Corrosion-induced hydrogen embrittlement in aluminum alloy 2024
Introduction
The structural integrity of aging aircraft structures can be affected by corrosion. As the time of an aircraft in service increases, there is a growing probability that corrosion will interact with other forms of damage, such as single fatigue cracks or multiple-site damage. The aging aircraft may have accumulated corrosion damage over the service life and its residual strength depends on possible degradation stemming from corrosion-induced embrittling mechanisms. One characteristic example where failure was attributed to multi-site damage (MSD) has been the Aloha Airlines accident in 1988. Damage was attributed to growth and linkage of multiple fatigue cracks, emanating from rivet holes [1]. Recent investigations on fire fighting planes of the Hellenic Aerospace Industry has also shown considerable corrosion damage around rivet holes [2].
There are two key questions regarding this issue: (1) Is there a corrosion-induced degradation of ductility, which in turn degrades damage tolerance and the residual strength of aerostructures? and (2) What is the underlying corrosion-induced embrittling mechanism? The answer to the first question has been given by a series of experiments [3], [4], [5], involving mechanical testing of pre-corroded alloy 2024. It was shown that (i) degradation of ductility and of fatigue life increases with corrosion exposure time and (ii) removal of the corrosion layer restores strength but not ductility. These results were attributed to the operation of a bulk corrosion-induced embrittlement mechanism, and it was suggested that hydrogen might be a possible underlying cause.
Other researchers have also considered hydrogen as an embrittlement mechanism in Al-alloys. Studies by Scamans et al. [6] of Al embrittlement in humid air, argued for a major role of hydrogen. In particular, the intergranular crack path and the reversibility of the phenomenon (recovery of ductility after degassing) supported a hydrogen rather than an anodic dissolution mechanism. Also, Scamans and Tuck [7] measured hydrogen permeability and stress corrosion resistance of the Al–Mg–Zn alloy, as functions of quench rate and aging treatment, and found similar trends. Speidel [8] reviewed results up to 1992, mainly for Al–Mg–Zn alloys. More recently, Young and Scully [9] considered the kinetics of crack growth of aluminum alloy 7050 in a humid air environment and confirmed that hydrogen embrittlement was the controlling mechanism. Jones [10] summarized evidence for hydrogen uptake and its contribution to crack growth for the low-strength alloy 5083.
Hydrogen is produced by surface corrosion reactions and part of it is absorbed in atomic form into the material [11]. In particular, the production of atomic hydrogen by a single-electron transfer process, according to the reactionH2O + e− → OH− + Hmakes water an aggressive environment for aluminium alloys [9]. Absorbed hydrogen diffuses towards the interior of the material and may be retained at various preferential locations. More specifically, it has been shown [12], [13] that lattice defects (vacancies, dislocations, grain boundaries) and precipitates provide a variety of trapping sites. Hydrogen traps are mechanistically classified as reversible and irreversible [14], depending on the steepness of the energy barrier needed to be overcome by hydrogen to escape from them.
Thermal desorption has been successfully used to study hydrogen diffusion and trapping in pure aluminium [15], [16], Al–Cu, Al–Mg2Si [13] and Al–Li alloys [17]. It has also been combined with accelerated corrosion tests in order to characterize corrosion and hydrogen absorption in alloy 2024 [18], [19]. In the last two works, the existence of multiple trapping states was verified and the quantity and evolution pattern of hydrogen was discussed. The goal of the present study is to link hydrogen uptake and trapping to material embrittlement.
Section snippets
Experimental procedures
The material used for the present study was alloy 2024-T351, supplied in thicknesses 1.6–3.0 mm. The chemical composition of the alloy (wt.%) is: Al–4.35Cu–1.5Mg–0.64Mn–0.5Si–0.5Fe. Exfoliation corrosion testing (EXCO) was performed according to ASTM specification G34-90 [20]. It included exposure at 25 ± 0.5 °C, in a solution containing 234 g NaCl, 50 g KNO3 and 6.3 ml concentrated HNO3 (70 wt.%) diluted to 1 L of distilled water. Exposure times in the EXCO solution ranged from 15 min to 96 h. Specimen
Microstructural description of corrosion
Corrosion in this alloy starts in the form of pitting. Pits begin to appear as early as after 15 min of exposure and are mainly located at intersections of cracks in the protective surface oxide layer (Fig. 1a). With exposure time pits become deeper and start to be connected by a network of intergranular corrosion paths (Fig. 1b). This process of pit-to-pit interactions leads to pit clustering and coalescence (Fig. 1c). From that point on, corrosion does not penetrate much deeper but instead
Conclusions
The experiments performed in this work lead to the following conclusions regarding corrosion-induced hydrogen embrittlement in aircraft Al-alloys:
- 1.
Corrosion damage starts with pitting and proceeds to pit-to-pit interactions, intergranular attack and exfoliation.
- 2.
Hydrogen is produced during the corrosion process and is being trapped in distinct states in the interior of the material.
- 3.
The temperature of hydrogen evolution and the variation of hardness with heating provide indirect evidence of the
Acknowledgment
Part of this work has been financially supported by the Greek Secretariat of Research and Technology (GSRT) and by AirBus.
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