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Because of a wider range of grain sizes than those reported from previous earthquakes, gravels characteristics liquefied in the Wenchuan earthquake are representative and universal.
Earthquake & location Ground motion strength Features of liquefied gravelly soils 1 1975 Haicheng Earthquake; Shimen dam, Liaoning, China Seismic intensity Ⅶ Loose; un-compacted fill in upstream shell of dam 2 1976 Tangshan Earthquake, Miyun dam, Beijing, China (PGA=0.05g，140 second) Loose to medium dense; un-compacted fill in upstream shell of dam 3 1976 Tangshan Earthquake, Luan county urban, China Seismic intensity Ⅹ Ejected gravel particles (mostly 3-9 cm with 15 cm maximum); 4 1964 Alaska Earthquake -- Alluvial fan; loose 5 1983 Borah Peak Earthquake; Pence Ranch area, USA PGA=0.3-0.5g Alluvial fan; The slope is 5 degree; loose 6 1976 north-eastern Italy Earthquake; Priuli, Italy PGA=0.2g Alluvial fan; shear wave velocity is 140-210m/s 7 1993 Hakkaido-Nansei-Oki Earthquake; Mt.Komagataka, Japan -- Relative density is 30%; Mean grain size is 3 cm; the shear wave velocity is less than 100m/s 8 1995 Kobe Earthquake; Port island, Japan PGA=0.25-0.4g 12-15m of uncompacted fill overlain
The BPT whose resistance is defined as the number of blows required to drive the casing through an increment of 30 cm was developed in Canada in the late 1950s [6] .
●Because of the wider range of grain sizes of liquefied gravel soil, the gravels liquefaction evaluation method developed from the Wenchuan earthquake should be feasible for worldwide use.

In various grinding methods, it is known that the cutting operation is mainly performed by grains located on the front of the working surface of the wheel.
At each repeated meeting of the cut with the wheel working surface, part of the active grains falls into already cut grooves, which leads to uneven immersion along the height of the circle, an increase in the operation of external friction of the grains and connection with the metal surface, and an increase in the temperature effect on the treated surface.
The number of strips is determined by the ratio of the height of the circle to the feed.
To minimize the graph scheme of the algorithm, the informativity of the parameters is determined ρxk; T(X,V)=mk+ρk-qk (3) where m_k- the number of columns of the parameter X_k∈X the normalized match table; ρ_k-summarnoye number of solutions determined by all pairwise nonequivalent values of X_k parameters; q_k- a parameter that takes zero or one values, depending on whether or not undefined X_k values exist.
were, mk- the number of columns of the parameter Хk∈Х the normalized match table; ρk- summarnoye number of solutions determined by all pairwise nonequivalent values Хk; qk- a parameter that takes zero or one values, depending on whether or not undefined Хk values exist Rxkik; T(X,V=V; The match table recorded in the input language for input to the computer is represented by the following sequence[5]: p=1zTApx11Ux12Ux13…Ux1k=x21Ux22Ux23…U2k =x31Ux32Ux33…Ux3j=……………………….xm1Uxm2Uxm3…Uxmn= (4) Here x11,x1n; x21,x22,; x2k; xm1; xm2; xm1 arguments that meet the applicability criteria x1,x2, xm, Z- number of solutions corresponding to v1,v2,… vn.

In cladding steel plate, cladding interface vanished and was replaced new recrystallized grains, and no interface defects or inclusions were detected.
In head and tail of sample, no cladding interface and defect was detected and cladding interface was replaced by recrystallized grains, indicating a sound heavy gauge plate can be achieved by vacuum cladding rolling under investigated parameters.
(2) With decreasing vacuum level, interface inclusions containing a number of silicon and aluminum elements increased

