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For production of larger numbers of deposits using sequential deposition in multiple forming chambers from the same batch of suspension a suspension tank is required with sufficient volume to achieve the required number of deposits.
The final volume will be dependent on a number of factors including the deposit thickness, the target deposition times and the optimum number of deposits from a suspension batch.
The duplex micro-structure of enlarged secondary grains (up to 150 micron) within a fine grained matrix can lead to fracture initiating flaws, particularly where interlinking of large grains increases the effective flaw size considerably.
For this reason it is often preferred to incorporate between 5-10% of ZrO2 as a discreet 2 nd phase at the grain boundaries within the beta"-alumina which acts to suppress the secondary grain growth, limiting the largest grains to around 20 microns [6,9].
Interest in SOFCs capable of reduced temperature operation has led to a number of innovations in the field.

The deposition film possesses similar smooth surface and homogenous grain size.
The composite target included a high-purity (99.999%) aluminum disk with a diameter of 80mm and a number of Gd powders placed symmetrically on the surface of the Al disk.
Gd contents were controlled by varying the number of Gd powders and the atomic concentrations of Gd were from x = 0.05 to 0.02, corresponding to the number of Gd powders.
The grain size gets inhomogeneous.
The deposited film sample possesses similar smooth surface and homogeneous grain size.

This is understandable as the γ fiber grains have higher stored energy; while the α fiber grains have lower stored energy [15].
The orientations of many small and undistorted grains can be obtained by EBSD, as shown in Fig. 5 (a) and (b), and these small grains are newly recrystallized ones.
The size of these small grains ranges from 1µm to 5µm.
When the annealing time lasts to 10s, the number of small, equiaxed and undistorted grains evidently increases.
Among the recrystallization nuclei, those belonging to the γ fiber {111}, such as {111}<110>, {111}<112> ones, take large number.

Further, the grain size of the magnesium matrix has been reduced by the presence of AlN particles.
The mean grain size was measured using the linear intercept method.
The CLEMEX Micro Hardness Tester was used to determine the micro hardness (Vickers Hardness Number, VHN) at test load of 200g and dwell time of 13s.
The grain size of the composite is found to be 65mm which is compared with the grain size of AZ91 (100 mm) alloy [Fig. 5(a)].
It is seen that there is significant reduction of grain size in the composite which is due to the grain refining efficiency of AlN.

These analyses were performed in the initial just quenched state (AQ) and also after a number (C) of compression cycles.
This was inferred by the fact that precipitates observed at the β grain boundaries are richer in Ti as compared to the interior of grains, which is a characteristic of the stable α phase.
Table 1: Mo content of the grain boundary precipitates and grain interior in the Ti – Mo alloys.
Alloy Composition Mo [wt%] β Precipitates at grain boundaries Interior of β grain Ti-6%Mo 3.38 9.70 Ti-8%Mo 7.28 8.30 Ti-10%Mo 1.68 9.67 Ti-15%Mo 2.73 13.62 Figure 3 shows the elastic modulus (E) and the residual deformation (εres.) for the Ti – Mo alloys as a function of the number of compression cycles.
Fig. 3: Variation of the elastic modulus, E, (a) and the residual strain, εres (b) with the number of compression cycles for the Ti – Mo alloys.

The minimum specimen number is determined according to the sampling method, test type and intended precision degree.
Tensile experimental tests: a) parallel to the grain direction; b) perpendicular to the grain direction.
Compression experimental tests: a) parallel to the grain direction; b) perpendicular to the grain direction Fig. 4.
Shear experimental tests: a) parallel to the grain direction; b) perpendicular to the grain direction.
The number of tested specimens must be determined according to Standard ISO 3129: “Wood.

It is interesting to note that the number and area of pores of samples A3, A4 were lower than those of samples A1, A2.
CaSiO3 grains growth may cause more pores in the doping sample that leads to the different effects on the dielectric loss.
Therefore, the images of Au, Pt, Pd elements for high atomic number were white, while the images of Ca, B, Si, and O for low atomic number elements were gray.
Through XRD analyses, the pure CaO-B2O3-SiO2 system contained a large number of CaSiO3 with a small amount of crystal phase CaB2O4.When added a amount of CBS glass to the LDK glass, there was no obviously change in the crystal phase composition, but CaSiO3 Fig.4 Dielectric properties of sample A0-A4 grains became larger and more with SEM observations and quantitative analyses.
The effect on the dielectric properties, grains grown of CaSiO3 played a more dominating role than that of porosity did.

The crystalline grain was about 13 nm size after only a few hours of milling time.
Their characteristics are fine grain size and high grain boundary density which have been found to be determinant for their physico-chemical properties [3,4].
Continuous milling acts mostly on the structure of grain boundaries than on the size of the crystallites.
The first phase is the stage of plastic deformation (multiplication of the number of dislocations).
The pursuit of mechanical milling is not so effective in concern of the diameter of particles and the grain size, but acts rather on the grains boundaries.

Al based materials prepared by powder metallurgy (PM) process offer a number of interesting opportunities for high strength applications.
Variation in grain size and lattice strain as function of milling time.
The variation of grain size and lattice strain as a function of milling time is shown in Fig. 6.
Grain size after 24 hours milling was found to be~30nm.
Verlinden, Precipitation hardening and grain refinement in an Al-4.2 wt.% Mg-1.2 wt.% Cu processed by ECAP, Mater.

Then, the location (x, y) of an abrasive grain within the contact arc at time t can be expressed as (x=Vgt, y=Asin(2πft)).
(2) If the distribution density of the abrasive grain on the grinding wheel periphery is M, the number, N, of the acting abrasive grain per unit time would be N=MbVg.
But since the number, Ng, of simultaneously acting abrasive grains is Ng=Mbl, the total grinding force under ultrasonication, Fwith, can be expressed as: ∫ + ∆ =⋅= l g g g fs gg with dxx V f V Af V blVk NFF 0 2 ) 2 cos 2 (1 pp (5) The total grinding force in the absence of ultrasonication, Fwithout, can be derived by setting the vibration amplitude A in Eq.5 equal to zero: gfs without VbVkF ∆=
A vitrified bond CBN (cubic boron nitride) grinding wheel 5 mm in diameter and a grain mesh size of #400 was employed.
This indicates that chips with smaller cross sectional areas were fractured more easily by the impact of the ultrasonicated abrasive grain.