Sort by:
Publication Type:
Open access:
Publication Date:
Periodicals:
Search results
Online since: April 2022
Authors: Khaled Abou-El-Hossein, Peter Babatunde Odedeyi
Otieno and Abou-El-Hossein [23] also worked on another aluminum alloy (RSA 905).
[6] Santos, M.C., et al., Machining of aluminum alloys: a review.
[11] Lin, K., et al., Effect of tool nose radius and tool wear on residual stresses distribution while turning in situ TiB 2/7050 Al metal matrix composites.
Abou-El-Hossein.
[22] Otieno, T., et al.
[6] Santos, M.C., et al., Machining of aluminum alloys: a review.
[11] Lin, K., et al., Effect of tool nose radius and tool wear on residual stresses distribution while turning in situ TiB 2/7050 Al metal matrix composites.
Abou-El-Hossein.
[22] Otieno, T., et al.
Online since: September 2018
Authors: Akeel M. Kadim, Karrar A. Hammoodi, Ghufran S. Salih
In three-layer device an extra layer, (EL) is located between (HTL) and (ETL).
Electrical Measurements The I-V characteristics of the hybrid QDOLEDs achieved by the ITO/PEDOT: PMMA/QDs/Alq3/Al and ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
(a) Fig. 5: I-V forward characteristics of the hybrid OLEDs devices: (a) ITO/PEDOT:PMMA/QDs/Alq3/Al and (b) ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
Electroluminescence Measurements The EL measurements in fig.7 were approved out using a photomultiplier detector at room temperature, and the lower limit of voltages for white light which has been achieved experimentally from fig.4 which are 6V for PEDOT:PMMA/0.1%wt QDs/Alq3 and 4V of PEDOT:PMMA/0.1%wtQDs/Alq3/TPBi hybrid organic light emission devices respectively. 540 nm 460 nm 610 nm 540 nm 440 nm 610 nm a)) b)) Fig. 7: EL spectrum of hybrid OLEDs devices: (a) ITO/PEDOT:PMMA/QDs/Alq3/Al and (b) ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
Table 1: EL coordinates for hybrid organic light emitting devices.
Electrical Measurements The I-V characteristics of the hybrid QDOLEDs achieved by the ITO/PEDOT: PMMA/QDs/Alq3/Al and ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
(a) Fig. 5: I-V forward characteristics of the hybrid OLEDs devices: (a) ITO/PEDOT:PMMA/QDs/Alq3/Al and (b) ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
Electroluminescence Measurements The EL measurements in fig.7 were approved out using a photomultiplier detector at room temperature, and the lower limit of voltages for white light which has been achieved experimentally from fig.4 which are 6V for PEDOT:PMMA/0.1%wt QDs/Alq3 and 4V of PEDOT:PMMA/0.1%wtQDs/Alq3/TPBi hybrid organic light emission devices respectively. 540 nm 460 nm 610 nm 540 nm 440 nm 610 nm a)) b)) Fig. 7: EL spectrum of hybrid OLEDs devices: (a) ITO/PEDOT:PMMA/QDs/Alq3/Al and (b) ITO/PEDOT:PMMA/QDs/Alq3/TPBi/Al.
Table 1: EL coordinates for hybrid organic light emitting devices.
Online since: January 2012
Authors: Shi Ming Shen, Su Min Zhou, Wei Huang
It is an Al and Mg rich silicate having the structural composition: Mg5Si8O20(OH)2(OH2)4·4H2O [1].
MFPs were subjected to activation before EL plating.
Zhao, et al.: Adsorption of Pb (II) on palygorskite from aqueous solution: Effects of pH, ionic strength and temperature, Appl.
Gacsi et al.: The electroless deposition of nickel on SiC particles for aluminum matrix composites, Surf, Coat.
Zhou et al.: Fabrication of Ni-P/ Palygorskite Core-shell Linear Powder via Electroless Deposition, App.
MFPs were subjected to activation before EL plating.
Zhao, et al.: Adsorption of Pb (II) on palygorskite from aqueous solution: Effects of pH, ionic strength and temperature, Appl.
Gacsi et al.: The electroless deposition of nickel on SiC particles for aluminum matrix composites, Surf, Coat.
Zhou et al.: Fabrication of Ni-P/ Palygorskite Core-shell Linear Powder via Electroless Deposition, App.