The oxygen concentration is superior in the grain boundary region (Nd-rich) compared to that verified in the hard magnetic phase.
In 2010, such compound consumed 21% of the RE elements and it is estimated that, in 2015, such number might achieve 26% [1].
Conclusions Based on the results presented in this work it is possible to conclude: - the remanent magnetic moment per unit mass and Hc decrease due to the presence of oxygen in the hard magnetic phase as well as to the possible presence of a soft magnetic phase; - the magnetic moment per unit mass at µ0H = 2 T increases after 16 hours due to the possible presence of a soft magnetic phase in the microstructure of the HDDR powders prepared from NdFeB-based sintered magnets; - the oxygen concentration is superior in the grain boundary phase compared to the value found at the matrix RE2Fe14B-based phase; and - a protective coating must be applied on the particles surface in order to avoid the deleterious effect of oxygen on the magnetic properties.

of undegraded limits; Nd - Number of degraded limits
From the design, a number of operating cycles were provided, Nc = 3295 cycles, which implies a number of operating hours, Nt = 144882 hours.
From the aspect of degradation, it is not possible to deduce the direction of the maximum main stresses force Re-inspection for a maximum of 30000 hours 3 Focused Cavities were observed, often multiple cavities on the same grain boundary.
Constituents Imperfection At 35mm below the B1 welding bead 1 Ferrite, perlite, with bainitic grains and carbides Not noticeable PM 1 ... 8 Ferrite, perlite, with bainitic grains and carbides Not noticeable PM 2 At 35mm below the B2 welding bead 1 Ferrite, perlite and carbides Not noticeable PM 3 ... 8 Ferrite, perlite and carbides Not noticeable PM 35,36 At 50mm above the B3 welding bead 1 Ferrite, perlite and carbides Not noticeable PM 5 ... 8 Ferrite, perlite, with bainitic grains and carbides Not noticeable PM 6 Table 6 shows the results obtained from the quantitative examination of the metallographic replicas taken from the basic material of the coke chamber mantle 180 - R1D, replicas deposited and extracted.
Table 6 - Experimental results Measuring line number Length of measuring line L[mm] Number of degraded limits Nd Number of undegraded limits Nu Total number of limits N=Nu+Nd At 35mm below the welding bead At 50mm below the welding bead At 35mm below the welding bead At 50mm below the welding bead At 35mm below the welding bead At 50mm below the welding bead At 35mm below the welding bead At 50mm below the welding bead B1.1 B2.1 B3.1 B1.1 B2.1 B3.1 B1.1 B2.1 B3.1 B1.1 B2.1 B3.1 1 0,177 0,177 0,177 1 1 2 5 6 5 6 7 7 2 2 2 1 6 4 5 8 6 6 ... 10 1 1 2 5 5 6 6 6 8 B1.2 B2.2 B3.2 B1.2 B2.2 B3.2 B1.2 B2.2 B3.2 B1.2 B2.2 B3.2 1 0,177 0,177 0,177 2 2 2 7 6 5 9 8 7 2 2 2 2 6 7 6 8 9 7 ... 10 2 2 1 6 5 3 8 7 4 B1.3 B2.3 B3.3 B1.3 B2.3 B3.3 B1.3 B2.3 B3.3 B1.3 B2.3 B3.3 1 0,177 0,177 0,177 2 2 2 7 4 6 9 6 8 2 3 3 3 5 6 7 8 9 10 ... 10 2 2 2 5 6 6 7 8 8 B1.4 B2.4 B3.4 B1.4 B2.4 B3.4 B1.4 B2.4 B3.4 B1.4 B2.4 B3.4 1 0,177 0,177 0,177 3 2 1 8 7 8 11 9 9 2 3 3 2 6 7 7

