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Table 1 Specification of knitted fabric Fabric Number Composition Organization Fabric density Horizontal density [column /5cm] Longitudinal density [row /5cm] 1 Cotton/lycra（95/5） Plain weft-knitted 75 135 2 Cotton Plain weft-knitted 81 98 3 Cotton 1+1Rib 114 88 Table 2 Specification of woven fabric Fabric Number Composition Organization Fabric density Warp density [yarns/10cm] Weft density [yarns/10cm] 1 Cotton Plain weave 493 402 2 Polyester / cotton Plain weave 786 298 3 Cotton Twill weave 345 345 Sample were cut at the place 10cm away from the cloth edge.
Knitted fabric ：lengthwise sample size is 11cm taken along the grain direction, the other direction is 5cm; widthwise sample size is 5cm taken along the grain direction, the other direction is 11cm.
Woven fabrics ：the warp-wise sample size is 5cm taken along the grain direction, the other direction is 11cm. the broadwise sample size is 11cm taken along the grain direction, the other direction is 5cm..

Thus, the number of the formed grains is much more and the sizes of the grains became finer.
With the increasing of the pressure, the microstructure was finer and the number of TiB2 ceramic particles was augmented.
The fine of grains induced the longer path of the deflection and the extending energy of the cracks was consumed more.
The longer path of the crack deflection due to the finer grains and the promotion of the crack-tip plastic blunting by the strengthened metal matrix improved the fracture toughness.

The product of the chemical reaction (ASG) is a fundamental aspect of this reaction, thus the transport of alkali ions in pore solutions of reactive grains showed that alkalis ions move towards the reactive grains precisely the contour of the grains and aggregates, in cement paste / Aggregate borders.
εASG=(VASG -Vpores)/V (3) Likewise the numbers of aggregates Ng reacting are calculated as a volume fraction of the entire volume fraction of the structure.
The molar number of alkali-silica volume gels was calculated.
(c) (d) This results showed that the rheological behavior of concrete component (aggregates, cement paste, silica gel formed, grains, ...) should be further investigated.

These process steps can be repeated several times until the desired number of layers and mechanical properties, respectively, are obtained.
Figure 1: Principle of the ARB process Due to the induced high shear strains, the coarse grains of the initial state are transformed to an ultrafine-grained microstructure with a grain size below one micron and an elongation in rolling direction.
Additionally, very high strains at these peaks forward the development of an ultrafine grain structure [10].
The change concerning the grain size leads to significantly different material properties.
Figure 14: Influence of the number of brushing runs on the surface roughness of AA6016-W As a consequence, for a desired and sufficiently high surface roughness the brushing wheel and the corresponding contact force and feed rate have to be selected according to these experiments.

With the temperature increasing, the number of pores reduced and bulk of pores was smaller.
The grain size was small.
There were a great number of small-size pores.
The grain size was bigger.
With the increasing of the sintering temperature, CA6 grains grew up.

The number of available Mg-based alloys, however, is very limited.
The strengthening of AS series alloys is mainly achieved by fine Mg2Si phase particles formed on grain boundaries.
Generally, the increase of RE-content will produce more Al11RE3 phase at the grain boundaries and reduce the amount of aluminum available for Mg17Al12 phase.
The strengthening of ACM522 alloy is mainly realized by Al-Ce, Mg-Ca, Al-Ca and other intermetallic compounds distributed on grain boundaries.
For example, the number of available Mg-Al based elevated temperature magnesium alloys is very limited, and these alloys developed suffer from inferior diecastability or have disadvantages in terms of marginal performance improvement and high materials costs.

