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Detection Method for Mycotoxin Exists In Grain Ruili-Pei 1,a, Jiapeng-Liu 2,b and Ying-Wang 2,c 1 Hebei Province Grain and Oil Quality Testing Center, China 2 Beijing Huaan Maico Biological Technology Co., Ltd., China a lpx13273101336@163.com Keywords: Mycotoxin, Detection Method, Grain Abstract.
In this paper, the harm of mycotoxin for grain was analyzed.
Up to now, the number of AFT that had been identified reached more than 20 kinds.
In recent years, the China’s grain yield is maintained in one trillion jins or so, if the un-edible amount of grain whose mycotoxins exceed the standard fixed at 1% , the annual grain loss will about ten billion jins.
Enzyme-linked immunosorbent assay and chemiluminescence in immunological assay have higher sensitivity and specificity, and are suitable for small and medium-sized laboratory to detect a large number of samples.

It is known that curved and poorly defined grain boundaries of the ARB processed alloy become sharp and stable as the number of ARB cycle increases.
As the number of ARB cycle increased, dislocation cells disappeared and equiaxed ultra-fine grains appeared.
The yield stress and tensile strength vary similarly with the number of ARB cycles.
However, the gap increases as the ARB cycle number increases, which points out that grain boundaries become equilibrated and grain boundary strengthening operates with the cycles.
Wear rate vs. number of ARB cycles for commercial purity 1100 Al. 0 1 2 3 4 5 6 7 5 10 15 20 25 30 Wear Rate (1x10 -13 m 3 /m) Number of Cycle Applied Load: 0.5N Applied Load: 1 N

Grain growth controlled by particles able to move together with grain boundaries is investigated by means of numerical simulation.
Introduction Particle-controlled grain growth is usually associated with the grain boundary (GB) pinning by immobile particles [1].
Unfortunately, there was not taken into account that a moving GB sweeps out particles from the traversed volume, which increases the particle number on the GB above that corresponding to their random spatial distribution.
As nA= nV/SV (nV is the number of particles per unit volume, SV=3/D the specific boundary area in 3D microstructure [7], and D the current mean grain diameter), nA= nVD/3 = fD/(4πr3)
Particles on Grain Boundaries.

However, if thermodynamic stabilization can be attained by reducing the grain boundary energy by segregation of solute atoms, a number of models [7-11] have predicted that a metastable equilibrium grain size can exist in alloy systems due to solute segregation to grain boundaries.
Grain growth in nanocrystalline Pd-19 at.% Zr.
Grain growth in nanocrystalline Fe and Fe – 4at.% Zr.
At 500oC some abnormal grain growth is observed with a few ~ 1 mm grains observed.
National Science Foundation under grant number DMR-0504286.

Statistical Aspects of Grain Coarsening in a Fine Grained Al-Sc Alloy M.
The pre-aged samples were annealed for up to 10 h at temperatures of 400, 450 and 500 °C with a limited number of experiments carried out at 550 °C.
To determine each grain size distribution, ~ 1000 grains were measured using AnalySIS Pro v3.0 software (Soft Imaging System GmbH).
Annealing at 500 °C resulted in rapid grain coarsening and a more pronounced a broadening of the grain size distribution.
A number of theoretical and empirical continuous probability distributions have been compared with experimental data in an attempt to gain a more fundamental understanding of normal subgrain/grain growth processes [2].

New experimental data related to the grain size and the Bauschinger effects have been obtained for ferritic steels with grain size in the range of 3.5-22µm.
The consequences are discussed for fine grain metallic alloys.
As the back-stress σb is assumed to be mainly due the dislocation pile-ups against the grain boundaries, it can be expressed in a simple form as : b M b n D µ σ = , (5) where D is the grain size and n the mean number of the dislocations in a pile-up.
The ratio λ/b gives the number of dislocations per slip band geometrically necessary to provide the deformation and the corrective term (1-n/n0) accounts for the finite number of sites available for dislocations at the grain boundary.
Conclusion New experimental data related to the effect of grain size and the Bauschinger effect have been obtained for ferritic steels with grain size in the range of 3.5-22µm.

This paper focuses on contact pressure between grain and workpiece.
Fig.1 Structure mode Every contact cell includes several KEPYOPTS, and recommends default to fit a great number of contact problems.
In order to simulate the normal force of grains on die surface, the indentation of a symmetric, cone-shape grain with the rough surface is used as the model of the single-grain polishing.
ABC section presents the axial plane of the cone-shape grain with the cone angle 2γ; h is the depth of the grain in the workpiece. there exists a rigid region HBDGH.
Since all acting grains are not on the same plane of the polishing disk, when the force is small, the total number of acting grains is less, and the depth is larger.

Others have an impact on the tungsten performance in the first wall, e.g. its high ductile-brittle transition temperature (DBTT), high atomic number (high radiation loss from fusion plasma via impurities) and significant degradation of properties with grain growth [7,8].
In the fine-grained material, He and H ions tend to accumulate at the grain boundaries, thus limiting the development of bubbles within the grains.
Particle size of the initial powder was decreased from median value of 1.2 mm prior to milling (number distribution of the particle sizes in the measured powder) to median value around 250 nm after milling and the overall span of the distribution decreased from 0.43-3.91 mm prior to milling to 0.16-0.52 mm (representing Dn (10) – Dn (90) of the number distribution) after milling.
The particle size distribution of the powders before and after milling; number distribution was chosen to depict the effectivity of the milling process.
Powder milling including powder particle/grain refinement and introduction of higher density of crystal lattice defects and strain caused increase in the hardness number by more than 100 HV1 (compare W0 and WM sample).

The development of the microstructure during grain growth is caused both by the change of average grain size and, what is of concern for crystallographic texture evolution, by the change of the grains' orientation and misorientations distribution in the grain structure.
The direction of p remains the same Journal Title and Volume Number (to be inserted by the publisher) 3 when the sense of the field is reversed.
The freedom to change the magnitude of the driving force for boundary migration by exposing the samples to magnetic fields of different strength yields the unique opportunity to change the dri- Journal Title and Volume Number (to be inserted by the publisher) 5 ving force on a specific grain boundary and thus, to obtain the driving force dependence of grain boundary velocity (Fig. 3).
For a comparison, the reduced mobility of the curved 86° 1010< > tilt boundary σ⋅= mA at 673 Journal Title and Volume Number (to be inserted by the publisher) 7 K in a Zn bicrystal was measured to be K673 ZnA =3.2⋅10 -8 m2/s [28] yielding an absolute mobility (assuming σ∼0.46 J/m2) of K673 Znm ≅7.0⋅10-8 m4/J⋅s.
In contrast, the same heat Journal Title and Volume Number (to be inserted by the publisher) 9 treatment in the same magnetic field results in a distinct difference between usually symmetrical texture peaks when the sample is tilted by +30° or -30° to the field direction around the rolling direction leading to a configuration where the c-axis of grains corresponding to one texture component is aligned normal to the field direction.

The most notable property of grain boundary engineered materials is the increased number of special boundaries in the material [2].
The CSL theory designates the misorientation based on the inverse of the number of overlapping lattice sites [3].
To characterize the connectivity, triple junctions are classified based on the number of special versus the number of random boundaries at the junction.
However, after a certain number of cycles or too large a strain, the special boundary fraction actually begins to decrease [9].
Acknowledgements The work was supported primarily by a Materials World Network grant from the National Science Foundation under the Award Number DMR-1107896.