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Meanwhile, the (111) peak of the sputtered Al is higher than evaporated Al due to the crystallite size of sputtered Al (42.4 nm) are larger than evaporated Al (34.1 nm).
Fig. 2: XRD spectra for (a) Sputtered Al, (b) Evaporated Al, (c) AuNPs formed on sputtered Al and (d) AuNPs formed on evaporated Al.
El-Sayed, Gold nanoparticles: optical properties and implementations in cancer diagnosis and photothermal therapy.
El. (2015) 1
El. 25 (2014) 2227.

Maryamova, et al.: Sensors and Actuators A.Physical.
Lavitska, et al. in: Perspectives, Science and Technologies for Novel Silicon on Insulator Devices, edited by P.L.F.Hemment et al., Kluwer Acad.
Balestra et al., Kluwer Acad.
Flandre et al., Dordrecht: Kluwer Academic Publishers. (2005), p. 297
Shklovskii, A.L.

Hu.et al. [4] found that the single crystal Ni52.6Mn23.1Ga24.3 has a considerable magnetic-entropy change, 18J/kgK, in a field of 5T at the martensitic transition.
But O.Tegus.et al. [5] research on single crystal Ni53Mn22Ga25 shows that the magnetic-change is only modest, by far not as large as value of Ni52.6Mn23.1Ga24.3.
X-ray diffraction pattern of Ni54.9Mn20.5Ga24.6 at room temperature 0. 0 0. 5 1. 0 1. 5 2. 0 0 10 20 30 40 50 60 Moment(emu/g) µ0H(T) f i el d i ncr easi ng f i el d decr easi ng Fig.2.Magnetization isotherms of Ni54.9Mn20.5Ga24.6 on field increase and decrease at room temperature The AC-susceptibilities of the experimental alloy are shown in the Fig.3.
The width of temperature hysteresis is about 10K defined from the AC-susceptibilities curve. 280 290 300 310 320 330 340 350 360 370 200 400 600 800 1000 1200 1400 1600 1800 2000 2200 AC- s us c ept i bi l i t i es Temper at ur e( K) Dur i ng heat i ng Dur i ng cool i ng Fig.3.Temperature dependence of AC-susceptibility for Ni54.9Mn20.5Ga24.6 on heating and cooling 320 330 340 350 360 0 2 4 6 8 10 Moment(emu/g) Temperature(K) heat i ng cool i ng Fig.4.Temperature dependence of the magnetization of Ni54.9Mn20.5Ga24.6 in field of 0.05T 0.0 0.5 1.0 1.5 2.0 2.5 0 10 20 30 40 50 60 T=318K T=323K T=327K T=331K T=335K T=337K T=339K T=341K T=343K T=345K T=348K T=352K T=357K T=361K Moment(emu/g) μ 0H( T) 0.0 0.5 1.0 1.5 2.0 0 10 20 30 40 50 T=348K T=345K T=343K T=341K T=339K Moment(emu/g) µ0H(T) f i el d i ncr easi ng f i el d decr easi ng Fig.5.Magnetization isotherms of Ni54.9Mn20.5Ga24.6
Materials Science and Engineering A342 (2003) 231-235 [8] D.A.Filippov et al.Journal of Magnetism and Magnetic Materials 258-259(2003) 507-509

In transition metals, the influence of temperature on the vacancy parameters has been partially studied in the case of Ta [22] and W [23] by taking into account the electronic contribution to the vacancy formation (Sf el ) and migration (Sm el ) entropy.
The approximate linear temperature dependence of Sm el and Sf el leads to a quadratic temperature dependence of Hm el and Hf el (the corresponding enthalpy values), which however falls short to explain the temperature dependence of the activation energy in tungsten.
This has been confirmed by calculations performed in Al [28].
Concerning the vacancy migration energy in Fe, disparate experimental results have been published: Schaefer et al. [52] reported a value of 1.28 eV, while Vehanen et al. [53] found 0.55 eV.
In the absence of B impurities, thermal vacancies are stabilized by Al antisites in Al-rich alloys.

