Reactivity of Zircaloy-4 with Ti3SiC2 and Ti2AlC in the 1100–1300 °C temperature range

Tallman, Darin J.; Yang, Jian; Pan, Limei; Anasori, Babak; Barsoum, Michel W.

doi:10.1016/j.jnucmat.2015.02.006

Cited by 74 publications

(20 citation statements)

References 48 publications

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“…The thickness of the interaction zone was measured under SEM, which was repeated at least 5 times at the different position of joints. Similar method was adopted in other references as well [15,16]. Fig.…”

Section: Diffusion Kineticsmentioning

confidence: 97%

“…Finally, the maximum shear strength was obtained at 1000 • C for 10 min, measured to be 120 MPa, which was close to that of Ti 3 SiC 2 . Tallman et al [16] attempted to join the Ti 3 SiC 2 and Ti 2 AlC to Zircaloy-4 for nuclear reactor applications. However, all the diffusion couples fractured during sample mounting, which was mainly attributed to residual stresses during cooling process.…”

Section: Introductionmentioning

confidence: 99%

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Microstructure evolution and brazing mechanisms of the Ti2AlC/Ni joints using nickel based filler alloy

Zhang

Duan

et al. 2016

Journal of the European Ceramic Society

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Section: Diffusion Kineticsmentioning

confidence: 97%

Section: Introductionmentioning

confidence: 99%

Microstructure evolution and brazing mechanisms of the Ti2AlC/Ni joints using nickel based filler alloy

Zhang

Duan

et al. 2016

Journal of the European Ceramic Society

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“…Increase in Zr-to-Si ratio on the oxidized surface at 1000 °C without the preoxidation as confirmed in the XPS analysis, and the local silicon rich area in the cross-sectional image of the coating (Figure 3.13c) also support this explanation. According to the diffusion couple experiments between Ti3SiC2 and Zirc-4 [48], the effective diffusion coefficient of Si in Zirc-4 at 1300 °C was approximately six times larger than that at 1100 °C. Therefore, remarkably rapid silicon loss in the coating, which accelerated by the surface oxidation at 1000 °C in the absence of the protective layer, generated microstructural defects (i.e., clusters of voids) in the coating, which in turn induced the crack formation and intensified material degradation.…”

Section: High Temperature Air Oxidation Of Coatingsmentioning

confidence: 99%

“…The compositional ratio of Si to Zr was slightly reduced (less Si) at 700 °C but it increased again (more Si) at 1000 °C and gets doubled at 1200 °C compared to the as-received ZrSi2. Based on the published high diffusion rate of Si compared to Zr [48,49], it appears that a part of newly formed Si during oxidation diffused inward in the thin oxide layer so that the Si concentration on the surface is diminished during oxidation at 700 °C. However, a net outward flux of Si atoms at the higher temperatures increases the Si concentration on the outer-most surface.…”

Section: Evolution Of Oxide Surface Morphology In Zrsi2mentioning

confidence: 99%

Development of Self-Healing Zirconium-Silicide Coatings for Improved Performance Zirconium-Alloy Fuel Cladding

