Chemistry of gabbroic rocks from ODP Hole 118-735B

Gabbroic rocks and their late differentiates recovered at Site 735 represent 500 m of oceanic layer 3. The original cooling of a mid-ocean ridge magma chamber, its penetration by ductile shear zones and late intrusives, and the subsequent penetration of seawater through a network of cracks and into highly permeable magmatic hydrofracture horizons are recorded in the metamorphic stratigraphy of the core. Ductile shear zones are characterized by extensive dynamic recrystallization of primary phases, beginning in the granulite facies and continuing into the lower amphibolite facies. Increasing availability of seawater during dynamic recrystallization is reflected in depletions in 18O, increasing abundance of amphibole of variable composition and metamorphic plagioclase of intermediate composition, and more complete coronitic or pseudomorphous static replacement of magmatic minerals. Downcore correlation of synkinematic assemblages, bulk-rock oxygen isotopic compositions, and vein abundance suggest that seawater is introduced into the crust by way of small cracks and veins that mark the end of the ductile phase of deformation. This "deformation-enhanced" metamorphism dominates the upper 180 and the lower 100 m of the core. In the lower 300 m of the core, mineral assemblages of greenschist and zeolite facies are abundant within or adjacent to brecciated zones. Leucocratic veins found in these zones and adjacent host rock contain diopside, sodic plagioclase, epidote, chlorite, analcime, thomsonite, natrolite, albite, quartz, actinolite, sphene, brookite, and sulfides. The presence of zircon, Cl-apatite, sodic plagioclase, sulfides, and diopside in leucocratic veins having local magmatic textures suggests that some of the veins originated from late magmas or from hydrothermal fluids exsolved from such magmas that were subsequently replaced by (seawater-derived) hydrothermal assemblages. The frequent association of these late magmatic intrusive rocks within the brecciated zones suggests that they are both artifacts of magmatic hydrofracture. Such catastrophic fracture and hydrothermal circulation could produce episodic venting of hydrothermal fluids as well as the incorporation of a magmatically derived hydrothermal component. The enhanced permeability of the brecciated zones produced lower temperature assemblages because of larger volumes of seawater that penetrated the crust. The last fractures were sealed either by these hydrothermal minerals or by late carbonate-smectite veins, resulting in the observed low permeability of the core.

SHRIMP U-Pb zircon data from Gjelsvikfjella, Dronning Maud Land, East Antarctica

The Maud Belt in Dronning Maud Land (western East Antarctic Craton) preserves a high-grade polyphase tectono-thermal history with two orogenic episodes of Mesoproterozoic (1.2-1.0 Ga) and Neoproterozoic (0.6-0.5 Ga) age. New SHRIMP U-Pb zircon data from southern Gjelsvikfjella in the northeastern part of the belt make it possible to differentiate between a series of magmatic and metamorphic events. The oldest event recorded is the formation of an extensive 1140-1130 Ma volcanic arc. This was followed by 1104 ± 8 Ma granitoids that might represent, together with so far undated mafic dykes, part of a decompression melting-related bimodal suite that reflects the sub-continental Umkondo igneous event. The first high-grade metamorphism is constrained at 1070 Ma. The metamorphic age data are similar to those obtained from other parts of the Maud Belt, but also from the Namaqua-Natal Belt in South Africa, but the preceding arc formation was diachronous in the two belts. This indicates that the two belts did not form a continuous volcanic arc unit as suggested in previous models, but became connected only at the end of the Mesoproterozoic. Intense reworking during the Neoproterozoic, probably as a result of continent-continent collision between components of Gondwana, is indicated by ductile refliation, further high-grade metamorphic recrystallisation and metamorphic zircon overgrowths at approximately 530 Ma. This was followed by late- to post-tectonic magmatism, reflected by 500 Ma granite bodies and 490 Ma aplite dykes as well as a 480 Ma gabbro body.

Geochemistry of vein rocks of ODP Hole 118-735B

Rock samples from Hole 735B, Southwest Indian Ridge, were examined to determine the principal vein-related types of alteration that occurred, the nature of fluids that were present, and the temperatures and pressures of these fluids. Samples studied included veined metagabbro, veined mylonitic metagabbro, felsic trondhjemite, and late-stage leucocratic diopside-bearing veins. The methods used were standard petrographic analysis, mineral chemical analysis by electron microprobe, fluid inclusion petrography and analysis by heating/freezing techniques and laser Raman microspectroscopy, and oxygen isotopic analyses of mineral separates. Alteration in lithologic Units I and II (above the level of Core 118-735B-3OR; approximately 140 meters below the seafloor) is dominated by hydration by seawater-derived fluids at high temperature, up to about 700°C, and low water/rock ratio, during and immediately after pervasive ductile deformation. Below Core 118-735B-30R, pervasive deformation is less common, and brittle veining and brecciation are the major alteration styles. Leucocratic centimeter-scale veins, often containing diopside and plagioclase, were produced by interaction of hot (about 500°C) seawater-derived fluid and gabbro. The water/rock ratio was locally high at the veins and breccia zones, but the integrated water/rock ratio for the lower part of the hole is probably low. Accessory hydrous magmatic or deuteric phases formed from magmatic volatiles in some gabbro and in trondhjemite. Most subsequent alteration was affected by fluids that were seawater-derived, based on isotopic and chemical analyses of minerals and analyses of fluid inclusions. Many early-generation fluid inclusions, associated with high-temperature veining, contain appreciable methane as well as saline water. The source of methane is unclear, but it may have formed as seawater was reduced during low water/rock interaction with ultramafic upper mantle or ultramafic and mafic layer 3. Temperatures of alteration were calculated on the basis of coexisting mineral chemistry and isotopic values. Hydrothermal metamorphism commenced at about 720°C and continued to about 550°C. Leucocratic veining took place at about 500°C. Alteration within brecciated horizons was also at about 500° to less than 400°C, and the trondhjemite was altered at about 550° to below 490°C. Pressures calculated from a diopside-bearing vein, based on a combination of fluid inclusion and isotopic analysis, were 90 to 100 MPa. This pressure places the sample, from Core 118-735B-70R in Unit V, at about 2 km below the seafloor.

