On the Zener drag

Nes, E.; Ryum, N.; Hunderi, O.

doi:10.1016/0001-6160(85)90214-7

Cited by 771 publications

(321 citation statements)

References 9 publications

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“…[5][6][7][8]). Alloy variants with a large fraction of small dispersoids will experience large back-driving force and, hence, slow recrystallization kinetics (cf.…”

Section: Concurrent Precipitationmentioning

confidence: 99%

“…Fine dispersoids exert a pinning effect on both high and low angle boundaries [6,7], where a broader size distribution of fine dispersoids leads to a larger effective Zener drag pressure [8]. Coarse particles (>1µm), typically formed during casting, may provide sites for particle stimulated nucleation (PSN) and thus accelerate recrystallization [9], in contrast.…”

Section: Introductionmentioning

confidence: 99%

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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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“…[5][6][7][8]). Alloy variants with a large fraction of small dispersoids will experience large back-driving force and, hence, slow recrystallization kinetics (cf.…”

Section: Concurrent Precipitationmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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 interaction between the grain boundary and an impurity, which results in reduction of the driving force for migration, can be quantified by the so-called Zener drag. Zener formulated equations to calculate the influence of second-phase particles on a moving grain boundary based on laboratory experiments [36]. That the results achieved during laboratory studies can approximate the interaction of crystal growth and a dispersion of secondphase particles in geological systems was shown by Mas and Crowley [34], who achieved a quantitative analysis of the relationship between second-phases and the grain size in marble.…”

Section: Drag Force Of Mobile Particlesmentioning

confidence: 99%

“…In order to calculate the drag force of a single second-phase particle the assumption has to be made that the surface tensions of the particle and the grain boundary are in equilibrium. If this is assumed and the grain boundary meets the obstacle at an angle of 90 • , the two tensions will cancel out leaving only one surface tension (γ ) [36]. This surface tension is the internal energy of the matrix/matrix boundary and not of the matrix/particle interface [25].…”

Section: Drag Force Of Mobile Particlesmentioning

confidence: 99%

“…This force is highest for angles of 45 • between the bend grain boundary and an imaginary undeformed boundary. The area increase and the applied drag force from particle result in a higher energy needed for grain boundary migration and therefore slow down or even inhibit further grain boundary migration [after Nes et al [36]]. (B) Concept of the Zener pressure applied to a grain boundary by multiple spherical, coherent particles of the same radius.…”

Section: Drag Force Of Mobile Particlesmentioning

confidence: 99%

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Zebra pattern in rocks as a function of grain growth affected by second-phase particles

2015

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Alternating fine grained dark and coarse grained light layers in rocks are often termed zebra patterns and are found worldwide. The crystals in the different bands have an almost identical chemical composition, however second-phase particles (e.g., fluid filled pores or a second mineral phase) are concentrated in the dark layers. Even though this pattern is very common and has been studied widely, the initial stage of the pattern formation remains controversial. In this communication we present a simple microdynamic model which can explain the beginning of the zebra pattern formation. The two dimensional model consists of two main processes, mineral replacement along a reaction front, and grain boundary migration affected by impurities. In the numerical model we assume that an initial distribution of second-phase particles is present due to sedimentary layering. The reaction front percolates the model and redistributes second-phase particles by shifting them until the front is saturated and drops the particles again. This produces and enhances initial layering. Grain growth is hindered in layers with high second-phase particle concentrations whereas layers with low concentrations coarsen. Due to the grain growth activity in layers with low second-phase particle concentrations these impurities are collected at grain boundaries and the crystals become very clean. Therefore, the white layers in the pattern contain large grains with low concentration of second-phase particles, whereas the dark layers contain small grains with a large second-phase particle concentration. The presence of the zebra pattern is characteristic for regions containing Pb-Zn mineralization. Therefore, the origin of the structure is presumably related to the mineralization process and might be used as a marker for ore exploration. A complete understanding of the formation of this pattern will contribute to a more accurate understanding of hydrothermal systems that build up economic mineralization.

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Processing and Applications of Intermetallic γ-TiAl-Based Alloys

2000

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REVIEWSDevelopment and processing of high-temperature materials is the key to technological advancements in engineering areas where materials have to meet extreme requirements. Examples for such areas are the aerospace and spacecraft industry or the automotive industry. New structural materials have to be ªstronger, stiffer, hotter, and lighterº to withstand the extremely demanding conditions in the next generation of aircraft engines, space vehicles, and automotive engines. Intermetallic c-TiAl-based alloys show a great potential to fulfill these demands.

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On the Zener drag

Cited by 771 publications

References 9 publications

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

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

Zebra pattern in rocks as a function of grain growth affected by second-phase particles

Processing and Applications of Intermetallic γ-TiAl-Based Alloys

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