Sridharan

Mariani

Bai

et al. 2018

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Zirconium-alloy fuel claddings have been used successfully in Light Water Reactors (LWR) for over four decades. However, under high temperature accident conditions, zirconium-alloys fuel claddings exhibit profuse exothermic oxidation accompanied by release of hydrogen gas due to the reaction with water/steam. Additionally, the ZrO2 layer can undergo monoclinic to tetragonal to cubic phase transformations at high temperatures which can induce stresses and cracking. These events were unfortunately borne out in the Fukushima-Daiichi accident in in Japan in 2011. In reaction to such accident, protective oxidation-resistant coatings for zirconium-alloy fuel claddings has been extensively investigated to enhance safety margins in accidents as well as fuel performance under normal operation conditions. Such surface modification could also beneficially affect fuel rod heat transfer characteristics. Zirconium-silicide, a candidate coating material, is particularly attractive because zirconium-silicide coating is expected to bond strongly to zirconium-alloy substrate. Intermetallic compound phases of zirconium-silicide have high melting points and oxidation of zirconium silicide produces highly corrosion resistant glassy zircon (ZrSiO4) and silica (SiO2) which possessing self-healing qualities. Given the long-term goal of developing such coatings for use with nuclear reactor fuel cladding, this work describes results of oxidation and corrosion behavior of bulk zirconium-silicide and fabrication of zirconium-silicide coatings on zirconium-alloy test flats, tube configurations, and SiC test flats. In addition, boiling heat transfer of these modified surfaces (including ZrSi2 coating) during clad quenching experiments is discussed in detail. Development of Self-Healing Zirconium-Silicide Coatings for Improved Performance Zirconium-Alloy Fuel Cladding DE-NE0008300 Final Report 5 was also confirmed that the theoretical composition coating enhanced oxidation protection and wear resistance. Distinctive oxide layers of ZrSi2 prepared at 1000 °C and 1400 °C in ambient air were subjected to a 3.9 MeV Si 2+ ions irradiation at 305 °C and their radiation responses were characterized and analyzed. Nanocomposite oxides consisting of ZrO2 nanocrystals embedded in amorphous SiO2 matrix formed on ZrSi2 surface after oxidation at 1000 °C. Radiation-induced phase mixing of the oxide phases and amorphization of ZrO2 was observed up to ~ 820 nm in depth, about one-third of the total radiation damaged region (2.5 µm in thickness) as estimated by SRIM calculation. The ion-mixing was facilitated with fine ZrO2 grains (< 25 nm) at low doses (5 to 10 dpa) but not in larger grains (> 30 nm) even at high damage levels (30 to 60 dpa). Qualitative explanation of the ion-mixing of the nanocomposite was proposed with respect to grain size of ZrO2 in SiO2 matrix. Polygonal crystalline ZrSiO4 grains in dual-layered oxide scale on ZrSi2 at 1400 °C were completely amorphized under the ion-irradiation. Given the high corrosion resistance of ZrSiO4 and immobil...

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“…For example, it has been shown that Ti 3 SiC 2 has superb corrosion resistance to molten Pb and Pb-Bi alloys [20,21]. The diffusion between Zircaloy-4 and the MAX phases Ti 3 SiC 2 and Ti 2 AlC in the 1100-1300 • C range has also been explored [22]. These results show the A-group element diffusing out of the MAX phase and forming intermetallics with the Zr-4, with the penetration depth of the Si in Ti 3 SiC 2 being roughly an order of magnitude less than that of the Al from the Ti 2 AlC.…”

Section: Introductionmentioning

confidence: 99%

On the interactions of Ti2AlC, Ti3AlC2, Ti3SiC2 and Cr2AlC with silicon carbide and pyrolytic carbon at 1300 °C

Bentzel

Ghidiu

Anasori

et al. 2015

Journal of the European Ceramic Society

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a b s t r a c tHerein we report on the reactivity between silicon carbide, SiC, and pyrolytic carbon, PG, with the MAX phases, Ti 2 AlC, Ti 3 AlC 2 , Ti 3 SiC 2 and Cr 2 AlC. Diffusion couples were assembled and heated to 1300 • C under a load corresponding to a uniaxial stress of ∼30 MPa for 4, 10, and 30 h in a vacuum hot press, at a vacuum level of less than 1 Pa. The couples were then examined using optical and scanning electron microscopy, energy-dispersive X-ray spectroscopy, X-ray diffraction, and orientation image microscopy. Based on the totality of the results -after 30 h at 1300 • C -it is concluded that neither Ti 3 SiC 2 nor Cr 2 AlC appear to react with SiC. The former also appears not to react with PG. When heated in the vacuum of the hot press, both Ti 2 AlC and Ti 3 AlC 2 dissociated to form TiC surface layers that were ≈15-20 m thick. After reaction of Ti 2 AlC with SiC and PG, the TiC layer was only ≈10 m thick, indirectly confirming that the dissociation of these phases in vacuum was due to the Al evaporation from the surfaces. The Ti 3 AlC 2 /SiC and Ti 3 AlC 2 /PG diffusion couples resulted in TiC layers that were ≈50 m and ≈100 m thick, respectively. The Cr 2 AlC/PG diffusion couple resulted in the formation of ≈10 m interfacial layer comprised of Cr 3 C 2 and Cr 7 C 3 at the interface between the two materials.

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Reactivity of Zircaloy-4 with Ti3SiC2 and Ti2AlC in the 1100–1300 °C temperature range

Cited by 74 publications

References 48 publications

Microstructure evolution and brazing mechanisms of the Ti2AlC/Ni joints using nickel based filler alloy

Microstructure evolution and brazing mechanisms of the Ti2AlC/Ni joints using nickel based filler alloy

Development of Self-Healing Zirconium-Silicide Coatings for Improved Performance Zirconium-Alloy Fuel Cladding

On the interactions of Ti2AlC, Ti3AlC2, Ti3SiC2 and Cr2AlC with silicon carbide and pyrolytic carbon at 1300 °C

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