Electron Metallography of Chemical Attack Upon Some Alloys Susceptible to Stress Corrosion Cracking

Abstract

The microstructures of deformed copper-gold, copper-aluminum, copper-zinc and magnesium-aluminum alloys were examined by transmission electron microscopy. These specimens were further examined after exposure to solutions which do and do not cause stress corrosion cracking. Exposure to “cracking” solutions resulted in a localized pitting or tubular form of attack, whereas the solutions which did not produce cracking caused a uniform surface roughening. When thin-foil specimens were deformed within the corrosive environments, the tubular attack and the surface roughening were observed to be enhanced in the regions of heavy deformation. Observations also indicated that for all the alloys investigated, static dislocations did not initiate chemical attack. In general, the pitting or tubular type of attack may be initiated at grain boundaries, antiphase boundary junctions in ordered copper-gold alloys, at precipitates and the substructure of twins in magnesium-aluminum alloys and at other sites which could not be identified. It was concluded that compositional rather than physical disturbances initiate preferential chemical attack on the surface of the alloys studied. For copper-gold alloys the superficial chemical disturbance can be as small as a six-atom cluster. Rates of pitting greater than 0.4 cm/hr can be attained for copper-gold alloys, which compares well with stress corrosion crack velocities. In the discussion of these results a new mechanism for transgranular stress corrosion is presented. It is proposed that when susceptible alloys are exposed to stress corrosion cracking environments a mechanically weak, pitted structure is produced along active slip planes, and that ductile fracture occurs through this corroded material. The chemical activity of the slip planes, which are believed to initiate the pitting attack, is discussed in relation to (a) the type of surface slip structure found in alloys where cross slip is difficult, (b) increase in solute atom concentration at the crack tip through the mass transfer of solute atoms to the surface by planar groups of moving dislocations, and (c) segregation and precipitation on slip planes. It was found that very fine precipitates, which are either an intermediate magnesium-aluminum phase or Mg17Al12, formed on the basal planes of quenched magnesium-1 or 7 atomic percent aluminum (<0.001 percent Fe, Cu or Ni) alloys when aged at room temperature. The presence of these precipitates was associated with the transgranular stress corrosion susceptibility of these alloys.

Understanding Magnesium Corrosion—A Framework for Improved Alloy Performance

“…Makar et al, [90] however, attributed the EAC mechanism to a brittle hydride forming ahead of the crack tip; they also indicated that the diffusion coefficient for hydrogen in magnesium has not been measured. Pickering and Swan [91] advocated a mechanism involving corrosion tunnels, whereas Pugh and coworkers [92] advocated a mechanism of a rupture of a brittle surface film. Since these studies, there have been significant developments in the mechanistic understanding of EAC.…”

Plasmonic nanosponges

“…Actually, this method has already been used as the technique for 'depletion gilding' throughout the centuries in Europe [26,27]. However, the porous structure was identified for the first time using transmission electron microscopy (TEM) till to 1963 [28].…”

Mg and Its Alloys for Biomedical Applications: Exploring Corrosion and Its Interplay with Mechanical Failure

“…The tunnelling model was proposed by Pickering and Swan [97] and is characterized by the formation of tubular pits due to the rupture of the surface film at emerging slip steps (Figure 5a). At the beginning, the direction of these pits is considered to be governed by the electrochemical potential difference between the Mg matrix and the second phase that they assumed to be Mg 17 Al 12 .…”