Thermal creep of Zr–Nb1%–O alloys: experimental analysis and micromechanical modelling
Introduction
Zirconium alloys, which are widely used in the nuclear industry especially as cladding tubes and guide tubes for pressurized water reactors, can present a variability of their thermomechanical behaviour (e.g. thermal creep) as a function not only of the chemical composition but also of the microstructure. For a better control of the mechanical behaviour of the actual alloys, but also to take into account the evolution of the industrial elaboration processes (chemical composition, thermal treatments, etc.), different studies have been engaged, for instance [1], [2], to build a predictive modelling aiming at a precise description of the relationship between microstructure and effective mechanical behaviour. Following recent studies [3] on the optimization of the M5™ cladding tubes made of ternary alloy (Zr–Nb–O), this paper deals with the understanding of the influence of the microstructure on the thermal creep behaviour of Zr–Nb1%–O alloys at 400 °C. We have worked on fully annealed cladding tubes issued from the same ingot (i.e. same chemical composition) but elaborated using two different thermomechanical treatments which mainly differ by the time spent above the monotectoı̈d transformation (620 °C). These two thermomechanical treatments give rise to two different types of microstructure which apparently mainly differ by the spatial repartition of precipitates. The two alloys are found to exhibit significantly different viscosities under creep loading. Based on an experimental analysis coupled with an homogenization approach, this study contributes (i) to analyze and understand the observed differences on the mechanical behaviour and (ii) to establish a predictive modelling of the thermal creep, based on a physically relevant averaged constitutive relation at the grain scale and an accurate scale-transition scheme.
Section snippets
Elaboration
The products used for this study are Zr–Nb1%–O cladding tubes. All tubes are issued from the same ingot (i.e. same chemical composition, Table 1) and were obtained with identical cold-rolling operations (i.e. identical number of passes and reduction ratio). They only differ by the intermediate heat treatments performed during the cold-rolling process. According to the Zr–Nb phase diagram [4], a monotectoı̈d transformation β-Zr↔α-Zr+β-Nb takes place at about 620 °C, where β-Zr and β-Nb are body
Influence of the microstructure on thermal creep behaviour
The creep response of the Zr–Nb1%–O alloy was investigated at 400 °C in the low-stress domain (i.e. below the yield strength). Indeed, these stress-temperature conditions correspond to the one used industrially to characterize the out-of-pile creep behaviour. In this context, the response to an internal pressure loading with a hoop stress σθθ=130 MPa was first studied. As reported in Fig. 4, the evolution of the effective hoop strain during creep clearly indicates a strong dependence on the
Elastoviscoplastic micromechanical modelling
The homogenization techniques aim at deriving the effective behaviour of heterogeneous materials from the behaviour of their elementary constituents using appropriate average operators. Such an approach is thus well adapted to deal with the relation between microstructure and effective properties. For a comprehensive discussion of this approach in the framework of polycrystals, refer to [11], [12].
In the sequel, the Zr–Nb1%–O polycrystals will be considered as composite materials. Assuming that
Conclusion
The creep responses of two Zr–Nb1%–O alloys have been investigated in details. The two alloys exhibit identical crystallographic textures, grain size, grain shape, and chemical composition. They only differ by the thermal cycles during the elaboration process, alloy A being elaborated at low temperature whereas for alloy B thermal treatments alternate below and above the monotectoı̈d temperature. It has been shown that alloy B deforms by creep about 4 times slower than alloy A. Mechanical tests
Acknowledgements
This work was partially supported by EdF and Framatome ANP Nuclear Fuel, and the cladding tubes were provided by Framatome ANP Zircotube. The authors wish to thank J.P. Mardon (Framatome ANP Nuclear Fuel) for fruitful discussions and express their gratitude to F. Gregori (LPMTM, CNRS) for her generous contribution to the TEM observations.
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