scholarly journals Preparation of Fe-Al alloy layer on CLAM steel

2021 ◽  
Vol 70 (3) ◽  
pp. 036801-036801
Author(s):  
Wei Bing-Jun ◽  
◽  
Hu Li ◽  
Xiang Xin ◽  
Yang Fei-Long ◽  
...  
Keyword(s):  
Alloy Layer ◽  
Al Alloy ◽  
Clam Steel

scholarly journals Reaction between Iron and Solid Zinc through Thin Fe-Al Alloy Layer

2002 ◽  
Vol 88 (3) ◽  
pp. 136-141
Author(s):  
Yoshinori WAKAMATSU ◽  
Daisaku TOMITA ◽  
Yasushi KAJI ◽  
Masahiro YAMANE ◽  
Fumio NOGUCHI
Keyword(s):  
Alloy Layer ◽  
Al Alloy

Structure and Performance of Fe-Al Alloy Layer for Twin Wire Surfacing on the Steel Substrate

2013 ◽  
Vol 658 ◽  
pp. 158-164
Author(s):  
Jin Yu ◽  
Yin Zhuo Huang ◽  
Bo Wen Wu ◽  
Hou Xian Zhou
Keyword(s):  
Abrasion Resistance ◽  
Steel Substrate ◽  
Base Material ◽  
Performance Testing ◽  
Alloy Layer ◽  
Resistance Testing ◽  
Al Alloy ◽  
Welding Wire ◽  
Precipitated Phase ◽  
Welding Line

Surfacing of Fe-Al alloy layer is achieved on the surface of Q235 steel plate by using the twin wire consisting of one aluminum welding wire and one steel welding wire in the shielding of pure argon. When the ER1100 aluminum welding wire of Φ1.6mm and ER50-6 steel welding wire of Φ1.2mm are selected as the master wire and slave wire respectively, with preheating and interlayer temperature reaching 350°C by controlling filling volume of aluminum and steel , the Fe-Al alloy layer featured by well-formed welding line is thus gained with no macroscopic defect. As the mechanical performance testing shows, the shear strength of surface combining surfacing layer and steel substrate is higher than 270MPa. The rupture position is located in surfacing layer and it turns out to be brittle fracture; the micro-hardness of surfacing layer ranges from 320HV to 420HV. Abrasion resistance testing indicates that abrasion resistance of surfacing layer is better than that of base material. According to micro-structure observation, the welding line is a coarsening columnar structure with a great deal of precipitated phase. According to EDAX, the aluminum content of precipitated phase in surfacing layer ranges from 24% to 32% (at), and the steel content ranging from 76% to 68% (at) - it is thus considered a Fe3Al structure through XRD.

Characteristics of phase constitution in the Fe-Al alloy layer of calorized steel pipe

1995 ◽  
Vol 30 (10) ◽  
pp. 2635-2639 ◽  
Author(s):  
Li Yajiang ◽  
Zhang Yonglan ◽  
Liou Yuxian
Keyword(s):  
Alloy Layer ◽  
Steel Pipe ◽  
Al Alloy ◽  
Phase Constitution

scholarly journals Effects of Rolling Reduction and Strength of Composed Layers on Bond Strength of Pure Copper and Aluminium Alloy Clad Sheets Fabricated by Cold Roll Bonding

2014 ◽  
Vol 2014 ◽  
pp. 1-11 ◽  
Author(s):  
Yoji Miyajima ◽  
Kotaro Iguchi ◽  
Susumu Onaka ◽  
Masaharu Kato
Keyword(s):  
Shear Strength ◽  
Alloy Layer ◽  
Rolling Reduction ◽  
Al Alloy ◽  
Tensile Shear Strength ◽  
Tensile Shear ◽  
Shear Tests ◽  
Roll Bonding ◽  
Cold Roll ◽  
Cold Roll Bonding

Three types of clad sheets, Cu/Al, Cu/AA5052, and Cu/AA5083, were produced by cold roll bonding with the rolling reduction of 50% and 75%. Tensile shear tests which give tensile shear strength were performed in order to assess the bond strength. Scanning electron microscopy was performed on the fractured interface produced by the tensile shear tests, which suggests that the fracture occurs within the Al alloy layer. The tensile shear strengths considering the area fraction of deposit of Al alloy on Cu side were compared with the shear stress converting from the ultimate tensile strengths. As a result, the tensile shear strength of the clad sheets is attributed to the shear strength of Al alloy layer close to the well bonded interface. A simple model was proposed that explains the effects of the rolling reduction and area fraction of deposit of Al alloy.

Microstructure and Erosion Resistance of Hot-Dip-Aluminized 3Cr13 Steel

2013 ◽  
Vol 750-752 ◽  
pp. 2008-2011
Author(s):  
Zhi Gang Zhao ◽  
Xiu Lin Ji ◽  
Hai Shuai Wang ◽  
Shu Qi Wang
Keyword(s):  
Diffusion Process ◽  
Erosion Resistance ◽  
Alloy Layer ◽  
Ductile Material ◽  
Al Alloy ◽  
Erosion Behavior ◽  
Intermetallic Coating ◽  
Diffusion Temperature ◽  
Erosion Loss ◽  
And Diffusion

Fe-Al intermetallic coating was prepared on 3Cr13 steel by hot-dip aluminizing and diffusion process. The morphology and phase of the coating were analyzed; the erosion behavior of hot-dip-aluminized 3Cr13 steel was investigated. Results showed that the thickness of the coating increased with diffusion temperature, but decreased when diffusion temperature exceeded 800°C. The Fe-Al alloy layer diffused at 900°C presented compacted microstructure, and mainly contained FeAl and a few Fe3Al. Fe-Al intermetallic coating possessed obviously declined erosion loss compared with unaluminized 3Cr13 steel and represented typical erosion characteristics of ductile material.

A thermogravimetric study of the oxidative growth of Al2O3/Al alloy composites

1991 ◽  
Vol 6 (9) ◽  
pp. 1982-1995 ◽  
Author(s):  
K.C. Vlach ◽  
O. Salas ◽  
H. Ni ◽  
V. Jayaram ◽  
C.G. Levi ◽  
...  
Keyword(s):  
Surface Layer ◽  
Volume Fraction ◽  
Alloy Layer ◽  
Al Alloy ◽  
Near Surface ◽  
Bulk Growth ◽  
Continuous Formation ◽  
Metal Volume ◽  
Si Content ◽  
Metal Volume Fraction

The oxidation of liquid Al–Mg–Si alloys at 900–1400 °C was studied by thermogravimetric analysis (TGA). The development of a semi-protective surface layer of MgO/MgAl2O4 allows the continuous formation of an Al2O3-matrix composite containing an interpenetrating network of metal microchannels at 1000–1350 °C. An initial incubation period precedes bulk oxidation, wherein Al2O3 grows from a near-surface alloy layer by reaction of oxygen supplied by the dissolution of the surface oxides and Al supplied from a bulk alloy reservoir through the microchannel network. The typical oxidation rate during bulk growth displays an initial acceleration followed by a parabolic deceleration in a regime apparently limited by Al transport to the near-surface layer. Both regimes may be influenced by the Si content in this layer, which rises due to preferential Al and Mg oxidation. The growth rates increase with temperature to a maximum at ∼1300 °C, with a nominal activation energy of 270 kJ/mole for an Al−2.85 wt. % Mg−5.4 wt. % Si alloy in O2 at furnace temperatures of 1000–1300 °C. An oscillatory rate regime observed at 1000–1075 °C resulted in a banded structure of varying Al2O3-to-metal volume fraction.

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