehdustila. Sydämen hypertrofiaa ja sen syntymistä pyritään estämään kohonneen verenpaineen lääkehoidolla. Reniini-angiotensiini-aldosteronijärjestelmällä on keskeinen merkitys sydämen vajaatoiminnassa. Sydämen vajaatoiminnan ennusteeseen vaikuttavista lääkeaineista angiotensiinikonvertasin estäjät (ACEestäjät) ovat säilyttäneet johtoasemansa jo vuosikymmenten ajan. Angiotensiinireseptoreiden salpaajien (AT1-salpaajien) odotettiin syrjäyttävän ACE-estäjät sydämen vajaatoiminnan hoidossa, mutta toistaiseksi niitä pidetään vain vaihtoehtoisina lääkkeinä. Sympaattisen hermoston aktivaatiota vähentävät β-salpaajat ovat vakiinnuttaneet asemansa toiseksi tärkeimpänä lääkeryhmänä. Diureetit ovat paljon käytetty lääkeaineryhmä sydämen vajaatoiminnan hoidossa, mutta niistä ainoastaan aldosteroniantagonisteilla on tutkitusti ennustetta parantavaa vaikutusta. Kroonisen vajaatoiminnan hoidossa käytetään edelleen myös digoksiinia. Tulevaisuudessa sydämen vajaatoiminnan ennusteeseen vaikuttavia lääkeaineita voivat olla reniinin estäjät, neutraaliendopeptidaasin estäjät, vasopressiinin antagonistit tai inflammatroisiin sytokiineihin vaikuttavat molekyylit. Erikoistyön kokeellisessa osiossa tarkoituksena oli tutkia sydämen hypertrofian kehittymistä vatsa-aortta kuristetuilla rotilla ja kalsiumherkistäjä levosimendaanin sekä AT1-salpaaja valsartaanin vaikutuksia hypertrofian kehittymiseen. Kokeellisessa osiossa arvioitiin myös sydämen hypertrofian ja vajaatoiminnan jyrsijämallina käytetyn vatsa-aortan kuristuksen (koarktaation) toimivuutta ja vaikutuksia ultraäänen avulla määritettyihin kardiovaskulaarisiin parametreihin. Vatsa-aortta kuristettiin munuaisvaltimoiden yläpuolelta. Kuristus saa aikaan verenpaineen kohoamisen ja sydämen työtaakan lisääntymisen. Pitkittyessään tila johtaa sydänlihaksen hypertrofiaan ja vajaatoimintaan. 64 eläintä jaettiin ryhmiin, siten että jokaiseen ryhmään tuli kahdeksan eläintä. Ryhmistä kolmelle annettiin lääkeaineena levosimendaania kolmella eri päiväannoksella (0,01 mg/kg; 0,10 mg/kg; 1,00 mg/kg) ja kolmelle valsartaania kolmella eri päiväannoksella (0,10 mg/kg; 1,00 mg/kg; 10,00 mg/kg) juomaveden mukana. Lääkitys aloitettiin leikkauksen jälkeen ja jatkettiin kahdeksan viikon ajan. Kardiovaskulaariset parametrit, kuten isovolumetrinen relaksaatioaika (IVRT), vasemman kammion läpimitta systolessa ja diastolessa sekä seinämäpaksuudet, ejektiofraktio (EF), supistuvuusosuus (FS), minuuttitilavuus (CO) ja iskutilavuus (SV) määritettiin kahdeksan viikon kuluttua leikkauksesta ultraäänitutkimuksen avulla. Lisäksi määritettiin eläinten sydämen paino suhteessa ruumiin painoon. Tuloksia verrattiin ilman lääkehoitoa olleeseen koarktaatioryhmään. Eläinmallin toimivuutta arvioitiin vertaamalla koarktaatioryhmän tuloksia sham-operoidun ryhmän tuloksiin. Levosimendaanilla havaittiin työssä sydämen systolista toimintaa parantava vaikutus. Tämä näkyi tendenssinä parantaa ejektiofraktioita ja vasemman kammion supistuvuusosuuksia. Sydämen diastoliseen toimintaan ei kummallakaan lääkeaineella ollut merkittävää vaikutusta. Diastolista toimintaa arvioitiin isovolumetrisen relaksaatioajan muutoksilla. Sydämen hypertrofian kehittymiseen ei kummallakaan lääkeaineella ollut merkittävää vaikutusta. Eläinmallin todettiin mallintavan hyvin sydämen hypetrofiaa ihmisellä, mutta ei niinkään sydämen vajaatoimintaa.

Banded spatiotemporal chaos in sheared nematogenic fluids

We present the results of a numerical study of a model of the hydrodynamics of a sheared nematogenic fluid, taking into account the effects of order-parameter stresses on the velocity profile but allowing spatial variations only in the gradient direction. When parameter values are such that the stress from orientational distortions is comparable to the bare viscous stress, the system exhibits steady states with the characteristics of shear banding. In addition, nonlinearity in the coupling of extensional flow to orientation leads to the appearance of a new steady state in which the features of both spatiotemporal chaos and shear banding are present.

