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Its major fault mode is grain abrasion caused by dry sliding friction.
Collision force is the most difficult kind to investigate because the force numerical value is directly related with the collision parameters, but the collision parameters can only be confirmed by a number of experiments.

The mutual collision between balls and alloy powders, the cold weld between alloy powders, and the mutual diffusive between atoms occurred during high-energy milling process, thereby increasing crystal defects and grain boundaries [11,12].
The MgNi and MgNi+5%B alloy powders consist of irregular particles, with a grain size less than 5μm in diameter, and the MgNi+5%B alloy powders had slightly more uniform diameter than that of MgNi alloy powders.
%B alloys as a function of cycle number Table 4.
The maximum discharge capacity Cmax and cycle capacity retention rate Sn of the MgNi+x%B alloys Samples(x) Cmax(mAh/g) S20(%) HRD400(%) HRD800(%) Io(mA/g) MgNi 320.5 17.9 43.2 27.9 60.5 MgNi+2%B 337.1 17.8 53.4 30.5 158.3 MgNi+5%B 358.6 24.5 58.3 32.2 293.5 MgNi+10%B 347.7 29.4 48.6 28.5 112.6 Fig. 6 shows the discharge capacity of the MgNi+x%B(x=0,2,5,10) alloys with cycle numbers.

It is known that the amount of stored elastic energy in deformed polycrystals is dependent upon the grain orientation, and subsequently the release of this energy and evolution of the microstructure and texture during annealing is very much dependent on the starting texture and microstructure [1].
The models are highly dependent on assumptions made about the initial dislocation network and contributions from both the dispersed dislocations and those in the growing cell wall/sub-grain structure.
A tensile increase can result from dislocations being pulled into the denser regions (walls) clearing the interior region for a lattice expansion, while the subsequent increase in the compressive component may be due to the thinning of the cell and increasing the number of dislocations within the interior cell.
After recrystallization (>300°C) there is a distinct increase in the lattice strain due to both the annihilation of a large number of dislocations and the likely dissolution of Mg and other particles into solid solution causing the lattice to dilate.

Two phases of Stainless Steel Two phases of stainless steel is stainless steel which has a mixture of structures from ferrite bcc and austenite fcc besides that designed a number of content austenite phase is the same.
Its growth begins at the ferrite grain boundaries and then grows into the ferrite grain according to the crystallographic directions.
Method of TIG welding using shielding gas mixed with nitrogen can produce a relatively equal number of phases between ferrite - austenite at welding with 95 % argon + 5 % nitrogen in the welding speed 3 and 4 mm/sec.

Cavitation has also found application in a number of commercial products to clean or breakdown materials because of producing extremely high energy densities [3].
Such a device has also been used by a number of other scientists [10, 11].
Laser beam processing and subsequent rapid cooling of materials subjected on the cavitation erosion leads as a rule to grains refining and, due to diffusion retarding, creates the state of residual stresses within the processed material.
Refining of the grains and a decrease in micro cracks length causes the material to erode away in smaller pieces and at a lower rate.

This complex phenomenon possesses a great number of challenges for theoretical analysis.
In the equiaxed zone the crystal grains are freely moving in the melt.
At the macroscopic scale, liquid flow in the columnar mushy zone can be modelled by treating this region as a porous medium [1], while in the equiaxed mushy zone some models of grain suspension are applied.
However, a rather limited number of attempts were undertaken to measure this property and to associate it to the current morphology of the columnar mushy zone, i.e. to spacings of the primary and the secondary dendrite arms.

On the other hand, when the quenched specimen underwent subsequently the temper treatment shown in Table 2, sulfide would be formed or S would segregate in the grain boundary, because the solubility limit of S was estimated to be null at 873K [11,12].
But a small number of a Cr sulfide phase was also observed as submicron particles in the S-doped steel tempered at 873K for 18ks.
∑=i xMw ii ox , (2) where Mi (kg/mol) is the molecular mass of each oxide and xi (mol) is the number of each oxide moles, and both Mi and xi were estimated by using the experimental data obtained from EDS analysis and the cross-section observations.
It was also found that the steam oxidation resistance was improved when S made a sulfide or segregated in the grain boundaries, but never improved when S existed in a solid solution.

Varying quantities of material ranging from small to large can be processed, and the resulting powders usually display nanometer-sized grains.
McKamey of Oak Ridge National Lab., was mixed with 5 wt% and 10 wt% Si (<45µm grain size, 99.5% purity), giving the atomic compositions Fe64Al26Cr1Si8, and Fe59Al24Cr1Si16, respectively.
v (mm/s) 0 10 20 30 p(Bhf) Bhf (T) Journal of Metastable and Nanocrystalline Materials eVolume 12 33 A high number of iron atoms in antisite position (replacing aluminium atoms) and vacancies (mostly of iron) are present in the material.
After thermal annealing the Mössbauer spectrum of the Fe64Al26Cr1Si8 sample displays a sharper magnetic distribution shifted to higher values of hyperfine magnetic field, indicating a reduction in the number of configurations for the Fe atoms in the bcc structure.

The key point in flow forming is the suitable combination of a large number of parameters during the process which can significantly influence the properties of the final part.
Finally, the starting microstructure and hardness of the preform are also significant since the grain structure and the phases present can affect the deformation mechanism by modifying the activated slip systems or cause slip localisation.
In order to avoid effects from possible heterogeneities in the grain structure, pole figures were measured on five locations on each sample and the average ODF was calculated with MTEX.
Other researchers have also pointed out this variation in strength through the material’s thickness [12], but in some cases it could be less straightforward depending on the exact thickness reduction and number of passes [13].

Material Description Cement N Ordinary Portland cement Density: 3.16g/cm3 H High-early-strength Portland cement Density: 3.14g/cm3 Fine Aggregate S River sand from Kanagawa Density: 2.69 g/cm3 Water absorptivity: 1.49% Binder BB Blast-furnace slag fines type B (4000 grain) Density: 2.92 g/cm3 Superplasticizers (Ad) PCa High-range water-reducing agent RMC High-range water-reducing agent, AE type Figure 1.
By applying thermal stimulation at the construction site, it will be possible to construct high-performance concrete with a low water–cement ratio even at construction sites with a small number of workers.
Both high-early-strength Portland cement (H) and blast-furnace slag cement type B (BB) were used to simulate ordinary Portland cement with 45% replacement by blast-furnace slag fines (4000 grain).
Acknowledgment This research was supported by the Japan Society for the Promotion of Science, KAKENHI Grant Number JP20J23758, 2020-2022.