Abstract
This article discusses six cases of ancient silver embrittlement. The diagnostic techniques and results are surveyed, followed by the most likely explanations of embrittlement. There are two basic types of embrittlement: corrosion-induced, and microstructurally induced, which can act synergistically. Corrosion-induced embrittlement takes several forms, including what appears to be intergranular and transgranular stress corrosion cracking. The main intrinsic factor facilitating corrosion-induced embrittlement is retained cold-work in the silver. Microstructural embrittlement is characterized by intergranular fracture, most probably due to low-temperature segregation of lead to the grain boundaries. Knowledge of the details of embrittlement can be essential for optimizing the restoration and conservation of damaged artifacts.
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Introduction
Ancient silver artifacts are rare and valuable exhibits in many museums. Some are apparently in excellent condition, but others may have been badly damaged and embrittled during many centuries of burial. Preservation of these artifacts depends, or should depend, on a detailed understanding of the types of damage and embrittlement.
Since 1994, the NLR has investigated four cases of ancient silver embrittlement [1–7], one as a re-assessment [7], and reviewed two cases investigated by others [8–11]. Experience and insight gained from the investigations enables presenting the most likely explanations of embrittlement for all six cases. This is the main topic of this article.
The Artifacts
Five of the ancient silver artifacts are illustrated in Figs. 1–5. The Gundestrup Cauldron, Egyptian Vase, and Roman Kantharos (drinking cup) are about 2000 years old. The Byzantine Paten (altar plate) and Romanesque Kaptorga (small container for relics and amulets) date from the 7th and 10th centuries AD, respectively. The sixth artifact is a Sasanian King’s Head [11], dating from the 4th century AD. The Kaptorga and Head are the subjects of the reviewed cases mentioned above [8–11].
The artifacts are very different in form and origin. This is advantageous for the consistency of some of the explanations of the types of embrittlement.
Diagnostic Techniques
Table 1 lists the diagnostic techniques (besides visual observation) used for examining small (usually millimeter-size) samples from the artifacts. Limitations were imposed by the available samples and techniques. Fractography could not be done on the metallographic samples from the Cauldron and Paten; chemical analyses other than EDX were not possible for the Vase and Kaptorga; and EBSD was available only for the Cauldron. Also, only a sample from the Kantharos inner cup was available.
Survey of the Results
Tables 2 and 3 depict the survey of the results of the investigations. The results are discussed in the two main sections of this article later, where links between the types of embrittlement, artifact microstructure, and composition are indicated. For the Kaptorga, the possible contribution of the burial environment, a grave, is also considered.
Corrosion-Induced Embrittlement
Intergranular Corrosion and Cracking
Tables 2 and 3 show that corrosion-induced intergranular embrittlement was observed in samples from the Cauldron, Paten, Kaptorga and Head [4–6, 8–11]. This type of embrittlement has been attributed to segregation of copper to grain boundaries, either during cooling from final annealing during fabrication, or during long-term burial at ambient temperatures [9, 12–15]. In particular, the eminent metallurgist C. S. Smith was of the opinion that the so-called discontinuous precipitation of copper seems to be very detrimental [12]. This precipitation can cause the grain boundaries to appear irregular and meandering, particularly in ancient silver.
The unembrittled sample 366 from the Cauldron and the embrittled Paten and Head samples showed evidence of discontinuous precipitation, see Figs. 6–8. However, the embrittled samples from the Cauldron and Kaptorga did not. Hence, this type of precipitation is not needed for corrosion-induced intergranular embrittlement, and in the case of the Cauldron, it was innocuous.
For the Cauldron, the EBSD examination demonstrated a strong link between the amount of retained cold-work, degree of embrittlement and the presence or absence of discontinuous precipitation [4–6]. Figures 6 and 9 show examples from the two extremes, samples 365 and 366. The annealed sample 366, Fig. 6, was undamaged even though precipitation was present at many grain boundaries. However, the heavily cold-worked sample 365, Fig. 9, showed severe intergranular and transgranular corrosion, with no evidence of precipitation. The intermediately cold-worked samples 361 and 363 also showed intergranular corrosion, though less severe, and again without precipitation [4, 5]. It appears that cold-work suppressed the precipitation, since the annealed sample 366 contained less copper (3.44 wt.%) than sample 361 (4.64 wt.%), see Table 3. In this respect, it is noteworthy that precipitation in the cold-work-containing Head (84 HV vs. 43 HV fully annealed) was barely detectable, Fig. 8, even though the copper content was about 5 wt.% [11].
