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Table 1 provides the composition analysis results of zones marked by numbers in Fig. 2.
Fig.2 Microstructure and elements distribution of beginning part of the modified layer Fig.3 Microstructure and elements distribution of ending part of modified layer Table 1 Analysis results of zones marked by numbers in Fig.2 0.0 0.1 0.2 0.3 0.4 0.5 0.6 60 80 100 120 140 160 180 200 220 substrate modification layer Microhardness / HV0.05 Distance from surface / um Fig.4 Microhardness distribution of the depth along the modified layer Microhardness.
In the melting zone of substrate, the refined grain size due to rapid melting and solidification brings the hardness up to 130 HV0.05.
Composition [wt.%] Marked numbers Mg Al 1 2.33 97.67 2 41.40 58.60 3 56.36 43.64 4 74.91 25.09 5 89.70 10.30 6 92.63 7.37 Corrosion Resistance.

The ratio of the attached and proliferated cell numbers to the cultured cell numbers was defined as the cell attachment rate and the cell proliferation rate, respectively. 2.4 characterizations.
Fig.2 SEM morphologies of CHA reacted with SBF for different times (a)3 days; (b)6 days;(c) 12 days;(d) 24 days After immersion for 3 days, although there was no obvious mineralized layer on the surface of sample CHA, the grain boundaries became blurred, attributable to the dissolution of sample(Fig 2.a); after immersion for 6 days, the HCA crystals of low crystallinity with the size of 30 ~ 40nm were precipitated in the sample surface and distributed relatively evenly (Fig 2.b); thereafter, the material surface was covered by the leaf-like HCA with the length of 150-200nm (Fig 2.c); HCA layer continued to grow with the increase of the reaction time.
On the other hand, the initial attachment of cells was higher on CHA than on HA and that cell number did not differ in long-term culture (Fig 4.b), indicating the poor affinity of the HA surface for cells induced a delay in the initial cell attachment rather than a change in cell growth or differentiation.

The core of this heat exchanger is porous structure with a number of brazed joints [3].
A number of creep damage models of CCG have been proposed to predict the CCG in standard specimen.
The crack growth length was calculated by the numbers of damaged regular elements.
When many cavities have reached a critical size, they will coalesce to form micro-cracks along grain boundaries.

The phenomenon responsible for improved wear resistance in HSS cutting tools is the combined effect of increased number of η phase particles.
Analysis of the microstructure of HSS profile cutter shows that cryogenic treatment significantly alters the microstructure of these cutters, causing more finely and packed grains due to high bonding resulting higher wear resistance.
Care should taken while multiple tempering on the cutting tools as double tempering at 200 0C for 4hrs each resulted in the drop of hardness, hence it can be stated that excess number of tempering may soften the cutter by sacrificing hardness resulting in wear of the cutter at a faster rate.
[3] Susheel Kalia, Cryogenic Processing: A Study of Materials at Low Temperatures Low Temp Phys (2010) Volume 158: Numbers 5-6, 934–945 DOI10.1007/s10909-009-0058-x

The cutting inserts were a fine grained WC-6% Co substrate coated with 3.0 to 3.5 μm thick PVD-TiAlN (KC5010) with ISO tool designations CNMG 120408FW and multi radii (wiper) geometry adjacent to the designated 0.8mm nose radius.
The cutting time was calculated by means of the numbers of the cutting passes.
Surface RoughnessMeasurement.The surface roughness of the workpiecewas measured using Mitutoyo, type: SJ-301device.Signals obtained from the unit are transferred to an analysis for displaying or printing the result.Cut-off length and number of observations for each pass measurement were0.8 mm and 3 respectively.
Acknowledgement The authors wish to thank the Ministry of Higher Education (MOHE),UniversitiTeknologi Malaysia (UTM) and Research Management Center,UTM for the financial support to this work through the Long TermResearch Grant Scheme (LRGS) funding number 4L804.

This large number of components results mainly from the limited deformation capacity of sheet metal, thus requiring the complex structure of the chassis to be subdivided into a large number of components.
There is a motivation at present to develop a vehicle structure such that the chassis consists of only a small number of components of complex shape.
Preconditions for the use of super-plastic forming include [3]: – Fine, equiaxial grains with a size ≤ 10μm – A highly stable structure and resistance to pore formation – Precise control of temperature and forming speed during the process.

SiC grinding papers of grain size from #180 to #2000 were used to preparation of the metallographic specimen.
Individual phases and numbered sites of the analysis are marked in the Fig. 9.
By reducing of number of the Si particles, their influence is reduced.
On the other hand number of possible initiation centres such as intermetallic phases and the porosity can increase.

The deformation twins generate in the process of austenitic stainless steel tensiles at room temperature, their numbers increase with the increasing of the strain [5, 6].
In Fig.6 (b), (c) there are the α- martensite induced by strain indicated by the arrow, and the sheet organizations grow along the grain boundary to intracrystalline, formed in the twins crystal[4].
As shown in Fig.5 (b), part of the grid ε-martensites exist and a large number of α-lath martensite can be found, which is the intermediate phase form γ austenite deformation to the α-martensite.
The ε-martensite was the middle phase of γ → α-martensite transformation, and in the same method of cold working, the greater the cold deformation is, the larger the number of deformation twins and the martensite phase are.

However, the in situ reinforcement particles are coarse in size and sharp in circumference, meanwhile exist a large number of needle-like silicon phases.
A number of technological approaches have been proposed to address these problems[10-12].
When the melt is solidified, the α-Al come from eutectic α-Al+Al3Y become crystallization nuclei, which play the role of grain refinements[13].
Secondly, yttrium can form rare earth oxide solid particle with oxides in the melt, as the heterogeneous nucleation base of α-Al, part of them can promote a large number of α-Al nucleation, thus the alloy matrix is refined.

The secondary particles control the grain size during extrusion and rolling.
In a multiphase problem the phase-field variables, { }iφ , are connected by the constraint (no porosity is assumed) ( ) 1 , 1 N i i x tφ = =∑ r , (1) where N represents the number of involved phases.
For a multicomponent system the driving force for a phase transformation per mole of phase j is given by ( ) ( )1 m k k k k ij j j j i i k f c c cµ = = −∑D , (4) where jf is the molar Gibbs free energy of phase j, m is the number of components, kic is mole fraction of component k in phase i and kiµ is the chemical potential of the component k in the phase i.
The total number of computational nodes is 1150.