However, in the intermediate nearby the ceramic α-Al2O3 inclusions presented the highest diffraction peak in XRD pattern in contrast with ones of TiB2 and TiC phases, which indicated there were a large number of α-Al2O3 inclusions in the intermediate nearby the ceramic, as shown in Fig. 2(b).
And, the EDS results of the intermediate were shown in Fig. 3 (b) and Table 1, which not only promised there were both diffusion of C and Ti atoms from the liquid TiC-TiB2 ceramic to stainless steel during combustion synthesis in high-gravity field, but also demonstrated a large number of Fe atoms dissolved into Ti-enriched carbides in the intermediate.
Meanwhile, compared to the one of the ceramic far away from the joint, the microstructure of the ceramic nearby the joint was obviously refined so that the ultrafine-grained microstructure (i.e. micro-nanocrystalline microstructure) of the ceramic was achieved, respectively, as shown in Fig. 6(b) and Fig. 6(c).
As a result, at initial stage of solidification the nucleation rate of TiB2 solid as the primary phase inceases greatly due to the incease of Ti mole concentration in liquid TiC-TiB2 nearby the molten Ti alloy, resulting in the achievement of the ultralfine-grained microstructure in the ceramic nearby the joint, as shown in Fig. 6(c).
Because of high diffusion rate of C relative to B in molten Ti alloy and the isotropy of TiC in crystallography, a number of coarse Ti-enriched TiC particles are formed the joint area due to rapid growth of TiC crystals, while some fine Ti-enriched TiC particles are also found at the area nearby unmolten Ti solid alloy.

The optical microscopic metallography observation shows the rosettes of uniform spheroidal grains of strain free eutectic silicon phase in proeutectic Aluminium matrix after heat treatment.
It revealed the coarse strained grains of Al metal matrix.
Whereas the microscopic image of after heat treatment condition showed the evidence of grain morphological changes of A356 alloy that depicted the transformation of hard acicular eutectic silicon flakes to strain free uniform globular structure and grains of proeutectic Aluminium that had got refined [7, 11].
The Brinell hardness number (BHN) was calculated for without heat treated and with heat treated A356and its composite with SiCp reinforced and heat treated.
This strain free evenly distributed globular grains contributes to the strength of the metal

Doping with Zr first increases the grain size to a average value of 4.5 µm, with increasing doping level the grain size gets reduced to about 2 µm.
Doping with Sn does not change the grain size significantly, a slight decrease is observed at higher concentrations.
Only for Zr-doping an increase of grain size was observed for x ≤ 0.02.
A higher doping level leads to a reduced grain size.
Both Sn and Ge lead to a continuous reduction of grain size.

During liquid phase sintering, the rim phase (Ti, Mo, W)(C, N) precipitates on Ti(C, N) grains due to the dissolution of small grains and re-precipitation on large ones.
With addition of nano TiC and TiN content, the number of grains acting as crystal nucleus increases during sintering.
Consequently grain sizes become fine and small ceramic grains with "white core-black rim" are increased.
The microstructure of Cermet DNM changes under a depth of 30µm from surface as shown in Fig.1b: the grains in near surface become small, while inner rims in carbonitride grains vanish.
In our previous research [9,12], it is proved that white grains with rich W and Mo are formed during the post-treated processing due to the dissolution of the ceramic grains and the diffusion of alloy elements.

Table 2 Vertical mill slag powders' RRB distribution fitting parameters Sample number RRSB fitting parameters n R2 De nDe L1 1.34885 0.98454 14.1 19.0 Fig.2.
Since the height of angularity and the number of angularity have significant impact on the circumference of the ellipse, so the experiment defined angularity focus on the number of particle surfaces and the prominence of the parameters.
In the above formulas, represents the particle's area (not including holes), represents the grain boundary perimeter, represents the particles' smallest bounding polygon perimeter, represents the perimeter of criteria oval which has the same size and flat degree with the particle, and is the particles' maximum Fred diameter and minimum Fred diameter, is the diameter of the circle which has the same area with the particles.
Table 4 Vertical mill slag powders' morphology quantification results Quantization parameters e Sample number 2.224053 0.617327 1.671782 1.684370 1.673726 5.
An exact method for characterization of grain shape [J].