Major, trace and rare earth element concentration of ODP Site 210-1277 basalts, Newfoundland margin

Drilling of the distal Newfoundland margin at Ocean Drilling Program Site 1277 recovered part of the transition between exhumed sub-continental mantle lithosphere and normal mid-ocean-ridge basalt (N-MORB) volcanism perhaps related to the initiation of seafloor spreading, which may have occurred near the Aptian/Albian boundary, coincident with the final separation of subcontinental mantle lithosphere. Subcontinental mantle lithosphere was recovered near the crest of a basement high, the Mauzy Ridge. This ridge lies near magnetic Anomaly M1 and is inferred to be of Barremian age. The recovered section is dominated by serpentinized spinel harzburgite, with subordinate dunite and minor gabbroic intrusives, and it includes inferred high-temperature ductile shear zones. The serpentinite is capped by foliated gabbro cataclasite that is interpreted as the product of a major seafloor extensional detachment. The serpentinized harzburgite beneath is highly depleted subcontinental mantle lithosphere that was exhumed to create new seafloor within the ocean-continent transition zone. After inferred removal of overlying brittle crust, the detachment was eroded, producing multiple mass flows that were dominated by clasts of serpentinite and gabbro in a lithoclastic and calcareous matrix. Basaltic lavas were erupted spasmodically, mainly as sheet flows, with subordinate lava breccia, hyaloclastite, and possible pillow lava. The sedimentary-volcanic succession and the exhumed mantle lithosphere experienced later high-angle extensional fracturing and probably faulting. Extensional fissures opened incrementally and were filled with silt-sized carbonate, basalt-derived clastic sediment, and hyaloclastite, forming neptunian dykes and geopetal structures. Chemical analysis of representative basalts for major elements and trace elements were made using a high-precision, high-accuracy X-ray fluorescence method (utilizing increased count times) and by whole-rock inductively coupled plasma-mass spectrometry that yielded additional evidence for rare earth elements. The analyses indicate N-MORB to slightly enriched compositions. The MORB was produced by relatively high degree melting of a fertile mantle source that differed strongly from the cored serpentinized peridotites. The basalts exhibit a distinct negative Nb anomaly on MORB-normalized plots that can be explained by prior extraction of melt from upper mantle that had previously been affected by subduction, possibly during closure of the Iapetus or Rheic oceans. In the proposed interpretation, mantle lithosphere was exhumed to the seafloor and experienced mass wasting to form serpentinite-rich mass flows. The interbedded MORB records the beginning of a transition to "normal" seafloor spreading. This interpretation takes into account drilling results from the Iberia-Galicia margin and the Jurassic Alps-Apennines.

Inherited structural controls on fault geometry, architecture and hydrothermal activity: an example from Grimsel Pass, Switzerland

Exhumed faults hosting hydrothermal systems provide direct insight into relationships between faulting and fluid flow, which in turn are valuable for making hydrogeological predictions in blind settings. The Grimsel Breccia Fault (Aar massif, Central Swiss Alps) is a late Neogene, exhumed dextral strike-slip fault with a maximum displacement of 25–45 m, and is associated with both fossil and active hydrothermal circulation. We mapped the fault system and modelled it in three dimensions, using the distinctive hydrothermal mineralisation as well as active thermal fluid discharge (the highest elevation documented in the Alps) to reveal the structural controls on fluid pathway extent and morphology. With progressive uplift and cooling, brittle deformation inherited the mylonitic shear zone network at Grimsel Pass; preconditioning fault geometry into segmented brittle reactivations of ductile shear zones and brittle inter-shear zone linkages. We describe ‘pipe’-like, vertically oriented fluid pathways: (1) within brittle fault linkage zones and (2) through alongstrike- restricted segments of formerly ductile shear zones reactivated by brittle deformation. In both cases, low-permeability mylonitic shear zones that escaped brittle reactivation provide important hydraulic seals. These observations show that fluid flow along brittle fault planes is not planar, but rather highly channelised into sub-vertical flow domains, with important implications for the exploration and exploitation of geothermal energy.

