Wire bond reliability for power electronic modules - effect of bonding temperature

In this paper, thermal cycling reliability along with ANSYS analysis of the residual stress generated in heavy-gauge Al bond wires at different bonding temperatures is reported. 99.999% pure Al wires of 375 mum in diameter, were ultrasonically bonded to silicon dies coated with a 5mum thick Al metallisation at 25degC (room temperature), 100degC and 200degC, respectively (with the same bonding parameters). The wire bonded samples were then subjected to thermal cycling in air from -60degC to +150degC. The degradation rate of the wire bonds was assessed by means of bond shear test and via microstructural characterisation. Prior to thermal cycling, the shear strength of all of the wire bonds was approximately equal to the shear strength of pure aluminum and independent of bonding temperature. During thermal cycling, however, the shear strength of room temperature bonded samples was observed to decrease more rapidly (as compared to bonds formed at 100degC and 200degC) as a result of a high crack propagation rate across the bonding area. In addition, modification of the grain structure at the bonding interface was also observed with bonding temperature, leading to changes in the mechanical properties of the wire. The heat and pressure induced by the high temperature bonding is believed to promote grain recovery and recrystallisation, softening the wires through removal of the dislocations and plastic strain energy. Coarse grains formed at the bonding interface after bonding at elevated temperatures may also contribute to greater resistance for crack propagation, thus lowering the wire bond degradation rate

‘Old wood’ effect in radiocarbon dating of prehistoric cremated bones?

Numerous reports of successful radiocarbon dating of cremated bones have emerged during the last decade. The success of radiocarbon dating cremated bones depends on the temperature during burning and the degree of recrystallisation of the inorganic bone matrix. During cremation bones undergo major morphological and mineralogical changes which have raised some interesting questions and discussion on the origin of the carbon source in archaeologically cremated bones. Recent laboratory experiments reveal that the properties of the combustion atmosphere play a significant role regarding the source carbon in cremated bones. Thus radiocarbon dating cremated bones is potentially dating the wood used for the cremation fire. Here we compare a high precision radiocarbon dated human bone with an associated dendrochronological age from an oak coffin. We find that the age discrepancy between the dendrochronological age and the cremated bone of 73 ± 26 14C yr is best accounted for by the so called ‘old wood’ effect.

Microabrasion-corrosion of cast CoCrMo alloy in simulated body fluids

Wear and corrosion of metal-on-metal hip replacements results in wear debris and metal-ion release in vivo, which may subsequently cause pain and hypersensitivity for patients. Retrieved metal-on-metal hip replacements have revealed that two-body sliding wear and three-body abrasive wear are the predominant wear mechanisms. However, there is a lack of understanding of the combined effects of wear/corrosion, especially the effect of abrasion-corrosion.

This study investigates the sliding-corrosion and abrasion-corrosion performance of a cast CoCrMo alloy in simulated hip joint environments using a microabrasion rig integrated with an electrochemical cell. Tests have been conducted in 0.9% NaCl, phosphate buffered saline solution, 25% and 50% bovine serum solutions with 0 or 1 g cm(-3) SiC at 37 degrees C. Experimental results reveal that under abrasion-corrosion test conditions, the presence of proteins increased the total specific wear rate. Conversely, electrochemical noise measurements indicated that the average anodic current levels were appreciably lower for the proteinaceous solutions when compared with the inorganic solutions. A severely deformed nanocrystalline layer was identified immediately below the worn surface for both proteinaceous and inorganic solutions. The layer is formed by a recrystallisation process and/or a strain-induced phase transformation that occurs during microabrasion-corrosion. (C) 2008 Elsevier Ltd. All rights reserved.

Thermodynamically stable amorphous drug dispersions in amorphous hydrophilic polymers engineered by hot melt extrusion.

In this study thermodynamically stable dispersions of amorphous quinine, a model BCS class 2 therapeutic agent, within an amorphous polymeric platform (HPC), termed a solid-in-solid dispersion, were produced using hot melt extrusion. Characterisation of the pre-extrudates and extrudates was performed using hyper-differential scanning calorimetry (DSC), powder X-ray diffraction (PXRD) and Raman spectroscopy. Water uptake by the raw materials was determined using dynamic vapour sorption (DVS) analysis. Furthermore, the presence or absence of crystalline drug following storage at 25 °C/60% relative humidity and 40 °C/75% relative humidity in a sealed glass jar, and at 40 °C/75% relative humidity in an open glass jar for 3 months was determined using PXRD. Amorphous quinine was generated in situ during extrusion from both quinine base (5%, 10%, 20% w/w drug loading) and from quinine hydrochloride (5%, 10% w/w drug loading) and remained thermodynamically stable as a solid-in-solid dispersion within the HPC extrudates. When processed with HPC, quinine hydrochloride (20% w/w) was converted to amorphous quinine hydrochloride. Whilst stable for up to 3 months when stored under sealed conditions, this amorphous form was unstable, resulting in recrystallisation of the hydrochloride salt following storage for 1 month at 40 °C/75% relative humidity in an open glass jar. The behaviour of the amorphous quinine hydrochloride (20% w/w) HPC extrudate was related, at least in part, to the lower stability and the hygroscopic properties of this amorphous form.