Among other less significant features, two main parameters were found to be relevant: 1) the "typical grain size" (GStyp) which is an estimate of the diameter of the maximal circular area that can be drawn inside each mineral phase grain; 2) the "index of fracture" (Ifrac) that ranges from 0.0 (not fractured) to 3.0 (very fractured).
The values of Ifrac depend on the number of micro-cracks that are visible in each mineral grain.
Table 2 - Estimates of texture parameters: typical grain (phase) size GStyp in [mm] and index of fracture Ifrac .
Parameter Value Sample amount (aprox.) 3 g Powder grain size max 30 µm 2 θ (range) 5 - 104.996 º Scanning rate (2 θ) 0.012 º/s Slew 1.2 º/m Anode Cu (45kV, 20 mA) Table 4 - Range of interatomic distances in the most intense peak of each major mineral [5].
underestimated (underestimation in the number and dimension of the locations where this phase is observed).

An important parameter of polycrystalline materials is a relation between the volume DV and grain boundary DGB diffusion coefficients.
A single-phase powder with an orthorhombic lattice and 15-30 µm grains was prepared.
The initial material was a coarse-grain ceramics with 70-80% of theoretical density.
The number of primary beam particles hitting the sample was measured within ~1% by a secondary monitor.
Gust: Fundamentals of Grain and Interphase Boundary Diffusion (Ziegler Press, Stuttgart, Germany 1988)

This paper uses micro-grinding tool with 500# grains and 0.9 mm diameter to grind nickel-based superalloy Inconel600 through three factors(grinding depth, feed rate, spindle speed ) at three levels orthogonal grinding experiment in mesoscopic scale.
Machine: precise micro-grinding machine JX-1A; tool: micro-grinding tool electroplated 500# grains in the surface, the diameter of the tool handle is 3mm and the head diameter is 0.9 mm, the length of grinding tool is 4mm, the head length of the tool is 2 mm, the distance between the abrasive grain is 21.23μm according to (f) in figure 1; material: nickel-based superalloy Inconel600; testing instrument: three-dimensional contourgraph MICROMEASURE, STIL Sarl-France,as shown in figure 1.
Experimental results and analysis Table 1 Orthogonal experimental design and result analysis Factor Test number n[kr/min] [μm] [μm/s] Rak[nm] 1 1(30) 1(3) 1(100) 797 2 1 2(6) 2(200) 974 3 1 3(9) 3(300) 1150 4 2(40) 1 2 852 5 2 2 3 1047 6 2 3 1 657 7 3(50) 1 3 997 8 3 2 1 579 9 3 3 2 964 974 882 678 852 867 930 847 924 1065 R 127 57 387 N is 3 levels of each factor in the orthogonal table, shown in table1, is the average roughness of the j-th column factor at the 1 level, as the same theory, and can be get, j=1,2,3; is the difference between the adjacent level in the j-th column factor; Rrepresents the range of , , in the j-th column factor:
(4) (5) Here, is the interactive return coefficient of polynomial with degree and polynomial with degree, is the roughness of the interactive experiment, K is the number of interactive experiment, obtaining: =15
Table 2 The grinding parameters of verification test Factor Test number n[kr/min] [μm] [μm/s] 1 30 3 100 2 30 6 200 3 40 6 300 4 50 9 200 Table 3 The table of comparing regression calculation results with the test results Test 1 Test 2 Test 3 Test 4 Test Result 797 974 1047 964 regression calculation result 783 847 852 980 Relative error -1.76% -13.04% -18.62% 1.66% Conclusions Through range analysis of orthogonal experiment about grinding nickel-based superalloy Inconel600, obtaining: the influence of the feed rate is the biggest, followed by the spindle speed, the grinding depth is minimal; the optimized process grinding parameters :n=50kr/min, =100μm/s, =6μm, the minimal surface roughness is Ra=579nm.

The microstructure of a 12%Cr martensitic steel, quenched and tempered in air, consists of prior austenite grains, packets, blocks, and laths.
With the increase of number of cycles the height along one extrusion fluctuates importantly.
The number of secondary extrusions increases with number of cycles of loading but the height increases as well.
Then with the increase of number of cycles the heights increase too.
It is because the principal extrusions have prolonged in their length too with an increase of number of loading cycles; and the speed of growth of extrusions is not constant along the whole length of an extrusion.