Gold Ores Related to Shear Zones, West Santa Comba Fervenza Area (Galicia, NW Spain): A Mineralogical Study

Recent research has discovered high-grade Au ores in NNE-SSW trending shear zones in metamorphic proterozoic and palaeozoic terranes, some 40 km NW of Santiago de Compostela (NW Spain). The orebodies are bound to late-stage Hercynian structures, mainly due to brittle deformation, which are superimposed on earlier ductile shear zones, cutting through various catazonal lithologies, including ortho- and paragneisses, amphibolites, eclogites, and granites. Ore mineralogy, alteration, and ore textures define a frame whose main features are common to all prospects in the area. Main minerals are arsenopyrite and pyrite - accompanied by quartz, adularia, sericite, + (tourmaline, chlorite, carbonates, graphite), as main gangue minerals - with subordinate amounts of boulangerite, bismuthinite, kobellite, jamesonite, chalcopyrite, marcasite, galena, sphalerite, rutile, titanite, scheelite, beryl, fluorite, and minor native gold, electrum, native bismuth, fahlore, pyrrhotite, mackinawite, etc., defining a meso-catathermal paragenesis. Detailed microscopic study allows the author to propose a general descriptive scheme of textural classification for this type of ore. Most of the ores fill open spaces or veins, seal cracks or cement breccias; disseminated ores with replacement features related to alteration (mainly silicification, sericitization, and adularization) are also observed. Intensive and repeated cataclasis is a common feature of many ores, suggesting successive events of brittle deformation, hydrothermal flow, and ore precipitation. Gold may be transported and accumulated in any of these events, but tends to be concentrated in later ones. The origin of the gold ores is explained in terms of hydrotherreal discharge, associated with mainly brittle deformation and possibly related to granitic magmas, in the global tectonic frame of crustal evolution of West Galicia. The mineralogical and textural study suggests some criteria which will be of practical value for exploration and for ore processing. Ore grades can be improved by flotation of arsenopyrite. Non-conventional methods, such as pressure or bacterial leaching, may subsequently obtain a residue enriched in gold.

High-temperature mechanical properties of aluminium alloys reinforced with titanium diboride (TiB2) particles

The physical and mechanical properties of metal matrix composites were improved by the addition of reinforcements. The mechanical properties of particulate-reinforced metal-matrix composites based on aluminium alloys (6061 and 7015) at high temperatures were studied. Titanium diboride (TiB2) particles were used as the reinforcement. All the composites were produced by hot extrusion. The tensile properties and fracture characteristics of these materials were investigated at room temperature and at high temperatures to determine their ultimate strength and strain to failure. The fracture surface was analysed by scanning electron microscopy. TiB2 particles provide high stability of the aluminium alloys (6061 and 7015) in the fabrication process. An improvement in the mechanical behaviour was achieved by adding TiB2 particles as reinforcement in both the aluminium alloys. Adding TiB2 particles reduces the ductility of the aluminium alloys but does not change the microscopic mode of failure, and the fracture surface exhibits a ductile appearance with dimples formed by coalescence.

Dynamique des structures. Vulnérabilité aux bâtiments. Construction parasismique

La leçon s'addresse à la comprehension du comportement des bâtiments soumis à l'accéleration séismique, et présente une introduction au comportement dynamique de oscillateurs (un ou plusieurs dégrés de liberté), du comportément hystérétique des structures (selon modes de dissipation) et aux paramètres séismiques relevants à la conception parasismique, notamment aux spectres de réponse et de démande, et sa relation avec la capacité de la structure (courbe de capacité) où on peut identifier les niveaux de dommage -ou les critères de performance- pour des intensités séismique prévues au projet. Elle considère aussi les méthodes de définition et détermination de la vulnérabilité, façe aux séismes, des différentes typologies constructives, avec l'inclusion finale des typologies pour les sistèmes de contreventement et recomandations visées à éviter aux mêmes la concentration de dommage d'origine séismique. Lecture's goal focuses in the understanding of the behaviour of buildings under seismic excitation. It presents an introduction of dynamics (single or multiple degrees of freedom oscillators) and the hysteretic behaviour of ductile structures, introducing the seismic parameters relevant to the structural design, mostly in the context of response and demand spectra and their relations with capacity curves of structures. On the capacity curve obtained in pushover analysis, points representing the design objectives in terms of performance levels can be identified and related with seismic demand. Lecture deals also with methods on vulnerability analysis for building construction typologies and the behaviour (and related recommendations) of seismic resistant structural typologies, having the distribution of dissipative energy and damage in mind.