L’étude de l’InP et du GaP suite à l’implantation ionique de Mn et à un recuit thermique

Cette thèse est dédiée à l’étude des matériaux InMnP et GaMnP fabriqués par implantation ionique et recuit thermique. Plus précisément nous avons investigué la possibilité de former par implantation ionique des matériaux homogènes (alliages) de InMnP et GaMnP contenant de 1 à 5 % atomiques de Mn qui seraient en état ferromagnétique, pour des possibles applications dans la spintronique. Dans un premier chapitre introductif nous donnons les motivations de cette recherche et faisons une revue de la littérature sur ce sujet. Le deuxième chapitre décrit les principes de l’implantation ionique, qui est la technique utilisée pour la fabrication des échantillons. Les effets de l’énergie, fluence et direction du faisceau ionique sur le profil d’implantation et la formation des dommages seront mis en évidence. Aussi dans ce chapitre nous allons trouver des informations sur les substrats utilisés pour l’implantation. Les techniques expérimentales utilisées pour la caractérisation structurale, chimique et magnétique des échantillons, ainsi que leurs limitations sont présentées dans le troisième chapitre. Quelques principes théoriques du magnétisme nécessaires pour la compréhension des mesures magnétiques se retrouvent dans le chapitre 4. Le cinquième chapitre est dédié à l’étude de la morphologie et des propriétés magnétiques des substrats utilisés pour implantation et le sixième chapitre, à l’étude des échantillons implantés au Mn sans avoir subi un recuit thermique. Notamment nous allons voir dans ce chapitre que l’implantation de Mn à plus que 1016 ions/cm2 amorphise la partie implantée du matériau et le Mn implanté se dispose en profondeur sur un profil gaussien. De point de vue magnétique les atomes implantés se trouvent dans un état paramagnétique entre 5 et 300 K ayant le spin 5/2. Dans le chapitre 7 nous présentons les propriétés des échantillons recuits à basses températures. Nous allons voir que dans ces échantillons la couche implantée est polycristalline et les atomes de Mn sont toujours dans un état paramagnétique. Dans les chapitres 8 et 9, qui sont les plus volumineux, nous présentons les résultats des mesures sur les échantillons recuits à hautes températures : il s’agit d’InP et du GaP implantés au Mn, dans le chapitre 8 et d’InP co-implanté au Mn et au P, dans le chapitre 9. D’abord, dans le chapitre 8 nous allons voir que le recuit à hautes températures mène à une recristallisation épitaxiale du InMnP et du GaMnP; aussi la majorité des atomes de Mn se déplacent vers la surface à cause d’un effet de ségrégation. Dans les régions de la surface, concentrés en Mn, les mesures XRD et TEM identifient la formation de MnP et d’In cristallin. Les mesures magnétiques identifient aussi la présence de MnP ferromagnétique. De plus dans ces mesures on trouve qu’environ 60 % du Mn implanté est en état paramagnétique avec la valeur du spin réduite par rapport à celle trouvée dans les échantillons non-recuits. Dans les échantillons InP co-implantés au Mn et au P la recristallisation est seulement partielle mais l’effet de ségrégation du Mn à la surface est beaucoup réduit. Dans ce cas plus que 50 % du Mn forme des particules MnP et le restant est en état paramagnétique au spin 5/2, dilué dans la matrice de l’InP. Finalement dans le dernier chapitre, 10, nous présentons les conclusions principales auxquels nous sommes arrivés et discutons les résultats et leurs implications.

Défauts et diffusion dans le silicium amorphe

Nous avons observé une augmentation ‘’transient’’du taux de cristallisation interfacique de l’a-Si lorsqu’on réimplante du Si à proximité de l’interface amorphe/cristal. Après amorphisation et traitement thermique à 650°C pendant 5s de la couche a-Si crée par implantation ionique, une partie a été réimplantée. Les défauts produits par auto-réimplantation à 0.7MeV se trouvent à (302±9) nm de l’interface initiale. Cela nous a permis d’étudier d’avantage la variation initiale de la vitesse SPE (Épitaxie en phase solide). Avec des recuit identiques de 4h à 500°C, nous avons déterminé les positions successives des interfaces et en déduit les taux de cristallisation SPE. La cristallisation débute à l’interface et continue graduellement vers la surface. Après le premier recuit, (252±11) nm s’est recristallisé dans la zone réimplantée soit un avancement SPE de 1.26x10^18at./cm2. Cette valeur est environ 1.50 fois plus importante que celle dans l’état relaxé. Nous suggérons que la présence de défauts à proximité de l’interface a stimulé la vitesse initiale. Avec le nombre de recuit, l’écart entre les vitesses diminue, les deux régions se cristallisent presque à la même vitesse. Les mesures Raman prises avant le SPE et après chaque recuit ont permis de quantifier l’état de relaxation de l’a-Si et le transfert de l’état dé-relaxé à relaxé.

