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The perpendicular-to-grain loaded connections gave lower connection strength compared with connections loaded parallel-to-grain.
Fig.1 Specimen Design Fig.2 Specimen Labeling Rule Table 1 Material Property Plate type Plate thickness(mm) fy (Mpa) fu (Mpa) Bearing strength (parallel-to-grain )(Mpa) Bearing strength (perpendicular-to-grain )(Mpa) Literature[4] Steel plate 1 206.8 340.9 — — Steel plate 1.5 210.6 340.3 — — Literature[5] Steel plate 0.8 298.33 365.67 — — Steel plate 1.5 198 335 — — Steel plate 2 261.67 388.33 — — Steel plate 3 271.67 391.67 — — Literature[6] NAFC plate 8 — — 15.9 8.8 NAFC plate 12 — — 16.7 10.8 LCFC plate 8 — — 22.8 15.8 LCFC plate 12 — — 24.7 17.8 Design methods on shear capacity of steel plate-steel plate single tapping screw connections at home and abroad Design method of AISI specification.
Table 2 Comparison between Code Calculation and Test Results of Steel plate-steel plate Connections Specimen number Ptest (kN) Nvf (kN) Ptest /Nvf Pns (kN) Ptest /Pns Ps (kN) Ptest /Ps S1-1-4.8-1 3.3 1.676 1.969 3.137 1.052 1.450 2.276 S1-1-4.8-2 3.2 1.676 1.909 3.137 1.020 1.450 2.207 S1-1-4.8-3 3.4 1.676 2.028 3.137 1.084 1.450 2.345 S1.5-1.5-5.5-1 6 3.357 1.787 6.158 0.974 2.904 2.066 S1.5-1.5-5.5-2 6.1 3.357 1.817 6.158 0.991 2.904 2.101 S1.5-1.5-5.5-3 5.8 3.357 1.728 6.158 0.942 2.904 1.998 S0.8-0.8-3.45-1 2.13 1.467 1.454 2.041 1.045 1.269 1.681 S0.8-0.8-4.87-1 2.19 1.743 1.262 2.425 0.907 1.507 1.459 S0.8-0.8-5.43-1 2.90 1.840 1.581 2.561 1.136 1.592 1.828 S1.5-1.5-3.45-1 4.42 2.459 1.801 4.681 0.946 2.152 2.058 S1.5-1.5-4.87-1 5.30 2.970 1.786 5.704 0.930 2.569 2.066 S2-2-5.43-1 7.30 6.381 1.145 10.750 0.680 5.519 1.324 S0.8-2-4.87-1 2.46 2.790 0.882 3.847 0.640 2.441 1.008 S0.8-2-5.43-1 2.89 3.110
Table 3 Comparison between Theoretical Calculation and Test Results of Steel plate-non-steel plate Connections Specimen number Ptest (kN) P (kN) Ptest /P N8Z-2-3.5-1 1.647 0.445 3.699 N8H-2-3.5-1 0.965 0.246 3.916 N12Z-2-3.5-1 2.507 0.701 3.574 N12H-2-3.5-1 1.733 0.454 3.821 L8Z-2-3.5-1 2.013 0.638 3.153 L8H-2-3.5-1 1.380 0.442 3.119 L12Z-2-3.5-1 2.813 1.037 2.712 L12H-2-3.5-1 1.980 0.748 2.648 Table 3 presents:(1) Shear behavior of LCFC plate screw connections is better than that of NAFC plate screw connections.(2) The bearing strength and the thickness of sheathings are main factors that influence the shear behavior of steel plate-non-steel plate screw connections.(3) Results calculated by Eq.9 are safe compared with test results, and Eq.9 is suited to calculate the shear capacity of steel plate-non-steel plate screw connections.

There is also studied a computation where the grains of nanocrystalline magnetic materials are represented by a brick arrangement [21].
In a useful model, the magnetic material is assumed to consist of N discrete grains of material which are uniformly magnetized, and which interact via dipole-dipole and weak exchange coupling.
Each grain has uniaxial anisotropy, with the easy axes randomly distributed in plane with a uniform distribution.
The mesh satisfies the Delaunay condition, which minimizes the number of elements with extreme shapes for a given distribution of nodes.
A special procedure is used to assure good properties for the nodes of the mesh: The nodes are reasonably uniformly distributed in space, and no node belongs to an unreasonably large number of elements.

The raw materials used in the present investigation were the Cu30Sn alloy, Zn grain, Sn grain and powder of LaNd.
According to Table 1, Cu30Sn alloy, Zn grain, Sn grain and powder of LaNd were quantified on the electronic balance, the allowable error was ± 1%, and then melted them in the box-type resistance furnace with the heating temperature 800℃ for 50min-60min.
Table 1 Composition of alloy(mass%) Number Cu30Sn Zn Sn RE 1 8.57 74 17.43 0 2 8.57 73.9 17.43 0.1 3 8.57 73.7 17.43 0.3 4 8.57 73.5 17.43 0.5 Melting temperature.
Fig.5 XRD of Zn20Sn6Cu0.1RE Fig.6 Effect of the content of LaNd on resistance rate of Zn20Sn6CuxRE Figure 3a and Figure 3b show that massive light gray CuZn5 is smaller and increaser in number in the structure of Zn20Sn6Cu0.1RE than that of Zn20Sn6Cu, consequently, the resistivity rises because structure becomes smaller and interfaces are increased which hinder the motion of electrons; Zn20Sn6Cu0.3RE structure shape is similar to Zn20Sn6Cu0.1RE, so resistivity of 0.3wt.% RE changes little; When the content of RE reaches 0.5wt.%, the white Sn-rich phase is continuous distribution and the original continuous distribution of dark gray Zn-rich phase forms a clear block which homogeneous distributes in the white network Sn-rich phase, the structure gradually thick, resistivity should have decreased, but there are a lot of dark hollow in the structure so that resistivity increases significantly as shown in Figure 3d.