Evaluación del comportamiento mecánico, estructural y frente a la corrosión, de una nueva armadura de acero inoxidable dúplex bajo en níquel

La durabilidad de las estructuras de hormigón armado no es ilimitada, en especial en determinados ambientes. El ingreso de agentes agresivos en el hormigón, fundamentalmente dióxido de carbono e iones cloruros, rebasando el espesor del recubrimiento y alcanzando las armaduras, reducen el alto pH del hormigón hasta alcanzar un umbral crítico, por debajo del cual, el acero queda despasivado. Posteriormente, si existe el suficiente aporte de humedad y oxígeno, el acero se corroe, lo que supone drásticas reducciones de la vida de servicio de estas estructuras y su inevitable reparación. La utilización de armaduras de acero inoxidable es una alternativa que está recibiendo cada vez más consideración. Su resistencia a la corrosión en los ambientes más agresivos, incluso con ataque de cloruros, lo convierte en el material idóneo para prolongar de forma muy considerable la vida útil de la estructura. En este trabajo se ha evaluado el comportamiento mecánico y estructural, y de resistencia a la corrosión, de un nuevo acero inoxidable dúplex de bajo contenido en níquel, el EN 1.4482 (AISI 2001), y se ha comparado con el inoxidable austenítico más utilizado, el EN 1.4301 (AISI 304), con el dúplex EN 1.4362 (AISI 2304) y con el tradicional acero al carbono B-500-SD. El estudio mecánico y estructural se ha realizado en tres niveles diferentes: a nivel de barra, estudiando las propiedades mecánicas y de ductilidad de los cuatro aceros citados; a nivel de sección, estudiando su comportamiento a flexión con diferentes cuantías de armado por medio de los diagramas momento-curvatura; y a nivel de pieza, ensayando una serie de vigas armadas con diferentes aceros y cuantías, y comprobando su comportamiento a desplazamiento y resistencia por medio de los diagramas carga-desplazamiento. El estudio de resistencia a la corrosión se ha realizado embebiendo barras corrugadas, de los tres aceros inoxidables mencionados, en probetas de mortero contaminadas con diferentes cantidades de cloruros, y realizando mediciones electroquímicas durante un periodo de al menos un año. Se han preparado probetas de mortero para dos comparativas diferentes. La primera, manteniendo las probetas en un desecador con el 95 % de humedad relativa durante todo el periodo de mediciones. La segunda, sumergiendo parcialmente las probetas en una solución tampón para carbonatar el mortero. Los resultados de los ensayos mecánicos han demostrado dos aspectos diferentes. Uno, que las armaduras de acero inoxidable tienen un comportamiento muy similar a las de acero al carbono en lo referente a las resistencias alcanzadas, en el límite elástico y en rotura, pero distinto en cuanto al módulo de deformación longitudinal, cuyo valor es claramente inferior al del acero al carbono, por lo que su utilización en las estructuras de hormigón necesita tener en cuenta ese dato en los análisis lineales de cálculo. El segundo aspecto es que las armaduras de acero inoxidable laminadas en caliente presentan una ductilidad muy superior a las de acero al carbono, por lo que ofrecen una mayor seguridad frente a su rotura o al colapso de la estructura, lo que se debe tener en cuenta en el análisis de cálculo plástico. En cambio, las armaduras de acero inoxidable laminadas en frío sólo cumplen con los límites mínimos de ductilidad establecidos en la instrucción EHE-08 para los aceros soldables, y no para los aceros con características especiales de ductilidad. El estudio a nivel de sección refleja la paradoja de obtener secciones menos dúctiles con las armaduras de acero inoxidable laminadas en caliente que con las armaduras de acero al carbono. Para subsanarlo, se definen los conceptos de curvatura última de rotura y ductilidad de la sección en rotura, que tienen en cuenta las altas deformaciones alcanzadas por las armaduras de acero inoxidable. Los resultados a nivel de pieza permiten identificar el comportamiento estructural del hormigón armado con barras corrugadas de acero inoxidable y compararlo con el de las estructuras de hormigón armado convencionales, verificando los resultados experimentales con los teóricos obtenidos con la formulación recogida en la instrucción EHE- 08. Los ensayos de resistencia a la corrosión por cloruros demuestran, durante el primer año y medio de vida de las probetas, un comportamiento muy similar entre el nuevo acero inoxidable dúplex bajo en níquel y el austenítico y el dúplex utilizados para la comparación, incluso para las probetas carbonatadas. Por último, se añade una comparativa económica, realizada sobre dos edificaciones tipo, para cuantificar el sobrecoste que supone la utilización de armaduras de acero inoxidable respecto a las