Imidazole-imidazole stacking in some inorganic complexes

Reaction of CuCl2 center dot 2H(2)O with the 1:1 condensate (L) of 2-(2-aminoethyl) pyridine and 1-methyl-2-imidazolecarboxaldehyde in methanol yields monomeric CuLCl2 center dot H2O (1). Recrystallisation of 1 from aqueous methanol medium containing excess of PF6- affords the 1D coordination polymer [CuLCl](n)(PF6)(n) (2). A chloride bridge results in the coordination polymer. A face-to-face interaction is observed between the imidazole rings in 2. The interaction influences the structure and magnetic properties of 2 markedly. The complex 2 is ferromagnetic with a J value of 1.79 +/- 0.01 cm (1). The imidazole fragments in 2 are coordinated to the metal. In mononuclear [HgL2 ''](ClO4)(2), where L '' is the 1:2 condensate of ethylenediamine and 1-methyl-2-imidazolecarboxaldehyde, the imidazolyl moieties are not under the direct influence of the metal. Here the imidazole-imidazole interaction is angular and more distant. (C) 2009 Elsevier B.V. All rights reserved.

Effect of an ancillary ligand on single helix-double helix interconversion in copper complexes. Copper(I)-water bond

Reaction of Cu(ClO(4))(2)center dot 6H(2)O with the 1:2 condensate of benzildihydrazone and 2-acetylpyridine, in methanol in equimolar ratio yields a green compound which upon recrystallisation from 1:1 CH(2)Cl(2)-C(6)H(6) mixture affords [CuL(H(2)O)](ClO(4))(2)center dot 1/2C(6)H(6). The complex crystallises in the space group P-1 with a = 8.028(11) angstrom, b = 12.316(17) angstrom, c = 18.14(3) angstrom, alpha = 97.191(10)degrees, beta = 94.657(10)degrees and gamma = 108.039(10)degrees. It is single helical with the metal having a distorted trigonal bipyramidal N(4)O coordination sphere. The acid dissociation constant of the Cu(I) complex in CH(3)CN is 3.34 +/- 0.19. The X band EPR spectrum of the compound is rhombic with g(1) = 2.43, g(2) = 2.10 g(3) = 2.02 and A(1) = 79.3 x 10(-4) cm(-1). The Cu(II/I) potential of the complex in CH(2)Cl(2) at a glassy carbon electrode is 0.43 V vs SCE. It is argued that the copper-water bond persists in the corresponding copper(I) species. Its implications on the single helix-double helix interconversion in copper helicates are discussed. DFT calculations at the B3LYP/6-311G** level shows that the binding energy of water in the single helicol live-coordinate copper(I) species [CuL(H(2)O)](+) is similar to 40 kJ mol(-1).

Lightly branched comb polyesters: application in fast drying solvent-borne coating formulations

Novel oxazoline-based comb-polymers possessing linoleyl or oleic side chains have been synthesized and used to produce low viscosity coatings. Inclusion of the polymers in model paint formulations results in coatings that exhibit faster drying times than commercially available alkyd resin formulations. The comb polymers were produced from diol substituted oxazoline monomers that were synthesized through a scalable, solvent free protocol and purified by simple recrystallisation. Co-polymerisation of the oxazolines with adipic acid at 160 °C in the bulk resulted in the targeted polyester comb type polymers. The polymers were soluble in a range of organic solvents and compatible with commercial alkyd resins. Model paint formulations containing up to 40 wt% of the linoleyl-based comb polymers exhibited a dramatic reduction in viscosity (from 35 to 13 Poise at 25 °C) with increasing quantities of polymer added. Dynamic mechanical analysis (DMA) studies revealed that the drying rate of the model paint formulations containing the comb polymers was enhanced when compared with that of commercial alkyd resins.