Flow Instabilities and fracture in Ti-6Al-4V deformed in compression at 298 K to 673 K

Uniaxial compression tests were conducted on Ti-6Al-4V specimens in the strain-rate range df 0.001 to 1 s(-1) and temperature range of 298 to 673 K. The stress-strain curves exhibited a peak flow stress followed by flow softening. Up to 523 K, the specimens cracked catastrophically after the flow softening started. Adiabatic shear banding was observed in this regime. The fracture surface exhibited both mode I and II fracture features. The state of stress existing in a compression test specimen when bulging occurs is responsible for this fracture. The instabilities observed in the present tests are classified as ''geometric'' in nature and are state-of-stress dependant, unlike the ''intrinsic'' instabilities, which are dependant on the dynamic constitutive behavior of the material.

Sliding wear of copper against alumina

OFHC copper pins with 10 ppm oxygen were slid against alumina at a load of 50 N and sliding speeds of 0.1 ms(-1) to 4.0 ms(-1) The wear characteristics of copper were related to the strain rate response of copper under uniaxial compression between strain rates of 0.1 s(-1) and 100 s(-1) and temperatures in the range of 298 K to 673 K. It is seen that copper undergoes flow banding at strain rates of 1 s(-1) up to a temperature of 523 K, which is the major instability in the region tested. These flow bands are regions of crack nucleation. The strain rates and temperatures existing in the subsurface of copper slid against alumina are estimated and superimposed on the strain rate response map of copper. The superposition shows that the subsurface of copper slid at low velocities is likely to exhibit flow band instability induced cracking. It is suggested that this is the,reason for the observed high wear rate at low velocities. The subsurface deformation with increasing velocity becomes more homogeneous. This reduces the wear rate. At velocities >2 ms(-1) there is homogenous flow and extrusion of thin (10 mu m) bands of material out of the trailing edge. This results in the gradual increase of wear rate with increasing velocity above 2.0 ms(-1).

Microstructural evolution in liquid metal processed Al-alloy/SiCp composites

Al-Zn-Mg/SiCP composites processed by a liquid metal processing (stir casting) technique have been microstructurally characterised in the as-cast and extruded conditions. Uniform distribution of SiCP is observed with few defects, such as particle clusters, which are due to partial wetting and associated gas porosity. The constituent particles are associated with SiCP although their composition remains unaffected compared with the control alloy. Hot extrusion of the composite using a shear type die showed banding of particles in the extruded direction with 9 vol.% composite. Such defects however, are not predominant in 18% SiCP extruded composites. The presence Of Mg2Si is detected at the particle matrix interface as well as in the matrix.

Atomic Scale Fluctuations Govern Brittle Fracture and Cavitation Behavior in Metallic Glasses

We perform atomistic simulations on the fracture behavior of two typical metallic glasses, one brittle (FeP) and the other ductile (CuZr), and show that brittle fracture in the FeP glass is governed by an intrinsic cavitation mechanism near crack tips in contrast to extensive shear banding in the ductile CuZr glass. We show that a high degree of atomic scale spatial fluctuations in the local properties is the main reason for the observed cavitation behavior in the brittle metallic glass. Our study corroborates with recent experimental observations of nanoscale cavity nucleation found on the brittle fracture surfaces of metallic glasses and provides important insights into the root cause of the ductile versus brittle behavior in such materials.

Nanoindentation response of an ion irradiated Zr-based bulk metallic glass

Nanoindentation experiments were conducted on a Ni+ ion-irradiated Zr-based bulk metallic glass (BMG). The irradiation was carried out using 2.5, 5, 10 and 15 MeV ions and a flux of similar to 10(16) ions/cm(2). Post mortem imaging of the indents reveals a transition in the deformation mechanism of the irradiated regions from heterogeneous shear banding to homogeneous flow. Additionally, the load-displacement curves exhibit a transition from serrated to continuous flow with increasing severity of irradiation damage. The stress-strain response obtained from micro-pillar compression experiments complements the indentation response exhibiting a decrease in the flow stress and an `apparent' strain hardening at the lowest irradiation damage investigated, which is not observed in the as-cast alloy. (C) 2011 Elsevier B.V. All rights reserved.

Microstructure and texture evolution during accumulative roll bonding of aluminium alloys AA2219/AA5086 composite laminates

Accumulative roll bonding of two aluminium alloys, AA2219 and AA5086 was carried out up to 8 passes. During the course of ARB, the deformation inhomogeneity between the two alloy layers results in interfacial instability after the 4th pass, necking of the AA5086 layers after the 6th pass and fracture along the necked regions after the 7th and 8th pass. The EBSD analysis shows deformation bands along the interfaces after 8 passes of ARB. The ARB-processed materials predominantly show characteristic deformation texture components. The weak texture after the 2nd pass results from the combination of a weakly-textured starting AA2219 layer and a strongly-textured starting AA5086 layer. A strong deformation texture forms due to the high imposed strain after a higher number of ARB passes. Subgrain formation and related shear banding induces copper/S components in the case of the small elongated grains, while planar slip leads to the formation of brass component in the large elongated grains.

