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and oxygen atoms, different environments may be formed for oxygen ions in the SDC grain surfaces and the interfaces between two phases.
Thus an additional conduction path may be established in the interfaces or on the surface of the SDC oxide grains.
Moreover, during the oxygen ion migration, the Li+ cations may form transient bonds with the oxygen atoms on the SDC grain surface in facilitating a change of the oxygen ion's environment with a lower potential barrier and a faster mobility.
These negatively charged oxygen adsorbents (especially, the additional oxygen ions) and associated proton attachments on the surface of the ceria grains may essentially consist of an interfacial conduction path.
I-V and I-P characteristics for FCs using various SDC-Li2SO4 electrolytes operated at 610°C, where number 20, 40 etc means the mol% of Li2SO4 in the electrolyte(a) and (b) the electrolyte containing 40 mol% Li2SO4 at various temperatures.

Superplasticity can be induced either in materials possessing a stable, ultra-fine grain size at the temperature of deformation ≥0.4 Tm, where Tm is the absolute melting point or in those subjected to special environmental conditions [11].
The requirements necessary to achieve superplastic behaviour are: i) fine and equiaxed grain size, usually less than 10 microns. ii) Testing temperature that is greater than approximately half the absolute melting temperature of the subject material. iii) Controlled strain rate [12].
The deformation behavior of fine grained lead–tin eutectic alloy was investigated by Soliman and Al-Seif using compression specimens at initial strain rates in the range 10-5 to 10-1 s-1 [15].
They found an increase in ductility with the number of holes up to 10 holes and a decrease thereafter [16].
The extrusion process was carried at 25 oC which corresponds to a homogeneous temperature of 0.65 i.e. hot extrusion, using five extrusion dies of different openings to produce hollow cylindrical specimens of bore to outer diameter, (Db/Dout), of 0.1, 0.2, 0.3, 0.4 and 0.5 extrusion ratios of 6.6, 6.4, 6.0, 5.6 and 5, Figs. 1 and 2 at cross head speed = 5mm/min, and were kept in a freezer to avoid grain growth.

The deformation of crystal grain in this deformation zone is different because of the different workpiece material, cutting tool geometry parameter and cutting parameters.
Near the area of the beginning of plastic deformation, the workpiece material is compressed and grain is changed from the approximate round to oval.
As shown in Fig. 5 (v=1500m/min; vf=800m/min; ae=8mm; ap=1mm), the direction of the grain elongation and shear plane is different.
Fig.5 Oval Grain in the Deformation Zone Fig.6 Slip Line of Bottom Chip Deformation Zone II -the Friction Zone on Rake Face.
As the tool enter the shear plane, the compressive stress field is rotated, the dislocation density is increased, a large number of sliding surface are produced and many dislocation cross and reticular structure of dislocation are formed.

High micro-hardness and high tensile strength can be obtained with high burnishing speeds, due to directional deformation of grains and the orientations of residual stresses.
The resulting product was crushed in an Abbich mortar to powder with a grain size of 0.5 mm and next milled for 20 hours in a rotary-vibratory mill with WC grinding media in anhydrous isopropyl alcohol to a finer powder.
The grain size distribution and average size of particles were measured using a Shimadzu (type SA-CP3) apparatus.
These composites contained diamond grains and 10wt% Ti3(Si,Ge)C2 or 30wt%Ti3SiC2 bonding phases.
Burnishing tool working part Number of measure-ment SGS parameters after turning SGS parameters after burnishing KRa Ra’ μm Rz’ μm Rp’ μm Rt’ μm c’ , % Rt’ for Rmr’(c)=50% Ra μm Rz μm Rp μm Rt μm c, % Rt for Rmr(c)=50% D Ti3(Si.Ge)C2 1 0.8 4.33 2.42 4.7 2.3 0.3 3.33 2.28 3.92 2.2 2.67 2 0.77 4.33 2.7 4.9 2.7 0.42 3.81 2.1 4.28 2.1 1.83 3 0.76 3.44 1.64 4.22 1.6 0.22 1.78 0.72 1.9 0.7 3.45 D Ti3SiC2 1 0.83 4.56 2.68 4.88 2.93 0.21 1.43 0.72 1.72 0.7 3.95 2 0.83 4.67 2.81 5.51 3.1 0.19 1.32 0.69 1.59 0.66 4.37 3 0.84 4.62 2.87 5.17 3.19 0.21 1.44 0.76 1.81 0.75 4.00 a) b) Fig. 4.