Compared with Al and steel, however, their high-cost limits their wide applications, especially in civil.
Many researches on the semi-solid deformation behaviors of Al, Mg and steel have been carried out by scientists and engineers all over the world and many useful results have been obtained.
Ti14 alloy, being a Ti-Al-Cu-Si system (with Cu content greater than 10wt.%), is α and Ti2Cu type alloy [8~9].
Table 2 Tensile properties at RT of Ti14 alloy bar after heat treatment Forging way UTS/ΜΡa ∆UTS/% YS/ΜΡa ∆YS/% El/% ∆El% RA/% ∆RA% Semi-solid 843 +16 694 +19 13 -38 18 -56 Conventional 727 -- 585 -- 21 -- 41 -- Comparison with the values before and after heat treatment, the strength after heat treatment decreases and the plasticity increases greatly, that is, the elongation increases from 6.8% to 13%, which increases by 48%, and the reduction in area increases from 12% to 18%, which increases by 33%.
Bania: Beta Titanium Alloys in the year 1990s, TMS Publish, 1993, p.3 [4] Y.Q.Zhao, K.Y.Zhu et al: Chinese Patent, Application No.02101189.3 [5]Y.Q.Zhao, K.Y.Zhu et al: Chinese Patent, Application No.02101190.7 [6] Hirowo G.

Table 1 Chemical composition and measured Ac1, Ac3 and Ms of steel tube (mass / %) C Si Mn P S Al Nb Ti Ac1 (°C) Ac3 (°C) Ms (°C) 0.15 1.34 1.44 0.009 0.004 0.04 0.029 0.024 736 887 405 Experimental Results Microstructure.
Sample B exhibited a highest n-value of 0.23 and EL of 35.5%.
Sample A and B exhibit better mechanical properties since they show higher value of UTSEL products due to their higher EL.
This retained austenite do not transform to martensite even at high strains leading to the low EL and poor hydroformability.
However, sample C, with IBT holding time of 10min, shows a little lower UTS and EL.

Effect of Texture and Microstructure on Ductility of a Mg-Al-Ca Alloy Processed by Equal Channel Angular Pressing V.N.
Texture and microstructure formation during equal channel angular pressing (ECAP) of Mg-0.49%Al-0.47%Ca alloy were studied.
Material, Experimental Procedures and Calculations As-received Mg-0.49%Al-0.47% Ca alloy was in the form of a bar obtained by extrusion at 340ºC with the total diameter reduction of ~ 4.4.
Mechanical properties of the alloy before and after ECAP (YS = yield strength; UTS = ultimate tensile strength; EL = elongation to failure) N Process conditions Uniaxial tensile test temperature, ˚C YS, MPa UTS, MPa EL,% 20 190 245 8 1 Before ECAP 160 115 160 20 20 180 220 12 2 After ECAP 160 125 135 25 The improvement of tensile ductility of the investigated alloy by ECAP, especially of room temperature ductility, is the consequence of microstructure refinement and the change in the texture.
Volume fractions, Schmid factor values and CRSS for the slip systems calculated for the different texture components of the alloy before and after ECAP mij τiCRSS/τ1CRSS Test temperature 20˚C Test temperature 160˚C j Texture components fj i=1 i=2 i=3 i=4 i=1 i=2 i=3 i=4 i=1 i=2 i=3 i=4 1 <1010>// ED(X-axis) 0.67 0 0.29 0.25 0.22 1 ]1473)[1374( −− − 0.09 0.1 0.31 0.27 0.22 2 ]1242)[1465( −−− − 0.11 0.17 0.4 0.28 0.18 3 ]0615)[5398( − − 0.17 0 0.33 0.29 0.22 4 ]1440)[4374( − −− 0.15 0.13 0.27 0.24 0.2 5 ]1101)[5123( −−−− 0.11 0.43 0.15 0.14 0.2 1 5 5 6.5 1 2.5 2.5 3.5 Summary Processing of alloy Mg-0.49%Al-0.47%Ca by ECAP was shown to result in a significant enhancement of its tensile ductility both at room temperature and at an elevated temperature.

The precision of position determination is less than 2.5 o el. in steady-state operation in spite of virtual sensorless method.
Actual and estimated position in °el. a), error of position b) using ATO Conclusion A speed/position servosystem with 2-phase electrical induction/synchronous motor for robotic applications was introduced and presented.
The precision of position determination is less than 2.5 o el. in steady-state operation (see Fig. 8) in spite of virtual sensorless method.
Blaabjerg et al.: Evaluation of Low-Cost Topologies for Two-Phase IM Drives in Industrial Application, In: Record of 37th IEEE IAS Annual Meeting on Industry Application, 2002, vol. 4, pp. 2358 - 2365, ISSN 0197-2618

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Yi et al. [33] investigated progressive collapse behavior of RC frame through testing a three-story one-third scale model in Hunan University.
[12] Alashker, Y. and El-Taiwl, S. (2011).
K., El-Tawil, S. and Lew, H.
P., and El-Tawil, S. (2010).
[71] Li, H. and El-Tawil, S. (2012).