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Such Dimensions of up to 10 µm are quite reasonable, e.g. assuming prior austenite grain sizes of up to 50 µm and considering martensite fractions of 0.8.
The number of nucleation sites increases drastically due to the prior martensitic transformations speeding up the nucleation of new phases.

Samples and methods 310 grains of the polished and faceted rubelite are selected, and their sizes are in the range of 4 ´ 10 ´ 10 mm to 10 ´ 18 ´ 25 mm, and they don’t have visible inclusions.
Fig. 1 Setting Point Graph of Chromaticity Parameters Fig. 2 Setting Point Graph of three elements of color Table 1 Hue Grades of rubelite Samples Hue angle (10°, 43°] (347.5°, 360°] U (0°, 10°] (325°, 347.5°] (302.5°, 325°] Description Red Pink Purple Violet Number 68 226 15 1 Simulation color block of average value Grade I II III IV Fig. 3 Setting Point Graph of Hue Grades of Rubelite Hue grading.
The number of samples of each hue is 68, 226, 15, 1, which is the same as the fact that most of the rubrlites are pink and peach-red.
Table 2 Chroma Grades of Red Tourmaline Samples Chroma C* £ 12 12 < C* £ 20 20 < C* £ 28 C*>28 Description Light Medium Intense Vivid Grade IV III II I Simulation color block of average value Number of red hue 24 20 16 8 Number of pink hue 30 72 68 56 Number of purple hue 2 1 5 7 Number of violet hue -- 1 -- -- Table 3 Lightness Grades of Red Tourmaline Samples Lightness L* ³ 58 49 £ L* < 58 40 £ L* < 49 33 £ L* < 40 L* < 33 Gray G £ 59 59 < G £ 68 68 < G £ 76 76 < G £ 81 G > 81 Description Bright Slightly bright Medium Slightly dark Dark Grade III II I II III Number of red hue 1 15 15 18 19 Number of pink hue 17 42 64 67 36 Number of purple hue 3 1 5 5 1 Number of violet hue - - 1 - - The chroma of samples is concentrated in C* Î (10,25), and according to the visual effect the chroma can be divided into light, medium and intense, vivid four grades with increasing quality, and each grade has 56, 94, 89, 71 samples.

All confining systems were applied “as usual”, that is with a single textile (or fabric) sheet wrapped around each specimen until the desired number of layers was achieved.
Here, “conventional wrapping” corresponds to a single textile sheet being wrapped around the shear span until the desired number of layers is achieved.
These strengthening schemes were selected in this study so that they would provide useful insight into the effects of the fiber reinforcement ratio and the number of TRM layers (of equivalent axial rigidity).
Moreover, regardless of the matrix material (polymer-modified mortar versus epoxy resin), the strength generally increases with the number of layers and the axial load, at the expense of deformation capacity.
Weak textile-to-mortar bond regions were evident when mortar with finely-grained sand was used in combination with uncoated fiber meshes; this was attributed to the stickiness of the mortar (i.e. to the high plastic viscosity of the mixture) that led to poor mortar penetrability in the fiber bundles and to reduced failure load compared to the counterpart specimen comprising a TRC SiP form made of a coarse-grained mortar.

The fabric of ore are mainly idiomorphic hypidiomorphic - fine-grained, cryptocrystalline - fine grain, allotromorphic microgranular structure, blocky, banded, frame-slab structure.
Anomaly evaluation Evaluation index A large number of research in domestic and foreign shows that the parameter of gold deposit primary halo zoning is important index for improve accuracy and reliability of concealed prediction.

Fig.3 Lotus monofilament fiber in longitudinal revolving In Fig.3, in lengthways, the mature lotus fiber, with ribbon spiral revolving structure and clearly subtle cross grain, associates side by side by several monofilament fiber.
Seen from the surface morphology of lotus fiber observed by SEM, ribbon spiral revolving and revolving number in unite length are closely related to the variety, growing condition, harvest season, extraction place and extraction method.
Monofilament fiber in longitudinal tube of lotus stalk associates closely and shows spiral revolving structure with clearly fineness cross grain.

The figure (Fig. 4(b)) shows that the surface ceramic coating has a lamellar structure which has been formed by accumulating large numbers of flattened splats.
In laser remelting process, the surface ceramic coating is heating, melting and recrystallized, and forms fine grains (Fig. 5(b)).
The deepness of molten region and grain size are correlative to the process conditions, such as laser power, size of laser spot, scan velocity and materials’ thermal-physical properties.

Application of unconventional processing methods results in grain size reduction and increase of yield stress.
Chemical compositions of alloys with differentiated chemical composition for plastic forming were elaborated and they contained mainly Al, Mn, Zn, Zr, and rare-earth elements that create thermodynamically stable phases on grain boundaries.
These numbers show the extent to which lithium additive caused deterioration of electrochemical corroion resistance of magnesium alloy AZ31.

The HA peaks are better resolved after calcination as a result of the growth of the grains.
The HA peaks are sharper than for the sample calcined at 500 ºC, indicating that the temperature of the substrate during deposition was high enough to cause grain growth in the coating, but no phases associated with the decomposition of HA are detected.
A small number of dense particles can be seen in the coatings, as well as hollow spheres with a dense skin, distributed in a matrix of unmelted, porous aggregates.

The crack growth behavior is affected by metallurgical factors, such as grain size, material microstructure, inclusion etc[12].
It is also worth to consider that the grain size of the material is 0.1 mm and the transition crack length is 0.065mm.
In axial loading case, crack length is steadily increased with the number of cycle under axial loading case.

When substitutional elements are partitioned there is little doubt concerning their effects: the rates of transformation are essentially controlled by the slow diffusion of these elements, either in the parent austenite [1,2] or in a contacting austenite grain boundary [3] or both, and are typically insignificant on the time scale of modern heat treatments.
This method, which was used in the past by a number of investigators [14-16], consists of reheating the specimen into the austenite one phase region in an atmosphere of wet-H2.
The growing ferrite grains traverse many crystals of the parent austenite, thus eliminating any strong interfacial structural effects.