Introduction Microstructural features in Ti-6Al-4V alloy such as grain size, phase ratio, and crystallographic texture have been investigated by several authors [1, 2], and it has been found that increasing grain size increases the flow stress and tends to reduce the maximum strain rate sensitivity.
As in the case of the volume fractions of α and β phases are approximately equal, the value of mean phase size may be considered as mean grain size [13].
Approximately the number of grid-point cell was chosen as 50 microphotographs×3 sections×5 separation distances in each test specimen for the analysis of two- point probability functions.
By imposing the random distributions of grain size on the gauge-length region, the results obtained from the previous work could not provide a quantitative agreement with experimental data.
In order to represent the heterogeneous microstructural evolutions during the deformation, a number of finite element models have been generated and Fig. 5 shows the predicted spatial variations of mean phase size with deformation.

(1) where n was the number of data points, yi was the vertical coordinate of the image, and yi was the mean value of yi.
Then the current density presented a rapid rise followed by a slow decline, which corresponded to the initial nucleation and growth process of grain.
It was generally believed that the rising current density in former portion was mainly related to an increase in electroactive sites, where each independent nucleus expanded in size (instantaneous growth) and/or increased the number of nuclei (progressive) on the substrate.
Crystal structure The grain structure of obtained NiCo electroforming sample is further described by EDS, XRD, and SEM methods, which give further details on the deposited feature on Ru/C multilayer film.
In the meanwhile, the internal crystal morphology was typified by the large-sized and protruding pillars consisted of aggregation of polyhedral crystals, which grew asymmetrically and irregularly together with well-defined grain boundary, as shown in Fig.5 (c).

Experiment Number Fig. 4 The final temperature difference of experiments Experiment #1 was performed at one-step reheating process under the condition of ta1=7 min, Th1=581and th1=2 min.
The microstructure shown in Fig. 6 demonstrates that the grains are globular at position [B], and the globularization is in progress at position [A].
The grains of experiment #3 shown in Fig. 7 are larger than that of experiment #2 and coarse obviously, though the globularizations of them are similar.
The globular microstructure were not obtained, and the grains are a little coarse at both positions [A] and [B] due to the slow reheating speed and longer holding time.
In case of experiment #9, though the grains are larger than that of experiments #2 and #8, the globular microstructure was obtained by raising the temperature and prolonging the time of the first holding process.

To confirm the formation of Barium Cobalt ferrite and to understand the nature of the residual carbon in the samples the FTIR spectra were recorded on a FTIR spectrometer (Bruker Tensor 27) at room temperature using the KBr pellet method between wave number ranges 4000-400 cm-1.
Fig. 3 shows FTIR spectra of as-burnt powder, powder preheated at 500 ᴼC and post heated at 950 ᴼC for 4hrs in wave number ranges of 400 - 4000 cm-1.
The first layer consists of ferrite grains of fairly well conducting, which is separated by a thin layer of poorly conducting substances, which forms the grain boundary.
These grain boundaries are more active at lower frequencies; which act as a hindrance for mobility of the charge carriers [22], hence the hopping frequency of electron between Fe3+ and Fe2+ ion is less at lower frequencies.
As the frequency of the applied field increases, the conductive grains become more active by promoting the hopping of electron between Fe3+ and Fe2+ ions, thereby increasing the hopping frequency.

Strain localization areas can be detected by optical-digital methods, based on which a number of defectometry control algorithms are developed [4].
In other words, parallel displacement of the material grains under the effect of plastic deformation without violation of the material integrity has taken place, the scheme of which is given in Fig. 2c.
Having analyzed the form of the obtained dependency ɛ - Lrel, two sections are found: Up to 13% - the section of the accumulation and opening of multiple cracks, when their length increases quite slowly due to the individual growth of components of the surface dissipative structure (multiple cracking sections); After 13%, when due to significant plastic strains, first of all, the rotational shears of grain conglomerates, the opening of cracks, their rotational shear and further coalescence take place on the specimen surface.
In addition, structural elements (grains, subgrains) deform along the direction of loading, the intensity of shears increases in the primary and secondary sliding areas [14].
Shirokov, Effect of D16T alloy grain sizes on its deformation inhomogeneity under static and dynamic loading, Strength Mater. 44 (2012) 551-555

Because a certain number of deuterium atoms went into the palladium lattice, holes formed on palladium surface.
This is the reason why repeatedly charging deuterium into palladium become more and more easily later and the surface has a rice-grain metal particle generation.
The rice-grain metal particle (arrow in Fig. 12 ) in EDS analysis shown in Fig. 14.
Fig. 13 and 14 told us: after excess heat, there were a large number of 3.59 At﹪ Ag on palladium surface it might be produced during the excess heat process.
And on the rice-grain metal particle of experiment palladium surface elements, Ag was found and its origin might come from a nuclear transmutation process.

It is suggested in this work that the restoration of ductility in the preheating zone is proportional to the static recrystallization according to the following equation: (7) where: m - the number of time step, increment of static recrystallization.
Model of recrystallization The conventional model that characterizes the phenomena which occur in metallic materials during hot deformation uses equations describing recrystallization and grain growth.
To determine the coefficients in the equation (Eq. 14), which is describing the grain size after dynamic recrystallization, additional experimental tests must be done.
The experimental results showed that there is no fracture of the wire though the large number of passes and any further thermal processing of the wire was needed.
Analysis of the microstructure after 25 passes (for wire 0.1 mm, Fig 6a) showed that the wire material contains only recrystallized grains (Fig. 6b).