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Some Si particles are distributed along the grain boundary (Fig. 1a).
Viewed from [011]Si zone axis, the Si particle appears to be twinned (Fig. 1c), although the number density of Si twins appears to be low.
Fig. 3b was enlarged from one area as marked with a dashed line in Fig. 3a, showing a Al2Si2Sr particle at the grain boundary.
Fig. 6 shows a faceted Si crystal on the grain boundary in melt spun Al-5Si-6100 ppm Yb alloy.
Again, Si twinning was observed, although the number density of twins was reduced compared to the Si twinning in melt-spun condition.

The holes of the ceramic are full of aero gel particles whose grain size is 10 ~ 20 μm and the distribution of pore size is ten-seventy nm.
The pores formed by the fiber have been filled with a large number of SiO2 aerogels as Figure 1(b) show.
As can be seen by the microscopic structure, after compositing with aerogels, the original large numbers of micron- millimeter holes are replaced by a large number of low thermal conductivity of SiO2 aerogels.
It is equal to set infinite number of hot-covering plates on the transmission way of thermal radiation.
And the increasing number of twists and turns of aerogels hole wall will cause the absorption of infrared rays and diffuse in different direction and suppress the heat radiation.

Melting enthalpy is no longer a constant but a number decrease with diameter decreasing.
The Curie temperatures of iron in different particle sizes show no difference because Curie temperature is one of the intrinsic magnetic parameters related to chemical composition and crystal structure but not to the grain size.
(3) Melting enthalpy is no longer a constant but a number decrease with diameter decreasing.

Although the broadening of the peaks shows small crystal grain size of the particles and the average crystal grain size can be evaluated utilizing the Scherrer equation, it is important to understand that the Scherrer formula referred as the crystallite size, not a particle size.
After 5-6 days of sample preparation, the distribution consists of two fractions: a large number of small magnetic particles with an average diameter of 77.93 nm (98.8%) and a small amount of large aggregates with an average diameter of 405.7 nm (1.2%).
However, in Sample B that was prepared after about 1-2 days, particle size distribution consists of two fractions: a large number of small magnetic particles with average diameter 140.7 nm and a small part number of large aggregates with average diameter 669,7 nm.
Acknowledgment This research received financial support from grant number 178/SP2H/LT/DPRM/2019, by the Department of Ministry of Research, Technology, and Higher Education of Republic Indonesia, through the Institute for Research and Community Services of Lambung Mangkurat University with contract number: 123.5/UN8.2/PP/2019.

The microstructure of the alloys is not homogenous, and there are large grains along with small grains, indicating that dynamic recrystallization occurred during the extrusion, Fig. 2(a-b).
Yet, since the Mn content in both the alloys is similar (Table 1), the number of Al-Mn particles is not expected to be different and their effect on the alloys’ corrosion behaviour of the alloys is assumed to be the same.
The Mg2Sn particles are larger, however the number of Mg-Al-Zn particles is higher, i.e. there is more pitting sites on the alloy’s surface.
It seems that the mechanism of corrosion initiation was pitting corrosion and it was affected by the number of second phase intermetallics.
In order to improve the alloy’s corrosion resistance, there is a need to develop an alloy with a tendency to form stable oxide layer, while at the same time it will have a minor number of second phase intermetallics.

However, it has been difficult for uses of the parts that are required in the high fatigue strength and high reliability, because of a large number of casting defects exist in the material.
Therefore, some treatments to reduce the size of casting defects and the number of casting defects have been studied.
And also, reason of this was that the surface crack initiation period became longer by SP treatment because the fine grains prevented the slip of microstructure also.
If based on the above results, fatigue property of Al alloy might be more improved by applying the shot peening to the SL die-casting material. 10 4 105 10 6 10 7 100 150 200 250 Stress amplitude σa , MPa Number of cycles to failure Nf , cycles NP SP HIP non-HIP 10 4 10 5 10 6 10 7 100 150 200 250 Stress amplitude σa , MPa Number of cycles to failure Nf , cycles NP SP SL(slip) (a) Compare the SP with the HIP (b) Compare the SP with the SL Fig. 7 S-N curves Conclusions Rotating bending fatigue tests were carried out on two types of SP-treated AC4CH.
Reasons of this is that normally peening effects by the SP treatment such as compressive residual stress and work hardening effects are not so large in the Al alloy compared with other metal as steel. 4) The fatigue life property is improved by the SP treatment since the fatigue crack propagation rate decrease and the surface crack initiation period will become longer by the SP treatment because the fine grains prevent the slip of microstructure also.

As the head and tail part of strip coiling in higher temperature, growth of ferrite grain and diffusion of carbide become easier, solution strengthening weakens.
In this study, coiling temperature, finish rolling temperature and running speed of ZSAC1 strip and number of valves which had been turned on were analyzed.
Process automation system calculates the number of valves which need to be turned on and can modify computational accuracy of model constantly according to the measured coiling temperature.
Numbers of valves turned on for strip No.3 are shown in Table 3.
As shown in Table 3, numbers of valves turned on decreased when the tail part of strip No.3 entered into laminar cooling device.

After reaching a certain scale thickness (or, conversely, a certain number of thermal cycles), weight loss occurs due to partial scale spallation.
Titanium tends to oxidize within the subsurface region of the alloy, particularly at grain boundaries.
When present in a small but sufficient amount, the RE tend to segregate to the alloy/scale interface and scale grain boundaries, and have the apparent effect of suppressing cation diffusion in the scale.
The mass-change behavior of the alloys as a function of number of thermal cycles is shown in Fig. 7.
The mass-change behavior of 800 series alloys from two different suppliers as a function of number of 1-day cycles at 1000 °C in air.

Introduction There are a number of strain determination methods, but only some of them are adequate for investigating local stresses.
With the experimental set-up described in [9], the strain resolution of a few parts per ten thousand is achieved if a sufficient number of Kossel lines are used.
The method Briefly, in the proposed method, line profiles collected from a reference pattern (originating from an area which is assigned zero strain) are used to determine positions of corresponding lines in other patterns originating from strained areas of the same grain, and then − based on shifts of line positions − the strain tensor is calculated.
To describe the profile-based strain determination method let us assume that a number of diffraction patterns collected from different locations in the same grain are available, and one of them is chosen as a reference pattern.
The numbers below the profiles represent profile correlation coefficients.

In order to count the number of attached cells, cells were detached using 0.25% trypsin with ethylene diamine tetraacetic acid and then resuspended in PBS.
The resulting formazan can be quantified spectrophotometrically and correlated with the number of viable cells and metabolic activity.
Fig. 3 Cell numbers attached to the surface of samples after 4 h seeding (presented as percentages of cells attached to Ti alloy).
When the corrosion is developing, the continuous distribution of glass matrix might prevent corrosion from spreading from one grain to another grain.
With regard to alloys, a large number of reports have shown that the ALP activity of cells was influenced by the surface parameters such as surface chemistry, microtopography and crystallographic orientation [15, 16].