The Role of Strain Rate Response on Tribological Behavior of Metals

In an effort to study the role of strain rate response on the tribological behavior of metals, room temperature experiments were conducted by sliding commercially pure titanium and a-iron pins against an H-11 die steel flats of various surface textures. The steel flat surface textures were specifically prepared to allow for imposing varying amounts of strain rates at the contacting interface during sliding motion. In the experiments, it was observed that titanium (a harder material than iron) formed a transfer layer on H-11 steel surface textures that produced higher strain rates. In contrast, the titanium pins abraded the steel surfaces that produced lower strain rates. The iron pins were found to abrade the H-11 steel surface regardless of the surface texture characteristics. This unique tribological behavior of titanium is likely due to the fact that titanium undergoes adiabatic shear banding at high strain rates, which creates pathways for lower resistance shear planes. These shear planes lead to fracture and transfer layer formation on the surface of the steel flat, which ultimately promotes a higher strain rate of deformation at the asperity level. Iron does not undergo adiabatic shear banding and thus more naturally abrades the surfaces. Overall, the results clear indicated that a materials strain rate response can be an important factor in controlling the tribological behavior of a plastically deforming material at the asperity level. DOI: 10.1115/1.4007675]

Evolution of microstructure and texture in friction stir processed Al-Mg-Mn alloy

Friction stir processing was carried out on the Al-Mg-Mn alloy to achieve ultrafine grained microstructure. The evolution of microstructure and micro-texture was studied in different regions of the deformed sample, namely nugget zone, thermo-mechanically affected zone (TMAZ) and base metal. The average grain sizes of the nugget zone, TMAZ and base metal are 1.5 mu m +/- 0.5 mu m, 15 mu m +/- 8 mu m, and 80 mu m +/- 10 mu m, respectively. The TMAZ exhibits excessive deformation banding structure and sub-grain formation. The orientation gradient within the sub-grain is dependent on grain size, orientation, and distance from nugget zone. The microstructure was partitioned based on the grain orientation spread and grain size values to separate the recrystallized fraction from the deformed region in order to understand the micromechanism of grain refinement. The texture of both deformed and recrystallized regions are similar in nature. Microstructure and texture analysis suggest that the restoration processes are different in different regions of the processed sample. The transition region between nugget zone and TMAZ exhibits large elongated grains surrounded by fine equiaxed grains of different orientation which indicate the process of discontinuous dynamic recrystallization. Within the nugget zone, similar texture between deformed and recrystallized grain fraction suggests that the restoration mechanism is a continuous process.

New insights into the development of microstructure and deformation texture in nickel-60 wt.% cobalt alloy

The present study investigates the critical role of deformation twinning and Bs-type shear bands in the evolution of deformation texture in a low stacking fault energy Ni-60Co alloy up to very large rolling strain (epsilon(t) approximate to 4). The alloy develops a strong brass-type rolling texture, and its formation is initiated at the early stages of deformation. Extensive twinning is observed at the intermediate stages of deformation, which causes significant texture reorientation towards alpha-fiber. A pseudo-in-situ electron back-scattered diffraction technique adopted to capture orientation changes within individual grains during the early stages suggests that twinning should be subsequently aided by crystallographic slip to attain alpha-fiber (< 1 1 0 >parallel to ND) orientations. Beyond 40% reduction, deformation is dominated by Bs-type shear bands, and the banding coincides with the evolution of < 1 1 1 >parallel to ND components. The volume fraction of shear bands is significant at higher strains, and crystallites within the bands preferentially show < 1 1 0 >parallel to ND components. The absence of the Cu {1 1 2}< 1 1 1 > component in the initial texture, and subsequently during rolling, indicates that, for the evolution of a brass-type texture, the presence of the Cu component is not a necessary condition. The final rolling texture is a synergistic effect of deformation twinning and shear banding. (C) 2014 Acta Materialia Inc. Published by Elsevier Ltd. All rights reserved.

Deformation of nanograined Ni-60Co alloy with low stacking fault energy

The evolution of deformation texture in a Ni-60Co alloy with low stacking fault energy and a grain size in the nanometre range has been investigated. The analyses of texture and microstructure suggest different mechanisms of deformation in nanocrystalline as compared to microcrystalline Ni-60Co alloy. In nanocrystalline material, the mechanism responsible for texture formation has been identified as partial slip, whereas in microcrystalline material, a characteristic texture forms due to twinning and shear banding.