Online since: November 2007
Authors: Helga Füredi-Milhofer, X. Ba, Y. Meng, Y. Huang, S.Y. Kwak, S. Ge, Y. Qin, E. DiMasi, N. Pernodet, Miriam Rafailovich
Crystals on the COL fibers were aligned closely to the perimeter of the fibers
)1(
COL EL
FN-EL
FN
and their size after 12 hours of exposure was comparable to crystals grown on the FN-EL fibers after 48
hours of exposure.
EL can not template the big crystal after 48 hours although the relative modulus of EL fibers increased in the early stage of mineralization.
Kwak, et al. (2006) Proc Natl Acad Sci USA 103 (40):14672-77
Sokolov, et al. (2003) J Biomed Mater Res 64: 684-92 [4] Y.
Rafailovich, et al. (2003) Polymer 44 (11):3327-32. 0 1 2 3 4 5 1.0 1.1 1.2 1.3 1.4 1.5 Accumulated Incubation time (hr) Average Relative Modulus 0 1 2 3 4 5 0.85 0.90 0.95 1.00 1.05 1.10 1.15 Average Fiber Height (µµµµm) Accumulated Incubation time (hr) El El-Fn Fn 0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6 20% 39% 10% Average Fiber Height (µµµµm) 0hr-mineralization 2hr-mineralization El El-Fn Fn 0 1 2 3 4 5 6 56% 69% 9% Average Relative Modulus 0hr-mineralization 2hr-mineralization (A) (B) ) (C) (D)
EL can not template the big crystal after 48 hours although the relative modulus of EL fibers increased in the early stage of mineralization.
Kwak, et al. (2006) Proc Natl Acad Sci USA 103 (40):14672-77
Sokolov, et al. (2003) J Biomed Mater Res 64: 684-92 [4] Y.
Rafailovich, et al. (2003) Polymer 44 (11):3327-32. 0 1 2 3 4 5 1.0 1.1 1.2 1.3 1.4 1.5 Accumulated Incubation time (hr) Average Relative Modulus 0 1 2 3 4 5 0.85 0.90 0.95 1.00 1.05 1.10 1.15 Average Fiber Height (µµµµm) Accumulated Incubation time (hr) El El-Fn Fn 0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6 20% 39% 10% Average Fiber Height (µµµµm) 0hr-mineralization 2hr-mineralization El El-Fn Fn 0 1 2 3 4 5 6 56% 69% 9% Average Relative Modulus 0hr-mineralization 2hr-mineralization (A) (B) ) (C) (D)
Online since: June 2008
Authors: Yuri Estrin, Mikhail V. Popov, V.N. Timofeev, Rimma Lapovok, L.L. Rokhlin, Tatiana V. Dobatkina, N.I. Nikitina, Sergey V. Dobatkin
Structure and Properties of Mg-Al-Ca Alloy
after Severe Plastic Deformation
S.V.
TEM micrographs showing the microstructure of the Mg-Al-Ca alloy after ECAP: a) at 300°C; b) at 220°C with back pressure. 1µm 1µm 1 10 100 Aging time, h 5 6 7 8 Specific electrical resistance, mcOm*cm 0 1 23 1 10 100 Aging time, h 500 600 700 800 900 Microhardness, MPa 0 1 2 3 Specific electrical resistance µΩm*cm (relative elongation, EL) by a factor of 2 and 3, respectively.
ECAP of the extruded Mg-Al-Ca alloy further increased strength and ductility, especially after aging (YS = 190 MPa, EL = 12%).
Mechanical properties (a-YS; b-EL) of Mg-0.49%Al-0.47%Ca alloy at Ttesting = 20 o C and 160 oC (shaded) after different treatments: 1 - annealing; 2 - quenching; 3 - annealing + ECAP at 300 o C; 4 - quenching + ECAP at 300 o C; 5 - extrusion + ECAP at 300 o C.
ECAP of the extruded Mg-Al-Ca alloy further increases strength and ductility, especially after aging (YS = 190 MPa, EL = 12%).
TEM micrographs showing the microstructure of the Mg-Al-Ca alloy after ECAP: a) at 300°C; b) at 220°C with back pressure. 1µm 1µm 1 10 100 Aging time, h 5 6 7 8 Specific electrical resistance, mcOm*cm 0 1 23 1 10 100 Aging time, h 500 600 700 800 900 Microhardness, MPa 0 1 2 3 Specific electrical resistance µΩm*cm (relative elongation, EL) by a factor of 2 and 3, respectively.
ECAP of the extruded Mg-Al-Ca alloy further increased strength and ductility, especially after aging (YS = 190 MPa, EL = 12%).
