Formation of Y2O3 nanoclusters in nano-structured ferritic alloys: Modeling of precipitation kinetics and yield strength

Hin, Céline; Wirth, Brian D.

doi:10.1016/j.jnucmat.2010.04.020

Cited by 74 publications

(28 citation statements)

References 41 publications

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“…Notably, the increase of number density of the dispersoids in the tempered martensite phase after irradiation at 475 C suggests that, during irradiation, coarse dispersoids may dissolve and/or break into fine dispersoids, on the other hand, nucleation of dispersoids may occur as well [43,44].…”

Section: Resultsmentioning

confidence: 99%

Temperature dependent dispersoid stability in ion-irradiated ferritic-martensitic dual-phase oxide-dispersion-strengthened alloy: Coherent interfaces vs. incoherent interfaces

et al. 2016

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a b s t r a c tIn this study, the microstructure of a 12Cr ferritic-martensitic oxide-dispersion-strengthened (ODS) alloy is studied before and after Fe ion irradiation up to 200 peak displacements per atom (dpa). Irradiation temperature ranges from 325 to 625 C. Before irradiation, both coherent and incoherent dispersoids exist in the matrix. In response to irradiation, the mean sizes of dispersoids in both the ferrite and tempered martensite phases change to equilibrium values that increase with irradiation temperature. The evolution of dispersoids under irradiation is explained by a competition between athermalradiation-driven shrinkage and thermal-diffusion-driven growth, with interface coherency affecting the growth mechanism. However, each coherency type exhibits different evolution behavior under irradiation. Coherent dispersoids, regardless of their initial size, change toward an equilibrium size at each temperature tested. On the other hand, incoherent dispersoids are destroyed at lower test temperatures but survive while shrinking in size at higher temperatures. This difference in behavior can be explained by the lower interfacial energy of coherent dispersoids in comparison with incoherent dispersoids. This study sheds light on the roles of interface configurations in maintaining dispersoid integrity under irradiation.

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Section: Resultsmentioning

confidence: 99%

Temperature dependent dispersoid stability in ion-irradiated ferritic-martensitic dual-phase oxide-dispersion-strengthened alloy: Coherent interfaces vs. incoherent interfaces

et al. 2016

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“…Based on Alinger's thesis [37], Hin et al chose a value of 125 MPA in a simple strengthening model [38]. The strengthening contribution due to solid solution s ss is classically used for fcc materials with the following form:…”

Section: Yield Strength Modelingmentioning

confidence: 99%

Tailoring the microstructure and the mechanical properties of ultrafine grained high strength ferritic steels by powder metallurgy

Mouawad

Boulnat

Fabrègue

et al. 2015

Journal of Nuclear Materials

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“…A critical consideration in LEAP data analysis is the number of ions collected from each needle. Thus, the objective of this study is to consider the effect of LEAP collected sample size on the measured cluster size, and to suggest methods to improve the fidelity of comparing average cluster sizes between larger and smaller data sets.The alloys selected for study are a commercial ferritic-martensitic (F-M) steel HCM12A and an oxide dispersion strengthened (ODS) steel, both of which are candidates for advanced reactor cladding and structural components [1]. The HCM12A (Fe-10.5Cr-1.43W-1.5Cu-1.04Ni-0.52Mn-0.3Si) is selected because of its tendency to nucleate Si-Mn-Ni-P-rich and Cu-rich nanoclusters upon irradiation [2], while the ODS (Fe-8.67Cr-1.95W-0.28Y-0.23Ti) is selected because of its pre-existing distribution of Ti-Y-O nanoclusters, which have exhibited varying degrees of morphological stability under irradiation [3].…”

mentioning

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Collected Data Set Size Considerations for Atom Probe Cluster Analysis

Swenson

Wharry

2016

Microsc Microanal

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Atom probe tomography is increasingly being used to complement transmission electron microscopy (TEM) to characterize microstructures, particularly for nano-featured materials containing phases that are below TEM resolution limits. Local electrode atom probe (LEAP) tomographic cluster analysis algorithms provide an objective means to identify and measure the size and number density of these nano-scale phases. However, there is a lack of standardized methodology for quantifying average cluster size, which presents ambiguities and challenges when attempting to compare nanocluster morphology between different specimens. A critical consideration in LEAP data analysis is the number of ions collected from each needle. Thus, the objective of this study is to consider the effect of LEAP collected sample size on the measured cluster size, and to suggest methods to improve the fidelity of comparing average cluster sizes between larger and smaller data sets.The alloys selected for study are a commercial ferritic-martensitic (F-M) steel HCM12A and an oxide dispersion strengthened (ODS) steel, both of which are candidates for advanced reactor cladding and structural components [1]. The HCM12A (Fe-10.5Cr-1.43W-1.5Cu-1.04Ni-0.52Mn-0.3Si) is selected because of its tendency to nucleate Si-Mn-Ni-P-rich and Cu-rich nanoclusters upon irradiation [2], while the ODS (Fe-8.67Cr-1.95W-0.28Y-0.23Ti) is selected because of its pre-existing distribution of Ti-Y-O nanoclusters, which have exhibited varying degrees of morphological stability under irradiation [3]. Both alloys were irradiated to 3 dpa at 500°C, using three different particles -neutrons, protons, and Fe ++ self-ions -for a total of six irradiated samples. Multiple LEAP needles were prepared from each sample using focused ion beam, and each needle was analyzed with a Cameca LEAP 4000X HR. Each LEAP data set was reconstructed with the Integrated Visualization and Analysis Software (IVAS) using the voltage history during the LEAP analysis and was visually inspected to ensure the tip shape was consistent with the SEM image prior to analysis. Cluster analysis was performed on each tip using the maximum separation method, with the parameter d max and N min selected to minimize any spurious detection of clusters [4]. Using the IVAS cluster analysis output data, which includes a radius of gyration (R g ) for each cluster, the Guinier diameter (D G ) for each cluster was determined using [5]:( 1) and then averaged within each LEAP data set (i.e. within each tip).Both the ODS and HCM12A consistently reveal that for a given sample, the average cluster size (i.e. Guinier diameter) increases with the total amount of ranged ions in each sample (i.e. the relative size of the collected sample), as shown in Figure 1. Our observation can be explained by considering the magnification (M) of the tip reconstruction [6]where L is the distance from the sample to the detector, R is the specimen radius of curvature, and ξ is the image compression factor. For each data set reconstruction, ξ was kept ...

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Formation of Y2O3 nanoclusters in nano-structured ferritic alloys: Modeling of precipitation kinetics and yield strength

Cited by 74 publications

References 41 publications

Temperature dependent dispersoid stability in ion-irradiated ferritic-martensitic dual-phase oxide-dispersion-strengthened alloy: Coherent interfaces vs. incoherent interfaces

Temperature dependent dispersoid stability in ion-irradiated ferritic-martensitic dual-phase oxide-dispersion-strengthened alloy: Coherent interfaces vs. incoherent interfaces

Tailoring the microstructure and the mechanical properties of ultrafine grained high strength ferritic steels by powder metallurgy

Collected Data Set Size Considerations for Atom Probe Cluster Analysis

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