Grain boundary energy and grain growth in Al films: Comparison of experiments and simulations

Barmak, K.; Kim, J.; Kim, C.-S.; Archibald, Wayne E.; Rohrer, Gregory S.; Rollett, Anthony D.; Kinderlehrer, David; Ta’asan, Shlomo; Zhang, Hao; Srolovitz, David J.

doi:10.1016/j.scriptamat.2005.11.060

Cited by 67 publications

(27 citation statements)

References 13 publications

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“…The observations of thin film growth at elevated substrate temperature are in qualitative agreement with models proposed for grain growth and preferred texture in thin films as well as their experimentally observed impact on magnetic properties (Bertotti 1998;Barmak et al 2006). For example, it has been proposed (Barmak et al 2006) that when the nuclei grow as spherical-cap-shaped islands, they will be surrounded by a zone of width d, in which any atom deposited on the substrate surface within a distance d, of a pre-existing island will diffuse to that island and become part of it instead of becoming part of a new nucleus.…”

Section: Resultssupporting

confidence: 86%

Effect of microstructural evolution on magnetic properties of Ni thin films

2009

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The magnetic properties of Ni thin films, in the range 20-500 nm, at the crystalline-nanocrystalline interface are reported. The effect of thickness, substrate and substrate temperature has been studied. For the films deposited at ambient temperatures on borosilicate glass substrates, the crystallite size, coercive field and magnetization energy density first increase and achieve a maximum at a critical value of thickness and decrease thereafter. At a thickness of 50 nm, the films deposited at ambient temperature onto borosilicate glass, MgO and silicon do not exhibit long-range order but are magnetic as is evident from the non-zero coercive field and magnetization energy. Phase contrast microscopy revealed that the grain sizes increase from a value of 30-50 nm at ambient temperature to 120-150 nm at 503 K and remain approximately constant in this range up to 593 K. The existence of grain boundary walls of width 30-50 nm is demonstrated using phase contrast images. The grain boundary area also stagnates at higher substrate temperature. There is pronounced shape anisotropy as evidenced by the increased aspect ratio of the grains as a function of substrate temperature. Nickel thin films of 50 nm show the absence of long-range crystalline order at ambient temperature growth conditions and a preferred [111] orientation at higher substrate temperatures. Thin films are found to be thermally relaxed at elevated deposition temperature and having large compressive strain at ambient temperature. This transition from nanocrystalline to crystalline order causes a peak in the coercive field in the region of transition as a function of thickness and substrate temperature. The saturation magnetization on the other hand increases with increase in substrate temperature.

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Section: Resultssupporting

confidence: 86%

Effect of microstructural evolution on magnetic properties of Ni thin films

2009

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“…The reason is that the special boundaries of this kind are more ordered and have a lower specific grain boundary energyup to ~10% lower than those of regular high-angle grain boundaries [45]. In more recent investigations, even larger differences in the energies between ∑7 and regular high angle grain boundaries have been reported in Al films [46] and polycrystalline nickel [1], respectively. Such special boundaries are less affected by concurrent precipitation and solute drag effects, firstly because the highly ordered structure yields less potential for nucleation of dispersoids, and secondly since the reduced grain boundary energy GB leads to a lower Zener drag (Eq.…”

Section: Impact Of Concurrent Precipitation On Texturementioning

confidence: 98%

Evolution in microstructure and properties during non-isothermal annealing of a cold-rolled Al–Mn–Fe–Si alloy with different microchemistry states

Huang

Engler

et al. 2015

Materials Science and Engineering: A

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The softening behaviour during non-isothermal annealing of a cold-rolled Al-Mn-Fe-Si model alloy was studied as a function of the state of microchemistry, in terms of the solute level of Mn, size and spatial distribution of the Mn-bearing dispersoids, as well as their temporal evolution. Microchemistry significantly affects the recrystallization microstructure, crystallographic texture as well as the mechanical property of the investigated alloy after non-isothermal annealing. The nucleation and growth of grains with different orientations are strongly dependent on both annealing temperature and microchemistry, in that pre-existing dispersoids have a less profound effect on retarding recrystallization than dispersoids forming concurrently during back-annealing. Strong concurrent precipitation suppresses nucleation and retards recrystallization, which finally leads to a coarse and pan-cake shaped grain structure, accompanied by strong P {011}<566> and/or M {113}<110> texture components and a relatively weaker ND-rotated cube {001}<310> component. A refined grain structure with medium strength P and cube {001}<100> components is obtained when the pre-existing dispersoids are coarser and fewer, and concurrent precipitation is limited. Porientated grains are less affected by second phase particles and experience a growth advantage at low annealing temperatures (<350°C), while M-orientated grains appear at higher temperatures. The intensity of the P texture does not necessarily increase with increasing supersaturation of Mn as observed during isothermal annealing, whereas the level of supersaturated Mn promotes the strength of the M texture. The mechanisms behind are discussed.

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“…In general, the grain boundary energy can vary as a function of all five macroscopic crystallographic parameters (three for lattice misorientation and two for grain boundary plane orientation) that are used to classify a grain boundary. Because of the large number of different grain boundaries, past measurements of grain boundary energies in face-centered cubic (fcc) metals have been made over a limited range of the crystallographic parameters [2][3][4][5][6][7][8][9][10][11][12][13][14][15][16]. In this paper, we report the relative grain boundary energies of nickel as a function of all macroscopic five crystallographic parameters, a quantity that will be referred to as the grain boundary energy distribution (GBED).…”

Section: Introductionmentioning

confidence: 99%

Relative grain boundary area and energy distributions in nickel

2009

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The three-dimensional interfacial network of grain boundaries in polycrystalline nickel has been characterized using a combination of electron backscatter diffraction mapping and focused ion beam serial sectioning. These data have been used to determine the relative areas of different grain boundary types, categorized on the basis of lattice misorientation and grain boundary plane orientation. Using the geometries of the interfaces at triple lines, relative grain boundary energies have also been determined as a function of lattice misorientation and grain boundary plane orientation. Grain boundaries comprising (1 1 1) planes have, on average, lower energies than other boundaries. Asymmetric tilt grain boundaries with the R9 misorientation also have relatively low energies. The grain boundary energies and areas are inversely correlated.

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Grain boundary energy and grain growth in Al films: Comparison of experiments and simulations

Cited by 67 publications

References 13 publications

Effect of microstructural evolution on magnetic properties of Ni thin films

Effect of microstructural evolution on magnetic properties of Ni thin films

Evolution in microstructure and properties during non-isothermal annealing of a cold-rolled Al–Mn–Fe–Si alloy with different microchemistry states

Relative grain boundary area and energy distributions in nickel

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