Mechanical properties (a-YS; b-EL) of Mg-0.49%Al-0.47%Ca alloy at Ttesting = 20 o C and 160 oC (shaded) after different treatments: 1 - annealing; 2 - quenching; 3 - annealing + ECAP at 300 o C; 4 - quenching + ECAP at 300 o C; 5 - extrusion + ECAP at 300 o C.
ECAP of the extruded Mg-Al-Ca alloy further increases strength and ductility, especially after aging (YS = 190 MPa, EL = 12%).
Online since: May 2006
Authors: José A. Rodríguez, José M. Gallardo, Enrique J. Herrera
Green relative density (Dg), green hardness (Hg), green rupture strength (Rs), sintered
relative density (Ds), degree of shrinkage (Σ), as-sintered hardness (Hs), ultimate tensile
strength (UTS) and elongation (EL) of the compacts.
Green compacts Sintered compacts Material Dg % Hg HB Rs MPa Ds % ΣΣΣΣ % Hs HB UTS MPa EL % MA Al 91.6 104 33 94.9 -3.48 65 195 1.6 MA Al 10 92.9 100 39 95.6 -2.91 63 188 2.1 MA Al 20 94.0 96 43 96.0 -2.13 60 176 2.6 MA Al 30 95.1 86 44 96.5 -1.47 57 165 3.8 The density of both green and sintered compacts improves with the percentage of blended unmilled powder.
The elongation increases more than twice when 30% elemental aluminium is mixed in (EL = 3.8% vs. 1.6%).
MA Al MA Al + Al MA Al MA Al +Al Fig. 3.
Schematic model of the as-pressed (left) and as-sintered (right) MA Al and blend (MA Al + Al) compacts.
Green compacts Sintered compacts Material Dg % Hg HB Rs MPa Ds % ΣΣΣΣ % Hs HB UTS MPa EL % MA Al 91.6 104 33 94.9 -3.48 65 195 1.6 MA Al 10 92.9 100 39 95.6 -2.91 63 188 2.1 MA Al 20 94.0 96 43 96.0 -2.13 60 176 2.6 MA Al 30 95.1 86 44 96.5 -1.47 57 165 3.8 The density of both green and sintered compacts improves with the percentage of blended unmilled powder.
The elongation increases more than twice when 30% elemental aluminium is mixed in (EL = 3.8% vs. 1.6%).
MA Al MA Al + Al MA Al MA Al +Al Fig. 3.
Schematic model of the as-pressed (left) and as-sintered (right) MA Al and blend (MA Al + Al) compacts.
Online since: November 2015
Authors: Norainiza Saud, Nurul Razliana Abdul Razak, Nisrin Adli
Eric (2010) and El.
The increase from 1 wt% Al to 5 wt% Al caused the grain growth retard more.
El-Daly, F.
El-Tantawyb, A.
El-Mossalamy, and A.A.
The increase from 1 wt% Al to 5 wt% Al caused the grain growth retard more.
El-Daly, F.
El-Tantawyb, A.
El-Mossalamy, and A.A.
Online since: April 2014
Authors: Hui Shan Yang, Li Shuang Wu, Zhi Yue Huang
ITO
LiF/Al
5.8
3.0
3.0
6.3
3.2
5.8
5.4
2.4
5.1
2.0
m-MTDATA
DPVBi
NPB
Alq:QAD 0.5%
Alq
LiF/Al
Alq (50-x nm )
DPVBi (x nm)
Alq:QAD 0.5% 20nm
DCJTB(0.05 nm)
NPB (10 nm)
m-MTDATA (45 nm)
ITO
Fig.1.
Normalized EL intensity of the different devices A-D at different voltage Fig.5.
CIE coordinates of devices A-D at different voltage Fig. 3 shows the EL efficiency curves as a function of luminance for the devices.
The EL spectra and the CIE coordinates of the white light-emitting device are influenced by the each emissive layer and applied voltage.
Fig.4 shows the EL spectra of devices A-D at different applied voltages.
Normalized EL intensity of the different devices A-D at different voltage Fig.5.
CIE coordinates of devices A-D at different voltage Fig. 3 shows the EL efficiency curves as a function of luminance for the devices.
The EL spectra and the CIE coordinates of the white light-emitting device are influenced by the each emissive layer and applied voltage.
Fig.4 shows the EL spectra of devices A-D at different applied voltages.
Online since: December 2014
Authors: Xin Ping Mao, Ming Tu Ma, Guang Ying Li, Chang Xu Zhao
Most of the hot stamped components from 22MnB5 blanks possess high strength-ductility with TS×El product from 10 to 15 GPa%.
