Search results

It is postulated that the high strength of the Al-Fe alloys could be achieved by both the nano-grained structures and the solid solution strengthening.
They exhibited full density with high-angle grain boundaries in micrometer range, and a sub-grain size typically smaller than 100 nm [1].
A Gaussian smearing [14] of 0.1 eV is applied to the occupation numbers.
The measured data of Fe content, grain size and yield stress [1] are also shown.
The analytical results obtained from Eq. (3) using the measured grain size and yield stress are also shown in this figure.

The reason for this inconvenient situation is obviously that microstructural processes in thermal creep remain poorly understood and this is due to the relatively small number of studies that have been carried out.
It means that the steam hydration process did not lead to the grain size coarsening.
The pre-hydrided specimens (Fig. 3b,c) contain also hydrides which are located predominantly in the grain interiors and also along the grain boundaries.
It can be suggested that the occurrence of coarse α-Zr grains in the central part at room temperature (Fig. 4b,c) may be related to coarse β-Zr grains at the creep temperature of 900°C.
However, after creep testing hydrides and Zr-Nb phase were formed mainly along grain boundaries.

Directionally solidified (DS) superalloys, which have elongated large grains, are used for gas-turbine blades.
Since the grain size is not small enough in comparison with the crack size observed often in a real component, the inhomogeneous microstructure due to the aligned grains may strongly affect the crack propagation property.
Since the grains are not sufficiently small in comparison with the crack size to be evaluated, the microstructural inhomogeneity due to the anisotroy of each grain [7, 8] affects the crack propagation [9, 10].
The elastic modulus at any angle can be calculated by average of each grain assuming that the grain orientation is random in the transversal plane to the DS axis.
The overall number of cycles is about the same order of experimental fatigue life (Fig. 5).

For a PZT capacitor of 100 nm lateral extension the approximate number of electrons only amounts to 5000.
Figure 2 shows embedded PTO grains before and after polishing.
Fig. 2 As-embedded PTO grains (left) and PTO grains in HSQ after a 1:30 min polishing time (right).
This also applies to small grains.
Essentially, these two effects (in-plane enhancement on the top and bottom of the grain, out-ofplane enhancement on the left and right side of the grain) depend on the slope of the grain.

It was established that it is the combined action of Sc and Zr that brings about the considerable grain refinement [1,2].
The grain structures of as-cast, homogenized and compression-tested samples were examined using optical microscopy.
Figure 1(b) reveals that the refined as-cast grain structure of the Scbearing alloy is retained after homogenization [8], and it is due to the pinning of grain boundaries by numerous, fine Al3ScxZr1-x dispersoids that form in the alloy during homogenization.
The very considerable reduction in the number density of the phase particles with temperature may be noted.
Further, compared to the base alloy, the number density of the phase particles formed in the Sc-bearing alloy at 300o C is considerably higher.

This indicates that the contents mainly consist of the broken pieces of the grains on the grinding wheel.
Fig.6 Comparison of ground surface profile between with or without micro-bubble dissolution As shown in the figure, after dissolving the micro-bubbles in the coolant, the number of bright spots is reduced, that is, the density of the grain fragments clearly decreases.
In an initial condition, fine grain fragments are included in the coolant and circulate with the coolant flow.
When a bubble contacts a grain fragment, it absorbs the fragment.
Finally, the surface of the coolant tank is wholly covered by the bubbles absorbing the grain fragments.

Two organizations are not formed slender recrystallization grain.
Page Numbers.
Do not number your paper: Tables.
The equations have to be numbered sequentially, and the number put in parentheses at the right-hand edge of the text.
Punctuation appears after the equation but before the equation number, e.g.

Poly-resistor formation with 12 and 21 number of squares shows the total average resistance of 303.52 Ω and 210.14 Ω respectively.
The overall experiments were conducted by deposition, doping and annealing to obtain uniform poly-silicon grains [12].
The diffusivity of the boron in the polysilicon grain and boundaries is measured by four-point probe and semiconductor parametric analyzer (SPA).
Varying depth also can be reached by changing a number of parameters in laser micromachining.
Comparing with conventional method, the resistor fabrication needs a number of masks and chemical solutions to produce the patterns.

The resultant system has a layered structure, comprising nanometric grains (less than 100 nm) at the top and a strain hardened transition layer in the subsurface.
These type of steels are used in a large number of industrial applications, among which are the food processing industry, the automotive valves manufacture, some surgical implants.
One of the well-known surface hardening is the grain refinement.
A large number of hardened steel shot with a diameter of 3 mm were placed at the bottom of a cylinder shaped chamber.
The grain sizes ranged from 10 to 50nm.

Boride particles can prevent grains from growing rapidly during heat treatment in the single α phase field through pinning grain boundaries [5].
Discontinuous coarsening occurs at lamellar grain boundaries in the boron-free 4800 alloy (Fig.4(a)) soaked for 4h, whereas it is suppressed in the boron modified 4808 alloy due to pinning of borides on grain boundaries.
However, many new γ grains nucleate at grain boundaries and TiB2/matrix interfaces as indicated by arrows in Fig.4(b).
The near γ microstructure in 4800 alloy is very inhomogeneous, which contains many elongated large grains formed by discontinuous coarsening at grain boundaries.
The irregularly distributed feathery and Widmastätten colonies destroy the integrity of the lamellar structure and result in a large number of interfacial faults, such as interfacial ledges, edges of terminated lamellae and curved interfaces [12], which play a key role in initiating instability of the lamellar microstructure.