Although the Cauldron results show retained cold-work is important, it is not always needed for corrosion-induced intergranular embrittlement. The Kaptorga has a fully annealed microstructure (without discontinuous precipitation, as mentioned above) but has been severely embrittled and highly fragmented [8–10]. Figure 10 shows an SEM metallograph and fractograph of samples showing (a) corrosion pitting at grain boundaries, linking to form cracks, and (b) corrosion-induced “clean” intergranular fracture being slowly destroyed by general corrosion. By analogy with clean intergranular stress corrosion cracking (SCC) followed by general corrosion in an aluminium–lithium alloy [16], the Kaptorga intergranular fracture has been suggested to be SCC also [6].
Since the Kaptorga silver was fully annealed [9], SCC would have had to result from external crushing forces combined with a particularly adverse environment. Both are distinct possibilities resulting from the grave burial: besides the weight of the soil, especially on hollow artifacts like the Kaptorga, the groundwater in graves can be very saline owing to human decomposition [17]. Support for these possibilities comes from another grave burial artifact, the Khan Cup, which was highly fragmented owing to “crystalline” fracture [18].
Transgranular Corrosion and Cracking
Tables 2 and 3 show that corrosion-induced transgranular embrittlement was observed in samples from the Cauldron (365) and Vase. The Vase has so far proven to be unique in undergoing synergistic corrosion-induced (transgranular) and microstructural (intergranular) embrittlement [1–5]. This synergy has been very damaging, but it has enabled the transgranular corrosion and cracking to be well characterized. This is because microstructural embrittlement caused intergranular break-up of the samples and revealed the internally-developing processes of corrosion-induced embrittlement from initiation to complete fracture.
The Vase underwent corrosion and cracking along slip lines and deformation twin boundaries owing to retained cold-work; and also corrosion along segregation bands, which were the much-modified remains of high-temperature solute element segregation (coring) during solidification. Examples are shown in Figs. 11 and 12, whereby the fractograph shows crystallographic cracking mainly along slip planes, followed by general corrosion destroying the fracture surfaces. As in the case of corrosion-induced intergranular embrittlement of the Kaptorga, Fig. 12 suggests a process of SCC, in this case transgranular.
More evidence for transgranular SCC was obtained from intergranular break-up of the samples. Figure 13 illustrates (a) the beginning of slip plane corrosion (pitting, most probably at emergent dislocations), (b) cracking, and (c) the resulting crystallographic fracture into blocks. The 90° “dog-leg” crack in Fig. 13b is significant, as are the high-angle narrow sides of the blocks in Fig. 13c. Given that the slip plane cracks are on {111} planes, the “dog-leg” crack cannot be on a {111} plane, but must be on either a {110} or {112} plane. The high-angle block sides are also likely to be on one of these planes. As explained in Ref. [6], these observations favor the strain-enhanced dissolution model of SCC proposed by Lichter et al. [19].
Rationale Linking Intergranular and Transgranular Cracking
The case history evidence may be interpreted to provide an overall rationale for corrosion-induced intergranular and transgranular cracking. Intergranular pitting and cracking is probably SCC caused by local strains (and compositional variations, particularly copper) at and near grain boundaries. The local strains derive from external forces (Kaptorga) and/or retained cold-work (Cauldron, Paten, and Head).
More retained cold-work (Cauldron, sample 365, Vase) increases the tendency for transgranular SCC, which is caused mainly by local strains because of dislocation pile-ups on slip planes. However, there is some contribution from local strains on “dog-leg” crystallographic planes and deformation twin boundaries.
Microstructural Embrittlement
Table 2 shows that microstructural embrittlement was observed in samples from the Vase and Kantharos inner cup. This type of embrittlement is fortunately less common than corrosion-induced embrittlement, since it occurs throughout the artifacts, leaving them particularly susceptible to fragmentation. (However, see the comments in the next section of this article concerning the brittleness of the Vase, Kantharos inner cup and Kaptorga.)
