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It uses rectilinear grid interception method similar to the one used in grain size determination along with mathematical statistics to realize the quantitative rating of the banded structure and directionality degree.
The standard diagram is determined by the increasing amount of banded ferrites by considering the degree of band penetrating the field of vision, the continuity as well as the quantity of deformed ferrite grains.
Second, the standard focuses on realizing the quantitative rating of banded structure and directionality degree in steel using rectilinear grid interception method similar to the one used in grain size determination and mathematical statistics method; the relevant inspection data could be applied to calculate the parameters such as band width, directionality degree index Ω12 and the anisotropic index AI.
The biggest obstacle encountered in applying ASTM E1268 standard to production and engineering inspection is that a large number of vision fields are required for measurement.

The testing methods included: • Testing the materials consistency o binder content as residue on ignition o change in grain size composition by sieving o density • Mechanical testing o compressive and tensile strength on cubes with an edge length of 40 mm referring to DIN EN 12190 and DIN EN1542 o Young’s modulus on cylinders with a diameter of 45 mm and a length of 140 mm referring to DIN EN 13412 o for abrasion resistance using the so called “Böhmescheibe” according to DIN EN 13892 o for creep resistance referring to DIN EN 13584 with a compression load of 25% of the maximum strength • Testing for adhesion to the concrete substrate by pulling of steel cylinders with a diameter of 50 mm, referring to DIN EN 1542
Figure 3 (a) Surface of dry sprayed polymer concrete specimen, (b) cut through the specimen, SPC applied to concrete substrate Table 1 Results from the laboratory testing of SPC specimens Test method Results Property Norm Unit Value Material consistency Binder-content residue on ignition [wt-%] 14 to 21 Change in grain size DIN EN 12192-1:2002 Loss of larger grains Mortar density DIN EN 12190:1998 [g/cm³] 2.02 Mechanical properties Compressive strength DIN EN 12190:1998 [N/mm²] 90 to 105 Tensile Strength DIN EN 1542:1999 12 to 16 Young’s-modulus DIN EN 13412:2006 13 500 to 18 000 Wear resistance DIN EN 13892-3:2004 [cm³ /(50 cm²)] 8 to 10 Creep deformation DIN EN 13584:2003 [mm/m/d] 0.039 Hygroscopic properties Coefficient of sorption DIN EN 13057:2002 [kg/(m2 d0,5)] 0.001 Diffusions resistance μH2O DIN EN ISO 7783:2012 - 3440 Thermal properties Thermal expansion αT DIN EN 1770:1998 [10-6 1/K] 32 Adhesion Pull off strength DIN EN 1542:1999 [N/mm²] > 3.5 average > 2.6 minimum Durability
Here, the spin-lattice (T1) relaxation was measured, indicating a number of material properties such as molecular mobility and magnetic impurities in the material.

Thus the typical MIM production of high-strength Ni-based superalloy components entails a number of sequential, time-consuming and expensive manufacturing steps which hinder the overall advantages of the entire MIM manufacturing route.
The higher temperature and longer sintering time caused considerable grain growth in lot A samples, which turned out somewhat oversintered.
Since the assintered density of these samples was already fairly high (98,49 ± 0,10% TD), it's concluded the gain in density due to HIPping was not enough to compensate for reductions in those mechanical properties which might have been caused by grain growth during HIPing. 5 As-sintered parts: Sint'd & HIP'd parts: Sint'd & heat treated parts: [1280 ºC / 2hr] [1185 ºC / 4 hr / 1000 bar] [1080 ºC / 8 hr - 700 ºC / 16 hr] 364 ± 8 HV10N 355 ± 3 HV10N 382 ± 9 HV10N As-sintered dog-bones: Sint'd & HIP'd dog-bones: Sint'd & heat treated dog-bones: [1280 ºC / 2hr] [1185 ºC / 4 hr / 1000 bar] [1080 ºC / 8 hr - 700 ºC / 16 hr] 0,2%PS UTS Є 0,2%PS UTS Є 0,2%PS UTS Є [MPa] [MPa] [%Lo] [MPa] [MPa] [%Lo] [MPa] [MPa] [%Lo] 800 1161 25
It's suggested HIP-induced grain growth caused these reductions despite the slight gain in density shown by the hot isostatically pressed parts. 5.

These parameters were optimized after number of experiments to get amorphous ribbons.
This increase in the value of Hc may be accounted by the fact that for small grain sizes (< 100nm), Hc increases with increases in grain size [1].
So we conclude that as the sample is annealed at higher temperatures, the nanocrystalline grain size increases giving a higher value of Hc.

