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As the research of petrophysical facies must build on the basis of sedimentary rock phase and the digenesis analysis, and by means of the integrative quantitative indexes to express, therefore, the reservoir porosity, permeability, clay content, median grain diameter and the characteristic parameters FZI reflecting pore structure are selected on the choice of phase mode characteristic indexes[2].
According to the existed expert studies and the specific circumstances to the reservoir lithology, physical properties and heterogeneity distribution of north three east regions of Daqing oilfield Shabei development zone, the petrophysical facies is divided by the following parameter indexes: porosity(), permeability(k)which reflect the physical properties of reservoir; clay content(), median grain diameter()which reflect the reservoir rock phase features; FZI[3] which reflect the micro-pore structure features of reservoir.
The minimizing error function is: (6) In formula (6), Y is the actual output vector of fuzzy neural network, D is the expected output vector [5], if are the parameters to be adjusted, the learning rule is: (7) In formula (7), is the learning speed, is the inertial coefficient, is the iteration number.
Compute the FZI value by count the porosity, permeability, clay content and median grain diameter of 537 natural layers or the relative homogeneous segment within layer, and divide 5 types’ petrophysical facies. 219 representative sample layers are selected to form the classification standard pattern library of petrophysical facies, among these layers, there are 53 samples of class I petrophysical facies, 76 samples of class II, 50 samples of class III, 30 samples of class IV, 10 samples of class V.
The correct number is 143, and the accuracy is 81.7%, it achieves the ideal classification results.

Changes of Concentration of Ca and Mg ions in SBF indicated that Ca and Mg ions took part in bioactive. 0 1 2 3 4 30 35 40 45 50 55 60 65 70 (a) Concentration of magnesium(ppm) Experimental serial number 18d 21d 0 1 2 3 4 40 60 80 100 120 140 (b) Concentration of calcium in SBF(ppm) Experimental serial number 18d 21d Fig.2 Ion concentration change of SBF after coatings soaked in SBF: (a) Mg 2+; (b) Ca2+ Fig.3 Morphology of coatings after soaked in SBF for different times: (a), (b) and (c) is single calcium phosphate coatings simulated for 3, 9 and 21days, respectively; (d), (e) and (f) is composite coatings simulated for 3, 9 and 21days, respectively Morphology of calcium phosphate coatings after soaked in SBF.
Small grain formed on composite coatings because of change of Ca, P between composite coatings and SBF.
At the same tine, amorphism constitutes appeared in XRD patterns, which showed that grain size of sample was thin, tiny and low crystal.
(2) Ppy makes crystal grain thin and makes crystallite form, which shows that the size of new constitutes is small and the constitutes are like to natural bones.

and parallel alignment of the phase distribution characteristics, between the laths can be seen at the same time a large number of unevenly distributed high-density dislocation entanglement, the formation of dislocation cell.
Fig. 3 TEM micro-graph of lower bainite in complex phase organization This is because the sub-stable residual austenite in the tempering will be decomposed into bainite and carbide and other more stable organization, in the plastic deformation, because of the reduction in the number of residual austenite, concentrated deformation zone will be transferred to the lath martensite, and a large number of tempering precipitation phase and dislocation interaction, can significantly improve the dislocation opening resistance, thus contributing to the yield strength of the test steel; at the same time, the residual austenite better At the same time, the better plasticity of residual austenite is also conducive to lower stress concentration, which can only lead to crack destabilization under higher stress conditions, thus leading to higher plastic transformation resistance.
With the increasing tempering temperature, the interface between adjacent martensite lath bundles starts to become less straight (Fig.5(b)), this is because at higher temperatures, the dislocation density decreases accordingly, the remaining dislocations will be rearranged, the lath martensite grains are split into sub-grain, and the tempering organization occurs similar to the cold working process "reversion" phenomenon; When the tempering temperature continues to rise to nearly 400°C, although the spatial morphology of the martensite grains is still lath, the demarcation line between the lath bundles has become very blurred (Fig.5(c)), probably because the dislocation density continues to decrease, and the small amount of The twin sub-structure basically disappears and most of the martensite containing supersaturated carbon undergoes desolvation, forming a transition from ε-carbide to more stable brittle carburite.
Firstly, there are a large number of dislocation sub-structures in the lath martensite group in the complex phase, the distribution of deliveries of lower bainite and martensite lath bundles, and a small amount of residual austenite can also reduce the stress concentration, the coupling effect of these factors is important to suppress the crack nucleation and expansion during the material deformation and fracture process, and achieve a good match of strength and toughness; at the same time, the sub-stable precipitation phase generated by tempering is uniformly distributed in the lath martensite matrix, which can also impede the movement of dislocations and make dislocation lines bend around it, leading to an increase in the nucleation rate of phase deformation and causing grain refinement.Third, a small amount of residual austenite existing between the martensite and lower bainite lamellae is also important for the improvement of the test steel properties, the small amount (<1-2%) and the
Making ultrastrong steel tough by grain-boundary delamination [J].