Influence of deformation conditions and texture on the high temperature flow stress of magnesium AZ31

The evolution of hot working flow stress with strain is examined in torsion, uniaxial compression and channel die compression. The flow stress was found to be strongly dependent on texture and deformation mode. At low strains this dependency accounted for a difference in flow stress of up to a factor of two. At higher strains the influence of texture and deformation mode was less marked. The stresses corresponding to an equivalent strain of 0.5 were modelled using a power law expression with an activation energy of 147 kJ/mol and a strain rate exponent of 0.15. The influence of texture and deformation mode on flow stress is rationalised in terms of the influence of prismatic slip, twinning and dynamic recrystallisation on deformation stress and structure.

Hot working microstructure map for magnesium AZ31

A thermomechanical processing (TMP) structure map is proposed that plots the critical strains required for dynamic recrystallization along with the grain sizes that result. These maps are useful in identifying the limits to grain refinement and designing hot working processes. They are readily constructed for well studied alloys such as plain carbon steel. In light of the recent interest in the hot working of magnesium, initial steps are taken here to construct a TMP structure map for the most common wrought magnesium alloy, AZ31. The completion of dynamic recrystallization is estimated using a geometrical approach and a twinning region is identified.

Effect of grain size on the deformation and dynamic recrystallization of mg-3AI-1Zn

The influence of grain size on the deformation of extruded Mg-3Al-1Zn tested in tension at temperatures between room temperature and 300°C is investigated. The results enable estimation of the deformation conditions for the transition from slip to twinning dominated flow and for the initiation and completion of dynamic recrystallization. A map illustrating these critical parameters is constructed and it is shown that the operating conditions of the common wrought processes straddle key transitions in microstructure behaviour.

An analysis of the transition between strain dependent and independent softening in austenite

The post-deformation softening behaviour of austenite has been studied for various compositions and deformation conditions. The strain at which the transition from strain dependent to strain independent post-deformation softening behaviour occurs (ε*) has been found to coincide closely with the strain to the peak stress (εp) under certain conditions but not under others. It has been proposed that the relationship between ε* and εp may be described geometrically using the initial grain size and the dynamically recrystallised grain size.

Synthesis and structure of bis(para-methoxyphenyl)selenoxide and its monohydrate. theoretical considerations of the hydration of diorganoselenium oxides

The title compound was prepared by base hydrolysis of (p-MeOC₆H₄)₂SeCl₂ in water and isolated as the crystalline monohydrate, (p-MeOC₆H₄)₂SeO·H₂O, in which the water molecule is associated via hydrogen-bonding. Water-free (p-MeOC₆H₄)₂SeO was obtained crystalline after drying and recrystallisation from toluene. Both crystal phases were investigated by single crystal X-ray diffraction. Preliminary DFT calculations at the B3LYP/LANL2DZdp level of theory suggest that the hydrogen bonded complexes R₂SeO·H₂O (R = H, Me, Ph) are by 2.79, 3.36 and 11.10 kcal mol^-1 more stable than the corresponding elusive diorganoselenium dihydroxides R₂Se(OH)₂. The hydrogen bond energies of R₂SeO·H₂O (R = H, Me, Ph) are 5.98, 7.18 and 5.89 kcal mol^-1.

Ultrafine grained structure formation in steels using dynamic strain induced transformation processing

The refinement of ferrite grain size is the most generally accepted approach to simultaneously improve the strength and toughness in steels. Historically, the level of ferrite refinement is limited to 5-10 μm using conventional industrial approaches. Nowadays, though, several thermomechanical processes have been developed to produce ferrite grain sizes of 1-3 μm or less, ranging from extreme thermal and deformation cycles to more typical thermomechanical processes. The present paper reviews the status of the production of ultrafine grained steels through relatively simple thermomechanical processing. This requires deformation within the Ae3 to Ar3 temperature range for a given alloy. Here, the formation of ultrafine ferrite (UFF) involves the dynamic transformation of a significant volume fraction of the austenite to ferrite. This dynamic strain induced transformation (DSIT) arises from the introduction of extensive intragranular nucleation sites that are not present in conventional controlled rolling. The DSIT route has the potential to be adjusted to suit current industrial infrastructure. However, there are a number of significant issues that have been raised, both as gaps in our understanding and as obstacles to industrial implementation. One of the critical issues is that it appears that very large strains are required. Combined with this concern is the issue of whether a combination of dynamic and static transformation can be used to achieve an adequate level of refinement. Another issue that has also become apparent is that grain sizes of 1 μm can lead to low levels of ductility and hence many workers are attempting to obtain 2-3 μm grains, or to introduce a second phase to provide the required ductility. There are also a number of areas of disagreement between authors including the role of dynamic recrystallisation of ferrite in the production of UFF by DSIT, the reasons for the low coarsening rate of UFF grains, the role of microalloying elements and the effects of austenite grain size and strain rate. The present review discusses these areas of controversy and highlights cases where experimental results do not agree.