de acero al carbono. El alto coste inicial de las armaduras de acero inoxidable se ve compensado en el coste final de la estructura de muy diferentes formas, principalmente dependiendo del grado de acero elegido y de si se emplean en el total de la estructura o solamente en los elementos más expuestos. The durability of the concrete structures is limited, especially in certain environments. The attack of aggressive agents in the concrete, mainly carbon dioxide and chloride ions, penetrating the thickness of concrete cover and reaching the reinforcements, reduce the high pH of concrete to the point of reaching a critical threshold, under which, the steel despasivates. Therefore, if there is enough humidity and oxygen, the steel corroes, causing drastic reductions in the service life of these structures and its inevitable repair. Despite the high initial cost compared to carbon steel, the usage of stainless steel reinforcements is an alternative with a major consideration nowadays. Its resistance to corrosion in the most aggressive atmospheres, including chlorides attack, makes the stainless steel a suitable material to extend considerably its lifetime. In this study, it’s been evaluated the mechanical and structural behaviour, and the corrosion resistance, of a new low-nickel duplex stainless steel EN 1.4482 (AISI 2001), and it has been compared with the most widely used austenitic type EN 1.4301 (AISI 304), with duplex steel EN 1.4362 (AISI 2304) and with the traditional carbon steel B-500-SD. The mechanical and structural study has been carried out in three different levels: bar level, studying mechanical properties and ductility of the four steels; section level, studying its behaviour when blending with different amounts of reinforcement through the moment-curvature diagrams; and structural element level, testing a series of reinforced beams with different steels and amounts, and checking its sag and resistance through the load-deflection diagrams. The corrosion resistance study was performed by embedding ribbed bars, using the three stainless steel listed, on mortar specimens contaminated with different amounts of chlorides, and taking electrochemical measurements over a period of at least one year. Mortar specimens have been prepared for two different comparisons. The first, keeping the specimens at 95% of relative humidity during the measurement period. The second, immersing the specimens partially in a carbonate buffer solution. The results of those tests have proved two different aspects. Firstly, that stainless steel reinforcements show a very similar behaviour to carbon steel, according to the reached levels of mechanical resistance, yield stress and steel strength, but a different behaviour in Young’s modulus, which value is clearly lower than the carbon steel. Therefore, when using in concrete structures it is need to consider on that point the existing calculus of linear analysis. The second aspect is that stainless steel reinforcement manufactured by hot-rolling process show a very higher ductility than carbon steel, offering a better security on cracks or structure collapse, which it has to be taken into account on plastic calculus analysis. However, the stainless steel reinfor9 cement cold-rolled bars only meet the minimum thresholds of ductility established by EHE-08 for welded steel, and not for steels with special ductility. The results at the section level reflect the paradox of getting less ductile sections with hot rolled stainless steel reinforcement than with carbon steel reinforcements. To overcome that, the concepts of last break curvature and break ductility section have been defined, which take into account the high deformation value achieved by stainless steel reinforcements. The results at the structural element level allow to identify the structural behaviour of reinforced concrete with stainless steel reinforcements and compared with that of conventional steel reinforcement, contrasting the experimental with the theoretical results obtained from the formulation contained in the instruction EHE-08. Tests on resistance of chloride corrosion show during the first year and a half of specimens life, a similar behaviour between the new low nickel duplex stainless steel and austenitic and duplex used for comparison, even for carbonated specimens. Finally, it has been included an economic comparison on two differents building types, to quantify the additional cost involved on the use of stainless steel reinforcement compared to that of carbon steel. The high initial cost of stainless steel reinforcements is offset in the final cost of the structure in many different ways, mainly depending on the chosen steel grade and whether the reinforcement is used in the total structure or only in risky structural elements.

