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Despite a number of investigations of Al–Mg-, Al–Mn-, Al–Mg–Si- as well as Al–Sc–Zr-based alloys there are considerably less systematized data about the Al–Mg–Si–Cr–Mn–Sc–Zr alloys in the literature.
Contributions of dislocations, textures, grain boundaries etc. are two orders of magnitude lower [1, 2, 5, 6].
The average grain size of the AC alloy was observed ~ 350 μm (see Fig. 2).
One can also suggest that the II-stage (Fig. 3b) is divided into two parts due to a formation of Mn-containing particles at (sub)grain boundaries and a formation of these particles in (sub)grain interiors.
Microstructure of the CR alloy isochronally annealed up to 450 °C, see Mn-containing particles at (sub)grain boundaries.

Current study found that the rate of particle removal significantly depends on the flow Reynolds number and the cavity shape.
Introduction Flows including solid particles are spotted in various engineering applications and plays an important role in industrial manufacturing process, waste water treatment, seeds drying technology, separation of grains and etc.
Another cavity shape which is the triangular is also considered and the maximum inlet velocity varies to obtain Reynolds number as 50, 100 and 400.
In higher Reynolds number, the vortex has the tendency to move to the right side and the circulating area of vortex is bigger.
Fig. 8-9 show the effect of Reynolds numbers.

In Refs. [16,18], authors tested a number of known rate equations and choose “the best one” for their materials studied.
Mean grain size of charged b-phase (hydrogenated Mg2Ni) compound was reduced somewhat during the hydrogen charging due to fragmentation of the largest grains.
Grain interior - Mg2Ni, light rectangular particles – MgNi2, fine eutectic (Mg)/Mg2- Ni at grain boundaries.
Fig. 6 Rows of MgH2 at grain boundaries of charged Mg2Ni casting.
The high temperature peak of the cast material is composed from a number of partials.

The magnetic induction inside the work zone and the magnetic forces acting on grains of the powder, are reduced.
The force acting on a ferromagnetic body (in our case - on a grain of the powder) in a magnetic field is determined by expression [7, 8]:
Having accepted an assumption, that the grain of a powder has the symmetric form (sphere, cube, ellipsoid, etc), the expression (3) can be transformed to a kind: , (4) Figure 6 Results of comparative tests of the magnetic abrasive powders: 1 - chilled cast iron, grain 600 μm; 2 - composite Al2O3М40+80%Fe, grain 100-160 μm where: μ is absolute magnetic permeability of a material of the grain; V - volume of the grain; B - the magnetic induction in a point of space, where the grain is located; gradB - gradient of a magnetic induction in the same point.
It follows from the analysis of the expression (4), that the magnetic force acting on an individual grain of the powder is more, than the more is magnetic permeability of the grain material and then is more its volume.
The grains of the powder contacted to the ledges should be stronger pressed to the magnetic pieces by magnetic forces.

The welded metal was composed of ferrite, grain boundary austenite (GBA), Widmanstatten austenite (WA), intragranular austenite (IGA).
The welded metals both consisted ferrite, grain boundary austenite (GBA), Widmanstatten austenite (WA), intragranular austenite (IGA).
And then WA nucleated at GBA and grew into ferrite grains along certain angles.
Basically at the same time, IGA nucleated in ferrite grains and grew into blocky or slender type.
The grain sizes of hot wire TIG and traditional TIG were almost the same.

The primary carbides form during solidification both intergranularly and intragranularly, and they display a low number density per unit volume and a large size [4].
As summarised by Olson in the context of the computational design of high alloyed stainless steels [8], steel toughening is achieved by controlling various factors: (1) the high temperature "grain refining" particle dispersion, (2) nanovoid formation, and (3) the segregation of embrittling impurities, particularly at the grain boundary.
Similar to semiconductor industry, it has been suggested the addition of dopants to diffuse towards the interface and control grain boundary toughness.
The new genes will be responsible for the nanovoid prevention and/or healing, and the grain boundary embittlement.
Introduction This research was carried out under the project number MC5.04192 in the framework of the Research Program of the Materials innovation institute M2i (www.m2i.nl), the former Netherlands Institute for Metals Research.

These conditions are varied according to a grain size of the diamond.
In the case where grain size of the source diamond was 25µm, voltage measurement on the S-PCD became unstable resulting in a big variation in the measured values.
Regardless of the grain size and type of the source diamond, electrical resistivity of both PCD as a whole was in the order of 10-4Ω·m.
Grain size was 10µm and the initial surface roughness was Rz=0.06µm in both types of PCD.
Test conditions were as follows; size of a SUS ball: f6mm, pressing load: 1N，rotating speed: 60rpm，total number of revolution: 3000，turning radius: R=1.6mm (Table 2).

This filler metal contains zirconium which stabilises the structure, prevents the grain grow and favours the reduction of porosity in welded joints.
All the joints (particularly after heat treatment) revealed precipitates along the grain boundary in the HAZ (probable hardening phases).
The joints after treatment were characterised by very fine grains in the parent metal and fine grains in the weld/HAZ.
However, in the case of the metallographic specimens of the MIG-Pulse welded joints some microcracks along the grain boundaries were detected.
The heat treatment process led to the precipitation of the appropriate number of hardening phases, which was confirmed by the macroscopic examination and the chemical composition analysis.

When the bath temperature increases, large number of Cd and Se ions gets adsorbed on the substrate which leads to crystallization.
It is observed from Fig. 6a that the film surface is found to be less uniform and covered with spherically shaped grains.
It is observed from Fig. 6b that the film surface is observed to be smooth, uniform and well covered with spherically shaped grains.
The average sizes of the grains are found to be in the range between 0.4 and 0.5 µm.
The surface morphology reveals a substantial increase of grain size for films deposited at higher bath temperature.

A number of the welds were fatigue tested with a bending fatigue tester.
In the HAZ, recrystallisation takes place and grain growth continues, depending on the temperature and time.
The recrystallised grain size depends on the number of nucleation places, which in turn depends on cold-rolling reduction.
Fig. 12 shows that the grain structure near the fusion line is evidently finer than that shown in Fig. 14; this is because of the grain refining in the recrystallisation process which is dependent on the cold worked area near the sheared edge.
Fig. 13b shows that the grain structure is quite coarse near the fusion line because of the higher heat input.