The media developed for dry barrel finishing is made of nylon resin mixed with abrasive grains.
� Turret rotation speed 0-240min -1 Rotation rate of barrel to turret -1 Distance between the turret center and the barrel center 160mm Barrel shape and number Equilateral octagon 㧔1.72L㧕˜4 Base side:46mm Length:165mm Barrel Turret Media Workpiece Workpiece� Ǿ30˜12mm, S45C(162,228HV), SUJ2(204,309,522,877HV) Media� Nylon6㧗Abrasives(A#320), ٌ4˜4, 6˜6mm Media charging ratio 20,50vol% Turret rotation speed 120,240min -1 Characteristic X-ray CrKǩ Target Cr Peak angle 2ǰ(deg) 156.4 Measuring method sin 2Ȁ Voltage (kV) 40 Current (mA) 40 Ȁ angle(deg) 0,7,15,22,30,37,45,52 Fixed time (sec) 10 Collimator (mm) 2.0 � Table 1 Specification of centrifugal barrel machine Fig.1 Centrifugal barrel finishing Table 2 Finishing conditions Table 3 Conditions of X-ray diffraction stress measurement Experimental Results and Discussion Influence of Finishing Conditions on Finishing Characteristics.
This is considered to be because the intrusion depth of the abrasive grain on the media surface to the workpiece surface at the collision of media to the workpiece decreases with the increase of the workpiece hardness.� Figure 9 shows the relationship between the workpiece hardness and the surface roughness under the same finishing conditions as shown in Fig.8.
Consequently, the change of the intrusion depth of the abrasive grain on media surface caused by the change of the contact force of the media to the workpiece becomes small as the intrusion depth decrease, and the surface roughness becomes small.�� Figure 10 shows the relationship between the workpiece hardness and the edge radius for one hour of finishing time under the same finishing conditions as in Fig.8.�6he edge radius decreases as the workpiece hardness increases.

A further milling of the nanocrystalline β-SiC particle leads to a decreasing grain size to 2.6 nm, and then causes a crystal to amorphous transformation.
This decrease is coupled to a particle state as energized (e) by severely introduced grain boundary and crystalline defects, which is a preparatory stage of the solid state amorphization.
The fracture toughness (KIC), as deduced from a relation of P/co3/2 =KIC/A(E/Hv)n with A=0.016 and n=0.5 (E is Young's modulus, Hv being Vickers hardness number) for a median/radial crack, is 13 MPa･m 0.5 .
In the case of d>dc, each grain that is excited to a critical energy (∆GMG) can undergo a crystal- amorphous transformation by one after another.

It had rather isotropic texture as shown in Fig. 1(a) obtained by electro backscatter diffraction (EBSD) measurement and had relatively large average grain size of about 180 μm.
Meanwhile, the extruded alloy had small average grain size of about 60 μm and had strong texture, of which the basal plane of hcp structure was about parallel to the extruded direction as shown in Fig 1(b).
Owing to the arrangement of the heaters and the thermocouple, the compressive displacement was converted from the number of pulse using the pre-determined compensation curve.
The EBSD measurement was performed only on the cast alloy because the large grain size is preferable to distinguish twinning from slip lines.

The size of the diamond abrasive (non conductive) used was SD700 mesh and the concentration was 125 (grain volume percentage: 31%).
The average grain size was 10µm for both types of PCD.
Though details are not shown on the results of the trueing using a vertical truer, it will be worth describing that the electrically conductive vitrified bonded wheel could be trued with extremely high efficiency requiring far less number of passes for correcting the wheel deviation, namely only one tenth of that required by the metal bonded wheel.
Fig.3 Normal grinding force at standard grinding Table 1 Experimental device and conditions Conductive vitrified bonded wheel •Standard diamond abrasive wheel •Conductive diamond abrasive wheel SD700, Conc.125 (f100mm×t5mm) Machine •NC surface grinding machine (NSP-50, Nachi) •Spindle: Air static spindle (Toshiba Machine) •Discharge power source (SUE-87, Sodick) PCD workpiece •Conventional PCD (C-PCD, 5mm×8mm) •Electrically conductive PCD (EC-PCD, 5mm×8mm) Diamond grain size: 10µm, Content: ≠90% Grinding conditions VS=40m/s, VW=0.1m/min, a=1µm, b=2mm, l=5mm Surface plunge grinding Discharge conditions ui=60V, iP=6A, te=4µs, to=10µs Working fluid Water soluble grinding fluid (NK-Z, 2%, Noritake) Results of the EDM Assisted Grinding Characteristics in the Standard Grinding.

The corrosion mechanism of Zr-based alloys can be explained by characterizing the oxide properties such as the crystal structure and the grain morphology.
A number of investigations have revealed that the crystal structure [10] and grain morphology [10,11] were closely related to the corrosion kinetics of Zr-based alloys, however, this conclusion remains a talking point.
Coarse grains were not found but fine cell structures were observed in the TEM microstructures of Zr-0.2Nb.

It is proved that thicker MAO-coatings formed in a solution with corundum particles are similar in grain structure to MAO-coatings formed in a liquid solution, but are characterized by a higher content of corundum and modifications of crystalline aluminum oxide in general.
However, the process of formation and growth of MAO-coatings occurs under the influence of a number of factors, including the synthesis of aluminum oxide and other substances as a result of plasmochemical reactions in MAO-coatings, the hydration of their surface layers and their dissolution by electrolyte solutions [6].
It is confirmed that the grain structure of MAO-coatings formed in a liquid solution and a solution with corundum particles do not have fundamental differences.
Fragments of cross microfractograms of the MAO-coating on the AMg3 alloy disk in the middle zone (a) and near the outer surface (b) At the same time, all MAO-coatings formed in 50...80 minutes and having a thickness of more than 120 mm have a pronounced loose outer part with a thickness of 15...20 mm with high porosity, large grains and undeveloped intergranular bonding.