Because a large majority of slope failures are triggered by intense rainfall [5,6,7], a number of researchers [8,9,10] have attempted to establish rainfall-intensity thresholds so that predictions about future slope failures can be made.
The properties determined for the colluvial soils and bedrock included natural water content, grain-size distribution, Atterberg limits, specific gravity, void ratio, degree of saturation, natural and saturated densities, coefficient of consolidation and permeability.
On the basis of grain-size distribution, the soils from the five samples were classified as well-graded sands (SW).
A plot of Atterberg limits (Table 1) on Casagrande plasticity chart (Fig. 3) shows that the fine-grained portion of colluvial and eluvial soils can be classified as silts and clays of low plasticity (ML and CL).
A comparison of Atterberg limits with natural water content, expressed as liquidity index, indicates the behavior of fine-grained soils upon shearing.

The double-layered sheet is composed of a thin plastic sheet and a flexible diamond wheel sheet, on which approximately 6 Ǵm diamond grains are electro-plated.
The diamond sheet, on which approximately 6 Ǵm diamond grains are embedded, finely grinds the rugged surface through deformation of the soft pad in the wake of surface contour, as shown in Fig.4 (bottom).
The lower areas of the grooves of width 200Ǵm and depth 1.0um show very few traces; in the upper areas, a large number of fine abrasive traces are apparent.
On the other hand, it is very difficult to form chip resulting in material removal for soft copper metal for a micro grain depth of cut (under 0.5 㨪 1.0Ǵ m) following in the wake of surface waviness.
For micro grain depth of cut, that is under 0.5 to 1.0Ǵm, it was very difficult to form chips that result in material removal for soft copper metal that lies in the wake of a surface waviness.

As the volume of pores is smaller than the volume of cement grain, very soft materials are needed as a filling – microsilica or nanosilica.
Generally, UHPC is a fine-grained concrete mixture with a high amount of cement, microsilica and steel fibers, which has a high density without capillary pores.
For UHPC production for this experiment, the option of a fine-grained mixture with a maximum gravel grain of 2 mm was selected.
Formula 3 sees the number of binding elements reach 963 kg/m3, while the water amount is 243 kg/m3 and the amount of superplastic additive reaches 0.32% of the cement.

These images reveal a lamellar microstructure, characterized by fine plates of martensite grains on the surface (zone A), where the impact of the carburized layer is evident.
Moving away from the surface, the size of martensite plates / grains gradually increases (zone B).
Consequently, at the center of the sample (zone C), where the carburizing treatment has no influence, a coarse microstructure is observed, featuring larger plates of martensite grains.
This analysis will employ high-resolution equipment to reveal the grain refinement effects induced by SMT-SP processing and to determine the thickness of this layer.
Acknowledgments This work was supported by a grant of the Ministry of Research, Innovation and Digitization, CCCDI - UEFISCDI, project number PN-III-P2-2.1-PTE-2021-0195, contract no. 94PTE / 2022, within PNCDI III.

In the last decades, there are some reports on the effect of RMF on the microstructure via experiments and numerical simulations.[8-12] The effect of RMF is mainly reflected in three factors: grain refinement[13,14], modified macrosegregation [15,16] and the transition of structure morphology[17-19].
Normally, the grain size is in reverse proportion with the outside particle density.
As a result, the RMF can increase the nucleation rate, refine the grains and increase the number of grain.

Subsequently, automatic polishing steps were applied first with a 3 μm grain size diamond suspension for 40 minutes, followed by polishing with a 1 μm grain size diamond suspension for 30 minutes, and finally polishing with a 0.05 μm grain size γ-Al2O3 suspension for 20 minutes with 15 N force for all the polishing steps respectively.
It has polygonal grains, but near to the spheres the number of silicon rich and magnesium rich (in case of AlSi12 and AlMg1 matrix respectively) precipitations had increased.