Revisiting the method to obtain the mechanical properties of hydrided fuel cladding in the hoop direction

The method reported in the literature to calculate the stress–strain curve of nuclear fuel cladding from ring tensile test is revisited in this paper and a new alternative is presented. In the former method, two universal curves are introduced under the assumption of small strain. In this paper it is shown that these curves are not universal, but material-dependent if geometric nonlinearity is taken into account. The new method is valid beyond small strains, takes geometric nonlinearity into consideration and does not need universal curves. The stress–strain curves in the hoop direction are determined by combining numerical calculations with experimental results in a convergent loop. To this end, ring tensile tests were performed in unirradiated hydrogen-charged samples. The agreement among the simulations and the experimental results is excellent for the range of concentrations tested (up to 2000 wppm hydrogen). The calculated stress–strain curves show that the mechanical properties do not depend strongly on the hydrogen concentration, and that no noticeable strain hardening occurs. However, ductility decreases with the hydrogen concentration, especially beyond 500 wppm hydrogen. The fractographic results indicate that as-received samples fail in a ductile fashion, whereas quasicleavage is bserved in the hydrogen-charged samples.

Simulación del proceso de rotura por tracción de alambres de acero perlítico con un modelo de fisura cohesiva

La fractura de metales dúctiles como el acero suele explicarse a partir de la hipótesis de nucleación, crecimiento y coalescencia de microhuecos. A partir de esta teoría, se han desarrollado diversos modelos numéricos, entre los que el modelo de Gurson y sus variantes son los más extendidos. Dichos modelos reproducen matemáticamente el fenómeno físico de crecimiento de huecos resultando en un desarrollo progresivo del daño en el interior del material durante un ensayo de tracción. En estos modelos, el daño comienza a desarrollarse en fases muy tempranas del ensayo, incluso anteriores a la carga máxima. Ensayos realizados por los autores parecen indicar, sin embargo, que en el caso de barras de acero eutéctico empleado en la fabricación de alambres de pretensado, el daño originado en el interior del material como consecuencia del crecimiento de microhuecos sólo es apreciable en un estado muy avanzado del ensayo, momentos antes de producirse la rotura. Además, desde hace décadas se conoce que la triaxialidad de tensiones tiene una fuerte influencia sobre la rotura de los materiales. En este trabajo se presenta un modelo de rotura para elementos de acero sometidos a tracción, basado en un comportamiento cohesivo del material y que contempla el valor de la triaxialidad de tensiones, diferente en cada punto de la sección crítica de rotura. The fracture of ductile materials, such as steel, is usually explained with the theory of nucleation, growth and coalescence of microvoids. Based on this theory, many numerical models have been developed, with a special mention to Gurson-type models. These models simulate mathematically the physical growth of microvoids, leading to a progressive development of the internal damage that takes place during a tensile test. In these models, the damage starts to develop in very early stages of the test. Tests carried out by the authors seem to point out that, in the case of eutectoid steel bars used for manufacturing prestressing steel wires, the internal damage that takes place as a result of the growth of microvoids is only noticeable in a very advanced state of the test. In addition to this, it is known that the stress triaxiality has a strong influence over the fracture of ductile materials. This work presents a fracture model for steel specimens in a tensile test, based on a cohesive behaviour and taking into account the effect of stress triaxiality, which is different in every point of the fracture plane.

A fracture model for pearlitic steel bars using a cohesive model

The fracture of ductile materials, such as metals, is usually explained with the theory of nucleation, growth and coalescence of microvoids. Based on this theory, many numerical models have been developed, with a special mention to Gurson-type models. These models simulate mathematically the physical growth of microvoids, leading to a progressive development of the internal damage that takes place during a tensile test. In these models, the damage starts to develop in very early stages of the test. Tests carried out by the authors suggest that, in the case of some eutectoid steels such as those used for manufacturing prestressing steel wires, the internal damage that takes place as a result of the growth of microvoids is only noticeable in very late stages of the tensile test. In the authors’ opinion, using a cohesive model as a failure criterion may be interesting in this case; a cohesive model only requires two parameters to be defined, with the fracture energy being one of them, which can be obtained experimentally. In addition to this, given that it is known that the stress triaxiality has a strong influence on the fracture of ductile materials, a cohesive model whose parameters are affected by the value of the stress triaxiality can be considered. This work presents a fracture model for steel specimens in a tensile test, based on a cohesive behaviour and taking into account the effect of stress triaxiality, which is different at each point of the fracture plane.

Simulación del proceso de rotura por tracción de alambres de acero perlítico con un modelo de fisura cohesiva

La fractura de metales dúctiles como el acero suele explicarse a partir de la hipótesis de nucleación, crecimiento y coalescencia de microhuecos. A partir de esta teoría, se han desarrollado diversos modelos numéricos, entre los que el modelo de Gurson y sus variantes son los más extendidos. Dichos modelos reproducen matemáticamente el fenómeno físico de crecimiento de huecos resultando en un desarrollo progresivo del daño en el interior del material durante un ensayo de tracción. En estos modelos, el daño comienza a desarrollarse en fases muy tempranas del ensayo, incluso anteriores a la carga máxima. Ensayos realizados por los autores parecen indicar, sin embargo, que en el caso de barras de acero eutéctico empleado en la fabricación de alambres de pretensado, el daño originado en el interior del material como consecuencia del crecimiento de microhuecos sólo es apreciable en un estado muy avanzado del ensayo, momentos antes de producirse la rotura. Además, desde hace décadas se conoce que la triaxialidad de tensiones tiene una fuerte influencia sobre la rotura de los materiales. En este trabajo se presenta un modelo de rotura para elementos de acero sometidos a tracción, basado en un comportamiento cohesivo del material y que contempla el valor de la triaxialidad de tensiones, diferente en cada punto de la sección crítica de rotura. The fracture of ductile materials, such as steel, is usually explained with the theory of nucleation, growth and coalescence of microvoids. Based on this theory, many numerical models have been developed, with a special mention to Gurson-type models. These models simulate mathematically the physical growth of microvoids, leading to a progressive development of the internal damage that takes place during a tensile test. In these models, the damage starts to develop in very early stages of the test. Tests carried out by the authors seem to point out that, in the case of eutectoid steel bars used for manufacturing prestressing steel wires, the internal damage that takes place as a result of the growth of microvoids is only noticeable in a very advanced state of the test. In addition to this, it is known that the stress triaxiality has a strong influence over the fracture of ductile materials. This work presents a fracture model for steel specimens in a tensile test, based on a cohesive behaviour and taking into account the effect of stress triaxiality, which is different in every point of the fracture plane.

