Polytype structure of intermetallic precipitates in zircaloy-4 alloys

Versaci, R.; Ipohorski, M.

doi:10.1016/0022-3115(79)90234-4

Cited by 34 publications

(7 citation statements)

References 2 publications

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“…Table 1). Among the literature many reports exist of both the cubic C15 [13][14][15][16][17][18] and the two hexagonal C14 and C36 [13,[16][17][18][19][20][21][22][23] Laves phases. Due to the nominal composition of commercial alloys, these SPPs have mostly been identified as Zr(Cr,Fe) 2 and Zr(Nb,Fe) 2 , however, they are also known to form with Mo and V additions [13,[24][25][26][27].…”

Section: Crystallography Of Intermetallic Phasesmentioning

confidence: 99%

Hydrogen solubility in zirconium intermetallic second phase particles

Burr

Murphy

Lumley

et al. 2013

Journal of Nuclear Materials

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The enthalpies of solution of H in Zr binary intermetallic compounds formed with Cu, Cr, Fe, Mo, Ni, Nb, Sn and V were calculated by means of density functional theory simulations and compared to that of H in α-Zr. It is predicted that all Zr-rich phases (formed with Cu, Fe, Ni and Sn), and those phases formed with Nb and V, offer lower energy, more stable sites for H than α-Zr. Conversely, Mo and Cr containing phases do not provide preferential solution sites for H. In all cases the most stable site for H are those that offer the highest coordination fraction of Zr atoms. Often these are four Zr tetrahedra but not always. Implications with respect to H-trapping properties of commonly observed ternary phases such as Zr(Cr,Fe) 2 , Zr 2 (Fe,Ni) and Zr(Nb,Fe) 2 are also discussed.

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Section: Crystallography Of Intermetallic Phasesmentioning

confidence: 99%

Hydrogen solubility in zirconium intermetallic second phase particles

Burr

Murphy

Lumley

et al. 2013

Journal of Nuclear Materials

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“…All three have the same stoichiometric formula ZrCr 2 and are all Laves phases, termed C15, C36 and C14 respectively (see Table 1 for further details). Even though the stable phase at reactor operating temperature is α-ZrCr 2 , there have been many reports of both cubic [13][14][15][16][17] and hexagonal [10][11][12][15][16][17][18][19][20] structures in Zr alloys, therefore all three have been considered here. Although the Zr-Ni binary system includes numerous intermetallic phases [21], Zr-Ni SPPs tend to be stable as Zr rich phases, in particular tetragonal Zr 2 Ni.…”

Section: Introductionmentioning

confidence: 99%

Hydrogen accommodation in Zr second phase particles: Implications for H pick-up and hydriding of Zircaloy-2 and Zircaloy-4

et al. 2013

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“…The morphology and size distribution of SPPs depend on several metallurgical factors such as alloy composition, fabrication method and heat-treatment conditions, and in addition -during serviceon irradiation dose and temperature (Vander Sande & Bement, 1974;Paul et al, 2010). Several studies have been conducted in the past to understand the influence of heat treatment and thermomechanical treatments on the formation of SPPs and their impact on the corrosion resistance of these alloys (Versaci & Ipohorski, 1979;Fong & Northwood, 1982;Chemelle et al, 1983;Yang, 1988). It was found that there is a strong correlation between precipitate size distribution and nodular (localized) corrosion resistance.…”

Section: Introductionmentioning

confidence: 99%

Ultra-small-angle X-ray scattering study of second-phase particles in heat-treated Zircaloy-4

et al. 2015

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The ultra-small-angle X-ray scattering (USAXS) technique has been used to investigate and to quantify the morphology and size distribution of secondphase particles in Zircaloy-4 under various heat-treatment conditions. The alloy samples were solutionized in the phase field at 1293 K for 15 min and then cooled at different rates, including water quenching, air cooling and furnace cooling. The water-quenched samples were subsequently subjected to a thermal aging treatment at 873 K for different aging times (30, 60, 120 and 300 min). The USAXS results show that water quenching and air cooling from the phase field produces a narrow size distribution of fine-size precipitates with an average diameter of 300-800 Å , while furnace cooling resulted in coarsening of the particles, with a broad size distribution having an average precipitate size of 600-1200 Å . Further, the furnace-cooled sample shows a higher volume fraction of particles than the water-quenched or air-cooled sample. The USAXS results on the quenched then aged samples show that aging at 873 K for 10 min resulted in very fine size precipitates with an average diameter of 200-350 Å . A rapid precipitation with the highest number density of second-phase particles amongst all the heat-treated samples (4.3 Â 10 20 m À3 ) was observed in the sample aged for 10 min at 873 K. Particles of larger size and with a broad size distribution were observed in the sample aged at 873 K for 300 min. A bimodal type of particle size distribution was observed in all the heat-treated samples. Important parameters in the characterization of second-phase particles, such as the average size, size distribution, volume fraction and number density, were evaluated and quantified. These parameters are discussed for both heat-treated and aged specimens. Transmission and scanning transmission electron microscopy characterization were carried out on all heat-treated samples, to assist in interpretation and to substantiate the results from the USAXS measurements.

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Polytype structure of intermetallic precipitates in zircaloy-4 alloys

Cited by 34 publications

References 2 publications

Hydrogen solubility in zirconium intermetallic second phase particles

Hydrogen solubility in zirconium intermetallic second phase particles

Hydrogen accommodation in Zr second phase particles: Implications for H pick-up and hydriding of Zircaloy-2 and Zircaloy-4

Ultra-small-angle X-ray scattering study of second-phase particles in heat-treated Zircaloy-4

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