Most of the hot stamped components from 22MnB5 blanks possess strength-ductility with TS×El product from 10 to 15 GPa%.
For 20s of P-T treatment at 400 oC, the higher strength-ductility is obtained with TS=1500MPa, El=17% and TS×El=25.5GPa%, as shown in Fig.4 [11].
Wang X.D selected a middle carbon steel with 0.485C, 1.195Mn, 1.185Si, 0.98Ni, 0.21Nb to carry out P-T treating at.400oC and obtained an ultra high strength-ductility with TS³2000MPa, El³10% and TS×El³20GPa%, as shown in Fig.5[12].
For conventional low alloyed TRIP assisted steels and the later developed Q-P steels, their chemical compositions are usually based on the original concept proposed by Matsumura et al in the range of 0.12–0.55C, 0.2–2.5 Mn, 0.4–1.8 Si (wt.%).
Most of the hot stamped components from 22MnB5 blanks possess strength-ductility with TS×El product from 10 to 15 GPa%.
For 20s of P-T treatment at 400 oC, the higher strength-ductility is obtained with TS=1500MPa, El=17% and TS×El=25.5GPa%, as shown in Fig.4 [11].
Wang X.D selected a middle carbon steel with 0.485C, 1.195Mn, 1.185Si, 0.98Ni, 0.21Nb to carry out P-T treating at.400oC and obtained an ultra high strength-ductility with TS³2000MPa, El³10% and TS×El³20GPa%, as shown in Fig.5[12].
For conventional low alloyed TRIP assisted steels and the later developed Q-P steels, their chemical compositions are usually based on the original concept proposed by Matsumura et al in the range of 0.12–0.55C, 0.2–2.5 Mn, 0.4–1.8 Si (wt.%).
Online since: January 2005
Authors: Lian Zhou, Yong Qing Zhao
Table 3 High strength titanium alloys researched in China and their typical properties
alloy composition (w.t.%) UTS
(MPa)
Toughness
K1c (MPa M ) αk(J/cm
2
)
β21S Ti-15Mo-3Al-2.7Nb-0.2Si 1200 50
TC21 Ti-Al-Sn-Zr-Cr-Mo-(Nb-Ni-Si) 1100 70
Ti-B19 Ti-Al-Mo-V-Cr-Zr 1250 70
Ti-26 Ti-15-3+Zr+Nb 1250
Ti-B18 Ti-Al-Mo-Zr-Sn 1300 50
Ti-B20 Ti-Al-Mo-Zr-Sn-Fe 1300 50
Titanium composites.
HE130, a Ti-Al-V-Mo-Fe-B system alloy, is a α+β high elastic Ti alloy.
Ti811ZB, a Ti-Al-Mo-Zr-B system alloy, is a near α high elastic Ti alloy.
Table 7 High elastic Ti alloys being researched in China and their typical properties Designation UTS(MPa) El(%) E(GPa) Composition(w.t%) HE130 1000 6 130 Ti-Al-V-Mo-Fe-B Ti811ZB 1100 6 125 Ti-Al-Mo-Zr-B Low cost titanium alloys.
Table 8 Low cost Ti alloys being researched in China and their typical properties Tensile at RT Tensile at 4000 C UTS YS EL RA UTS YS EL RA Alloy MPa MPa % % MPa MPa % % Composition (w.t%) Ti8LC 1050 990 12 30 700 600 15 50 Ti-Al-Fe-Mo Ti12LC 1100 1050 12 40 900 800 15 50 Ti-Al-Mo-Fe Corrosion resistant titanium alloys.
HE130, a Ti-Al-V-Mo-Fe-B system alloy, is a α+β high elastic Ti alloy.
Ti811ZB, a Ti-Al-Mo-Zr-B system alloy, is a near α high elastic Ti alloy.
Table 7 High elastic Ti alloys being researched in China and their typical properties Designation UTS(MPa) El(%) E(GPa) Composition(w.t%) HE130 1000 6 130 Ti-Al-V-Mo-Fe-B Ti811ZB 1100 6 125 Ti-Al-Mo-Zr-B Low cost titanium alloys.
Table 8 Low cost Ti alloys being researched in China and their typical properties Tensile at RT Tensile at 4000 C UTS YS EL RA UTS YS EL RA Alloy MPa MPa % % MPa MPa % % Composition (w.t%) Ti8LC 1050 990 12 30 700 600 15 50 Ti-Al-Fe-Mo Ti12LC 1100 1050 12 40 900 800 15 50 Ti-Al-Mo-Fe Corrosion resistant titanium alloys.