Diseño y comportamiento de uniones estructurales mecánicas y adhesivas. Condiciones superficiales y operacionales

Las uniones estructurales mecánicas y adhesivas requieren la combinación de un número importante de parámetros para la obtención de la continuidad estructural que exigen las condiciones de diseño. Las características de las uniones presentan importantes variaciones, ligadas a las condiciones de ejecución, tanto en uniones mecánicas como especialmente en uniones adhesivas y mixtas (unión mecánica y adhesiva, también conocidas como uniones híbridas). Las propiedades mecánicas de las uniones adhesivas dependen de la naturaleza y propiedades de los adhesivos y también de muchos otros parámetros que influyen directamente en el comportamiento de estas uniones. Algunos de los parámetros más significativos son: el acabado superficial de los materiales, área y espesor de la capa adhesiva, diseño adecuado, secuencia de aplicación, propiedades químicas de la superficie y preparación de los sustratos antes de aplicar el adhesivo. Los mecanismos de adhesión son complejos. En general, cada unión adhesiva solo puede explicarse considerando la actuación conjunta de varios mecanismos de adhesión. No existen adhesivos universales para un determinado material o aplicación, por lo que cada pareja sustrato-adhesivo requiere un particular estudio y el comportamiento obtenido puede variar, significativamente, de uno a otro caso. El fallo de una junta adhesiva depende del mecanismo cohesión-adhesión, ligado a la secuencia y modo de ejecución de los parámetros operacionales utilizados en la unión. En aplicaciones estructurales existen un número muy elevado de sistemas de unión y de posibles sustratos. En este trabajo se han seleccionado cuatro adhesivos diferentes (cianoacrilato, epoxi, poliuretano y silano modificado) y dos procesos de unión mecánica (remachado y clinchado). Estas uniones se han aplicado sobre chapas de acero al carbono en diferentes estados superficiales (chapa blanca, galvanizada y prepintada). Los parámetros operacionales analizados han sido: preparación superficial, espesor del adhesivo, secuencia de aplicación y aplicación de presión durante el curado. Se han analizado tanto las uniones individuales como las uniones híbridas (unión adhesiva y unión mecánica). La combinación de procesos de unión, sustratos y parámetros operacionales ha dado lugar a la preparación y ensayo de más de mil muestras. Pues, debido a la dispersión de resultados característica de las uniones adhesivas, para cada condición analizada se han ensayado seis probetas. Los resultados obtenidos han sido: El espesor de adhesivo utilizado es una variable muy importante en los adhesivos flexibles, donde cuanto menor es el espesor del adhesivo mayor es la resistencia mecánica a cortadura de la unión. Sin embargo en los adhesivos rígidos su influencia es mucho menor. La naturaleza de la superficie es fundamental para una buena adherencia del adhesivo al substrato, que repercute en la resistencia mecánica de la unión. La superficie que mejor adherencia presenta es la prepintada, especialmente cuando existe una alta compatibilidad entre la pintura y el adhesivo. La superficie que peor adherencia tiene es la galvanizada. La secuencia de aplicación ha sido un parámetro significativo en las uniones híbridas, donde los mejores resultados se han obtenido cuando se aplicaba primero el adhesivo y la unión mecánica se realizaba antes del curado del adhesivo. La aplicación de presión durante el curado se ha mostrado un parámetro significativo en los adhesivos con poca capacidad para el relleno de la junta. En los otros casos su influencia ha sido poco relevante. El comportamiento de las uniones estructurales mecánicas y adhesivas en cuanto a la resistencia mecánica de la unión puede variar mucho en función del diseño de dicha unión. La resistencia mecánica puede ser tan grande que falle antes el substrato que la unión. Las mejores resistencias se consiguen diseñando las uniones con adhesivo cianoacrilato, eligiendo adecuadamente las condiciones superficiales y operacionales, por ejemplo chapa blanca aplicando una presión durante el curado de la unión. La utilización de uniones mixtas aumenta muy poco o nada la resistencia mecánica, pero a cambio proporciona una baja dispersión de resultados, siendo destacable para la superficie galvanizada, que es la que presenta peor reproducibilidad cuando se realizan uniones sólo con adhesivo. Las uniones mixtas conducen a un aumento de la deformación antes de la rotura. Los adhesivos dan rotura frágil y las uniones mecánicas rotura dúctil. La unión mixta proporciona ductilidad a la unión. Las uniones mixtas también pueden dar rotura frágil, esto sucede cuando la resistencia del adhesivo es tres veces superior a la resistencia de la unión mecánica. Las uniones híbridas mejoran la rigidez de la junta, sobre todo se aprecia un aumento importante en las uniones mixtas realizadas con adhesivos flexibles, pudiendo decirse que para todos los adhesivos la rigidez de la unión híbrida es superior. ABSTRACT The mechanical and adhesive structural joints require the combination of a large number of parameters to obtain the structural continuity required for the design conditions. The characteristics of the junctions have important variations, linked to performance conditions, in mechanical joints as particular in mixed adhesive joints (mechanical and adhesive joints, also known as hybrid joints). The mechanical properties of the adhesive joints depend of the nature and properties of adhesives and also of many other parameters that directly influence in the behavior of these joints. Some of the most significant parameters are: the surface finished of the material, area and thickness of the adhesive layer, suitable design, and application sequence, chemical properties of the surface and preparation of the substrate before applying the adhesive. Adhesion mechanisms are complex. In general, each adhesive joint can only be explained by considering the combined action of several adhesions mechanisms. There aren’t universal adhesives for a given material or application, so that each pair substrate-adhesive requires a particular study and the behavior obtained can vary significantly from one to another case. The failure of an adhesive joint depends on the cohesion-adhesion mechanism, linked to the sequence and manner of execution of the operational parameters used in the joint. In the structural applications, there are a very high number of joining systems and possible substrates. In this work we have selected four different adhesives (cyanoacrylate, epoxy, polyurethane and silano modified) and two mechanical joining processes (riveting and clinching). These joints were applied on carbon steel with different types of surfaces (white sheet, galvanized and pre-painted). The operational parameters analyzed were: surface preparation, thickness of adhesive, application sequence and application of pressure during curing. We have analyzed individual joints both as hybrid joints (adhesive joint and mechanical joint). The combination of joining processes, substrates and operational parameters has resulted in the preparation and testing of over a thousand specimens. Then, due to the spread of results characteristic of adhesive joints, for each condition analyzed we have tested six samples. The results have been: The thickness of adhesive used is an important variable in the flexible adhesives, where the lower the adhesive thickness greater the shear strength of the joint. However in rigid adhesives is lower influence. The nature of the surface is essential for good adherence of the adhesive to the substrate, which affects the shear strength of the joint. The surface has better adherence is preprinted, especially when there is a high compatibility between the paint and the adhesive. The surface which has poor adherence is the galvanized. The sequence of application has been a significant parameter in the hybrid junctions, where the best results are obtained when applying first the adhesive and the mechanical joint is performed before cured of the adhesive. The application of pressure during curing has shown a significant parameter in the adhesives with little capacity for filler the joint. In other cases their influence has been less relevant. The behavior of structural mechanical and adhesive joints in the shear strength of the joint can vary greatly depending on the design of such a joint. The shear strength may be so large that the substrate fails before the joint. The best shear strengths are achieved by designing the junctions with cyanoacrylate adhesive, by selecting appropriately the surface and operating conditions, for example by white sheet applying a pressure during curing of the joint. The use of hybrid joints no increase shear strength, but instead provides a low dispersion of results, being remarkable for the galvanized surface, which is the having worst reproducibility when performed bonded joints. The hybrid joints leading to increased deformation before rupture. The joints witch adhesives give brittle fracture and the mechanics joints give ductile fracture. Hybrid joint provides ductility at the joint. Hybrid joint can also give brittle fracture, this happens when the shear strength of the adhesive is three times the shear strength of the mechanical joint. The hybrid joints improve stiffness of joint, especially seen a significant increase in hybrid joints bonding with flexible adhesives, can be said that for all the adhesives, the hybrid junction stiffness is higher.

