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The microstructure was characterized by equiaxed grains of about 40 μm with a large number of ∑3 annealing twins.
The microstructure was characterized by elongated grains with profuse lamellar features.
In order to characterize the nucleation rate during recrystallization the number of recrystallized grains per unit volume was estimated in specimens after different annealing times.
At both the lowest (560°C) and the highest (670°C) annealing temperature the number of recrystallized grains per unit volume reached the maximum values after very short annealing times and remained virtually the same on further annealing, i.e. nucleation was site saturated.
The nucleation of new grains was site saturated.

Using random number select transition particles and their transfer direction and compared with transfer time and particles falling transition interval time.
The main influence of the deposition rates is the number of transition.
Along with the increase of Si content, Si hinder grain growth trend is more obvious, especially when the content of 8%, the size of grain was a substantial decrease.
Si mainly is in the hole or the interstitial position of crystal lattice when the Si content is small; Si presents at the boundary of grain massively when the Si content is large, to barrier TiN crystal grain growing up, and to gather flaws in the around of Si, to increase the crystal grain quantity, so it is advantageous to the crystal grain refinement.
Si will cause grain refinement and the crystal grain arranges anomalous.

The number of inclusions has a direct impact on the content of acicular ferrite.
The number of inclusions will be affected by heat input in the austenite grain, the content of acicular ferrite will changed at the same time through two aspects.
On the other hand, due to the increase of heat input, the high temperature station time of liquid metal increased, which made grain size of the weld metal metallurgical structure increase.Grain coarsening will cause the decrease of the number of grain boundaries, making the grain refining strengthening effect is weakened.
Acicular ferrite grain boundary is large angle boundary, when the cleavage fracture occurs.
But acicular ferrite grain boundaries have precipitated carbide which increase the resistance of crack across the grain boundaries, crack extension requires more energy[5].

In other words, elongated grains inclined to the disc plane are formed.
Consider now the grain refinement process during ECAP.
Due to this, the routes BA and BC result in the most rapid formation of an equiaxed structure in terms of the number of passes [18].
This results in a bimodal microstructure with spatially separated fine-grained and coarse-grained components.
The number of cycles, temperature decrement between the cycles, iT∆ , the whole temperature fall between the first and last cycles, ∆Т, and number of passes in each cycle are the key parameters of the process and depend on the material and its initial microstructure.

Study on Wet Picking/Wet Repellence at the Grain Direction of Offset Paper Yonggang Yang Beijing Institute of Graphic Communication, Beijing, China yangyonggang11@yeah.net Keywords: wet picking; wet repellence; felt side; grain direction; offset paper Abstract: The wet picking and wet repellence of offset papers were studied using IGT-gst2 printability tester according to change printing conditions as printing speed and the amount of fountain solutions.
The wet picking and wet repellence measurements were respectively carried out on the felt side and at the machine (grain) direction of the 3 paper samples.
In addition, wet repellence along the paper fibers (grain direction) was lower than that in cross section on the felt side of the offset paper because the direction of grains was that of the majority fibers aligning together tightly [10].
If wet picking occurred, the strength confinement of a single fiber must be overcome and the strength of a single fiber was usually greater than the strength of the bonding force between the fibers, so that wet repellence along the paper fibers (grain direction) was lower than that in cross section on the felt side of the offset paper.
Acknowledgements This work was financed by the Beijing excellent talent fostering foundation (Grant number: 2010D005004000004) and the general program of science and technology development project of Beijing municipal education commission (Grant number: KM201110015002).

In particular, we focus on the effect of misorientation at grain boundary or phase interface on the kink evolution.
The specimen is constituted by two α-Mg phases (grains 1, 3) and LPSO phase (grain 2) and the displacement in the z-direction is constrained to prevent the structural buckling.
The specimen dimensions are in height, in width, in thickness and the following initial shape imperfection in the x-direction is introduced: , (8) where the superscript denotes the node number, both and the imperfection amplitudes and is the wave number.
We let the values of amplitude be 0.01 and 0.005 and the wave number be .
A large number of non-basal slip, in particular the pyramidal ones, in α-Mg phases is observed near the grain boundaries and kink bands.

Severe plastic deformation by continuous ECAE process affect the microstructure in some extent depending on the number of passes as shown in Fig. 2(b)-(e).
This microstructure also has the sub-grains separated to each other by low-angle grain boundaries (LAGBs) as indicated by double arrows in Fig.
As the number of passes increased, the dislocation density increased and smaller sub-grains form with mostly LAGBs.
After processing, the strength of steel increased continuously with an increase in the number of passes.
However, with increasing number of passes, the texture component from 4th pass onwards remains same i.e. {110}q components.

The correct detection of these phases requires the high magnifications and a large number of measurements fields.
Therefore, it is important to reduce the amount of Mg17Al12 phase and introduce thermally stable precipitates at grain boundaries as well as in the grain interior by adding proper alloying elements.
In addition, globular particles inside the α-Mg grains are visible.
Needle-shaped precipitates inside the α-Mg grains in Mg-5Al-3Ca-0.7Sr-0.2Mn alloy.
Reasonable number of measurement fields was obtained until at measurement error equals SE = 30%.

The refinement and uniformity of grains must be on the basis of reducing the “grain inheritance” and making use of complete austenitizing process [6].
It also reduces the number of residual austenite, and reduces or avoids grain inheritance.
Two times normalizing Two times normalization is to eliminate the nonuniform microstructure and mixed grains, and to refine grains.
Meanwhile, recrystallization generates new grain boundaries, and the harmful elements deposited on grain boundaries may be rearranged to reduce the segregation on grain boundaries.
Pre-treatment increases nucleating of austenite in recrystalization and decreases the number of residual austenite, which refines grains primarily and reduces grain inheritance.

Y2O3 could act as an inhibitor to the growth of ZnO grains when working with Sb2O3.
With the increase of Y:Sb ratio, a new phase of Y-Sb-O would be formed, which is a more effective inhibitor to the growth of ZnO grains, so the mean size of ZnO grains further decreased.
And the calculated mean sizes of ZnO grains in the corresponding samples (h).
However, without doping of Sb2O3, due to the abnormal growth of ZnO grains and the segregation of the doped Y2O3 at the grain boundaries, the densification of the samples was inhibited and the number of pores increased quickly.
However, without Sb2O3, the densification of samples decreased, the number of pore in them increased, and lots of the doped Y2O3 would segregate at the grain boundaries, resulting in increased carrier concentration there.