The weighted (R) and expected (E) reliability values were calculated using the following equations: where I(o, i) is the observed intensity of a fitted data point (i), I(c, i) the calculated intensity at this data point, I(b, i) the background intensity at this data point, w(i) the weight of this data point as w(i) = 1/I(o, i), N the number of fitted data points, P the number of refined parameters, and ∑I(o, i) in E is the sum of over all fitted data points (N) that are 2σ above the fitted background.
More importantly, the width of this temperature range △T（△T =1120-Tp）may determine the amount of grains remelted[16].
The key reason is that during heat-treating, Li+ reduced the viscosity of glass melt and weakened the resistance of ion migration, it is easy for crystal grains growth and the arrangement of grains tend to be regular.
With Li2O addition increasing, the content and size of crystal grains increased, and the melt had lower viscosity in favor for sintering densification.
But then, when the Li2O addition is more than 1.5%, the crystal grains remelting increased acutely, leading to more structural defects and the bending strength decreased relatively.

XRD studies indicated that all of BPT films consisted of single phase of a bismuth-layered structure with well-developed rod-like grains.
Generally, the formula of doped bismuth titanate is (Bi2O2)2+(Am–1BmO3m+1)2– , where A means mono-, di-, or trivalent ions, or a mixture of them; B means quadri- or quinquevalence ions, such as Ti4+, Nb5+, Ta5+; and m means integer number > 1.
Which indicate that the BPT films consist of well-developed rod-like grains with random orientation.
The average length and diameter of the grains of the film with x=0.75 are about 350 nm and 150 nm, respectively.
It implies that the film with x=0.75 promotes bismuth titanate grain growing greater than the film with x=0.25.

The introduction and application of lead-free alloys caused a number of soldering defects not observed earlier; mechanisms of their formation are still unclear.
Nickel is practically insoluble in tin; however – depending on the concentration – a number of intermetallic phases can form between the two metals.
Shnawah et al. have found that the microstructure of Sn-Ag-Cu alloys is constituted by fine-grained Ag3Sn and coarse-grained Cu6Sn5 intermetallic phases dispersed in the β-Sn matrix.
In Sn-Ag1.0-Cu0.5 alloy traces of fine-grained Ag3Sn along with relatively large-sized particles of primary tin are dispersed in the matrix.
The microstructure of the alloy containing 4% silver is different: the higher silver content results in the formation of a large number of Ag3Sn particles and small-sized primary tin (Fig. 5) [10].

The grain size distribution and the mean grain size were found from TEM images using the mean linear intercept method.
The mean grain/subgrain size is 560 nm.
After 8 passes of I-ECAP, there are a larger number of high angle grain boundaries and the mean grain/subgrain size is reduced to 410 nm.
TEM images and grain size distribution in Al 1070 subjected to 4 and 8 passes of I-ECAP.
Zhu, Continuous processing of ultrafine grained Al by ECAP-Conform, Mater.

After oxidation at 900 ºC (Figure 2a), large (0.5-2 μm) grains were dispersed throughout the fine (<0.2 μm) grains.
After oxidation at 1200 ºC (Figure 2d), fine (<1μm) grains have developed along the edge of large (5-15 μm) TiO2 grains.
After oxidation at 1300 ºC (Figure 2e), small (<2 μm) globular grains have developed along the edge of large (5-20 μm) TiO2 grains.
In addition, at these temperatures, the planar defects can still be seen in the TiO2 grains although fewer in number.
After oxidation at 1400 ºC (Figure 2f), small (<5 μm) globular Al2TiO5 grains were formed along the edge of large (10-50 μm) TiO2 grains.

A large number of experimental studies have shown that, 65Mn spring steel most suitable for manufacturing a variety of Plowshare, stubble cutter, rotary knives and other agricultural machinery in the soil working parts. 65Mn is a good material for blade, but should be reasonable to obtain the desired heat treatment microstructure and properties, such as grain refinement, reasonable quenching, etc. and fully tempered, reduce stress, to obtain high wear resistance, microstructure, etc.
It can be explained that when austenite grains began to be formed they were small; the grains will gradually grow with the temperature raising [5-7].
The higher of the temperature, the more significant do the grain grow under the certain temperature, and the longer the time kept, the bigger do austenite grain grow.
The material hardness value withered with the decline of the mechanical properties for the bigger grains.

It was obviously that micro-morphology of doped samples was identical basically, and the range of grain size was 1μm~10μm.
Meanwhile, a little gap between grains and porosity were found, and grain boundaries were observed clearly.
SEM micrograph of GDC sample is provided in Fig.2 (a), the grain size of GDC sample, more uniform and sample was more compact compared with other doped samples.
However, difference in grain sizes was significant in Fig.2 (b) and Fig.2 (d), the reason is that the addition of Bi2O3 resulted in decreasing the sintering temperature, and grains grown up gradually with the increase of sintering temperature.
Furthermore, because of the holding time was not long enough, the samples did not sinter well, which resulted in the increase of the number of pores.