Simulación de la rotura de barras de acero perlítico sometidas a tracción mediante un modelo de fisura cohesiva. Validación experimental

Las probetas cilíndricas fabricadas con materiales metálicos de elevada ductilidad, como el aluminio o el cobre, sometidas a tracción suelen presentar una rotura comúnmente denominada rotura en copa y cono, debido a su geometría. Este tipo de rotura se reproduce numéricamente con éxito mediante el modelo de Gurson-Tvergaard- Needleman, cuya formulación matemática se basa en el fenómeno físico de nucleación, crecimiento y coalescencia de microhuecos. A diferencia de dichos materiales, las barras de acero perlítico, material con una ductilidad apreciable, presentan un frente de rotura plano que no puede simularse correctamente con los modelos antes mencionados, apareciendo una región interior de daño que, en principio, también puede atribuirse a un fenómeno de nucleación y crecimiento de microhuecos, mientras que en el exterior aparece una zona cuya micrografía permite asociar su rotura a un mecanismo de clivaje. En trabajos anteriores los autores han presentado un elemento de intercara cohesivo dependiente de la triaxialidad de tensiones que, incorporado a un código de elementos finitos, permite reproducir de forma razonable el daño que se desarrolla en la región interior mencionada. En este trabajo se presentan los resultados de una campaña experimental que permite validar el modelo desarrollado. Para ello, se ensayan probetas de diferentes diámetros y se comparan los resultados con los obtenidos numéricamente, empleando tres bases extensométricas diferentes en cada uno de los diámetros. Los resultados numéricos se ajustan razonablemente bien a los obtenidos experimentalmente.The cylindrical specimens made of high-ductility metallic materials, such as aluminium and copper, usually fail showing a fracture surface commonly known as cup-cone fracture because of its shape. This type of fracture is successfully reproduced using the Gurson-Tvergaard-Needleman model, which is based on the physical process of nucleation, growth and coalescence of microvoids. Unlike these materials, pearlitic steel bars, which are considerably ductile, show a flat fracture surface that cannot be correctly reproduced with the aforementioned models. In this flat fracture surface, a dark region can be observed in the centre of the specimen, which is the result of a process of nucleation and growth of microvoids, while in the rest of the fracture surface a different region can be identified, which a micrographic study reveals to be the result of a process of cleavage. In previous works, the authors presented a triaxiality-dependent cohesive interface element that, implemented in a finite element code, can reproduce in a reasonably accurate manner the damage that takes place in the dark region mentioned before. The results of an experimental campaign designed to validate the model are presented in this paper. For it, different diameter specimens are tested and these results are compared to those obtained with the numerical models, using three different initial lengths for the strain. Numerical results agree reasonably well with those obtained experimentally.