Microstructural embrittlement is characterized by zero-ductility intergranular fracture, with sharply defined cracks and grain boundary facets, and bodily displaced grains [1–6]. Examples are given in Figs. 14 and 15. In particular, the bodily displaced grains demonstrate the severity of this type of embrittlement.
Embrittlement is most probably caused by low-temperature ageing, whereby an impurity element, or elements, segregates to grain boundaries throughout the artifact. The available evidence, including the Vase and Kantharos compositions listed in Table 2, indicates lead to be the most likely perpetrator [20, 21], though this has yet to be verified directly, e.g., by Auger spectroscopy. Other impurity elements might be involved, notably bismuth [11, 21], though apparently not for the Vase and Kantharos, see Table 2.
Remedial Measures: Comments from the Case Histories
Restoration and conservation of embrittled silver has been discussed in many publications, e.g. Refs. [1, 2, 4, 6–8, 11, 14, 18, 21–23]. The modern view is to consider both technical and ethical aspects. Preference is therefore given to reversible remedial measures that respect an artifact’s integrity, meaning veracity rather than wholeness. However, the second meaning, wholeness, can dictate the remedial measures: non-reversible consolidation is essential for preserving severely embrittled and fragmented artifacts [8, 10, 18, 22, 23].
Detailed case histories can be important in resolving the issue of reversible versus non-reversible restoration. Looking to the six case histories discussed in this article, the Cauldron, Paten, and Head are in generally good condition. Further conservation measures, if any, would likely be limited to periodic cleaning and possible application of removable protective coatings. Even so, the choice of cleaning methods and coatings requires careful consideration [4, 6, 11, 22, 24].
In contrast, the Vase, Kantharos inner cup and Kaptorga have been severely embrittled. From a fundamental point of view, one would expect the Kaptorga to be less fragile than the Vase and Kantharos inner cup. Any non-cracked areas of the Kaptorga should have retained the high ductility of annealed silver now that it is removed from the burial environment, but the Vase and Kantharos inner cups are now intrinsically brittle. In practice, however, the intergranular cracking in the Kaptorga has been so extensive that the fragments continued to break up even during careful handling before restoration [8]. Hence, all three artifacts were very fragile before restoration, and they have been non-reversibly restored.
The Vase restoration is old (and crude by modern standards), involving extensive use of an organic filler material. The Kantharos (both cups) has been restored by impregnation with an epoxy resin [7]. However, the tight cracks shown in Fig. 15 were free of resin, which suggests that the restoration has been only partly successful. The Kaptorga has been very carefully restored using an external and removable backing of silk and acrylic lacquer, followed by an internal backing of fine glass cloth and epoxy resin [8]. The external backing was then removed with acetone. This is a similar technique to that used for the Khan Cup [18].
Concluding Remarks
Ancient silver artifacts are rare and valuable museum exhibits. Consequently, it is difficult to obtain samples from the embrittled artifacts for detailed investigations. However, the case histories discussed in this article demonstrate that modern diagnostic techniques applied to small samples can tell much about the types of embrittlement and the conditions of the sampled artifacts. This knowledge can be essential for optimizing the preservation of these and other damaged artifacts.
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Acknowledgments
The author is indebted to several colleagues for providing information and assistance with obtaining and analyzing samples from the artifacts discussed in this article: Ron Leenheer, Allard Pierson Museum, Amsterdam; Peter Northover, Oxford University, Oxford; Joanna Cook, The Menil Collection, Houston; Ronny Meijers, Museum Het Valkhof, Nijmegen; Jiří Děd and Jarka Vaníčková, Institute of Chemical Technology, Prague; Ineke Joosten, Netherlands Institute for Cultural Heritage, Amsterdam; and Jean-Paul Steijaert and Tim Hattenberg, NLR.
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Wanhill, R.J.H. Case Histories of Ancient Silver Embrittlement. J Fail. Anal. and Preven. 11, 178–185 (2011). https://doi.org/10.1007/s11668-010-9429-5
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DOI: https://doi.org/10.1007/s11668-010-9429-5