Residual stress is that which remains in a body that is stationary and at equilibrium with its surroundings. It can be detrimental when it reduces the tolerance of the material to an externally applied force, as is the case with welded joints. On the other hand, it can be exploited to design materials or components which are resistant to damage, toughened glass being a good example. This paper, the second part of a two part overview, the first part having been devoted to measurement techniques, examines the nature and origins of residual stresses across a range of scales. This extends from the long range residual stress fields in engineering components and welded structures, through the interphase stresses present in composites and coatings, to the microscale interactions of phase transformations with local stresses.

/pdf/residual-stress-part-2-nature-and-origins-1cwqch6115.pdf

Residual stress. Part 2 – Nature and origins

Surface integrity in material removal processes: Recent advances

Our safety, comfort and peace of mind are heavily dependent upon our capability to prevent, predict or postpone the failure of components and structures on the basis of sound physical principles While the external loadings acting on a material or component are clearly important, There are other contributory factors including unfavourable materials microstructure, pre-existing defects and residual stresses Residual stresses can add to, or subtract from, the applied stresses and so when unexpected failure occurs it is often because residual stresses have combined critically with the applied stresses, or because together with the presence of undetected defects they have dangerously lowered the applied stress at which failure will occur Consequently it is important that the origins of residual stress are understood, opportunities for removing harmful or introducing beneficial residual stresses recognized, their evolution in-service predicted, their influence on failure processes understood and safe structural integrity assessments made, so as to either remove the part prior to failure, or to take corrective action to extend life This paper reviews the progress in these aspects in the light of the basic failure mechanisms

/pdf/residual-stress-and-its-role-in-failure-2ld6sd4vw6.pdf

Residual stress and its role in failure

Introduction of the Cl- anion in the borate systems generates a new perovskite-like phase, K3B6O10Cl, which exhibits a large second harmonic response, about four times that of KH 2PO4 (KDP), and is transparent from the deep UV (180 nm) to middle-IR region. K3B6O10Cl crystallizes in the noncentrosymmetric and rhombohedral space group R3m. The structure consists of the A-site hexaborate [B6O10] groups and the BX 3 Cl-centered octahedral [ClK6] groups linked together through vertices to form the perovskite framework represented by ABX 3.

https://pubs.acs.org/doi/pdf/10.1021/ja207317d

K3B6O10Cl: a new structure analogous to perovskite with a large second harmonic generation response and deep UV absorption edge.

Constitutive modeling for elevated temperature flow behavior of 42CrMo steel

Das Wechselverformnungsverhalten unlegierter normalisierter Stahle mit Kohlenstoffgehalten 0,1 ≤ C ≤ 1.05 (in Masse-%) ist in totaldehnungskontrollierten mitteldehnungsfreien Versuchen durch ausgepragte zyklische Entfestigungs- und schwache Verfestigungsvorgange gekennzeichnet. Die zyklischen Spannungs-Dehnungskurven werden mit wachsendem Kohlenstoffgehalt zu groseren Spannungsamplituden verschoben. Die mittelspannungsfrei ermittelten zyklischen Spannungs-Dehnungskurven unlegierter Stahle sind unabhangig von der Versuchsfuhrung. Die Ubergangslastspielzahl, bei der in der Dehnungswohlerlinie ea,e = ea,p wird, verschiebt sich mit wachsendem Kohlenstoffgehalt zu kleineren Werten.



In total strain-controlled tests without mean strain the cyclic deformation behaviour of unalloyed normalized steels with carbon contents 0,1 ≤ C ≤ 1,05 (wt.-%) is characterized by pronounced softening and slight hardening processes. With increasing carbon content the cyclic deformation curves are shifted to higher stress amplitudes. Cyclic stress strain curves of unalloyed steels determined in tests without mean load are independent of the testing procedure. With increasing carbon content the number of cycles for ea,e = ea,p (transition point) of strain-controlled SN-curves is shifted to smaller values.

Das totaldehnungskontrollierte Wechselverformungsverhalten unlegierter Stähle im normalisierten Zustand bei Raumtemperatur

Zyklische Verformung von Kupfer und α-Kupfer- Zinn-Legierungen bei konstanter Spannungsamplitude

An Chromstählen mit 0,02% Kohlenstoff und Chromgehalten zwischen 0,17% und 9,21% wurden grundsätzliche Untersuchungen über den Einfluß des Probenzustandes auf die Eigenspannungsausbildung nach Zugverformung durchgeführt. Bei Proben, die aus dem vom Hersteller gelieferten und 5 Stunden bei 400 \"C geglühten Stangenmaterial herausgearbeitet und danach nochmals 2 Stunden bei 520 °C geglüht worden waren, ergaben sich beim Zugversuch z. B. die in Abb. 1 sche-

Notizen: Beispiele anomaler Eigenspannungsbildung bei der Zugverformung von Chrom-Stählen

Der Einfluß der Graphitform auf den Elastizitätsmodul von ferritischen Gußeisenwerkstoffen

Reine Sintereisenwerkstoffe mit Dichten zwischen 6,88 und 7,57 g/cm3 wurden im Temperaturbereich von –184 bis 600°C quasistatisch zugverformt Erganzende Druckverformungen erfolgten bei 20°C Anwachsende Dichte bewirkt ansteigende Werkstoffwiderstands- und Duktilitatskenngrosen aufgrund zunehmender tragender Probenquerschnitte, geringerer Porenzahl, runderer Poren mit geringerer Kerbwirkung sowie einer geringeren Zahl der von Poren ausgehenden Rissen Bei Druckverformung entstehen nach gleichen Deformationen groosere Fliesspannungen als bei Zugverformung, da Porenschlieseffekte und die Behinderung von Risbildungen die tragenden Probenquerschnitte vergrosern Das Verformungsverhalten wird bei tiefen Temperaturen durch thermisch aktivierte Prozesse mit kurzreichenden Wechselwirkungen von Versetzungen mit Gleithindernissen, bei mittleren Temperaturen durch dynamische Reckalterungsvorgange aufgrund von elastischen Wechselwirkungen bewegter Versetzungen mit diffundierenden Kohlenstoffatomen und bei hohen Temperaturen durch erholungskontrollierte Versetzungskriechprozesse bestimmt



Quasistatic deformation behaviour of pure sintered iron in the temperature range between –184 and 600°C



The deformation behaviour of pure sintered iron materials with densities between 6,88 und 7,57 g/cm3 was investigated in tension tests in the temperature range of –184 and 600°C Supplementary compression tests were carried out at 20°C Increasing density leads to increasing material resistances and ductility properties due to the increase of the bearing specimen cross sections as well as due to smaller numbers of pores, more spherical pores with smaller notch effects and smaller numbers of mircocracks, which are initiated at pores After equal deformations, due to pore closing effects and the impediment of crack initation, the flow stresses of compressively deformed specimens are larger than those of tensily deformed The deformation behaviour is dominated at low temperatures by thermal activated glide processes of dislocations and their interactions with short range obstacles, at middle temperatures by dynamic strain ageing due to elastic interactions of glide dislocations and diffusing carbon atoms and at high temperatures by recovery controlled dislocation creep processes

Quasistatisches Verformungsverhalten reiner Sintereisen im Temperaturbereich von -184 bis 600°c

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