Low-pressure cold metal spray coatings for repair and protection of marine components

Author(s):  
M Pal

The marine environment is hostile to most engineering materials, a combination of in-service wear and exposure to marine environment leads to an accelerated material degradation.  Insufficient or poor protection of the substrates further assists the accelerated material degradation in marine environment. There is a direct relationship between the material-state of a ship and its operational capability, readiness, and service life.  The current state-of-the-art practice is to use paint-based coatings to maintain the material-state of ships.  However, the protection offered by paint coatings is usually brief due to inherent permeability and low damage tolerance of these coatings.  For this reason, the paint coatings require renewal at regular intervals, typically less than 5-years, to maintain a minimum level of protection from the marine environment.  The need for regular painting of ships results in a significant negative impact on the through-life availability, operational capability/readiness, and the cost of maintenance/operation of naval ships.  Therefore, the fleet owners and operators should look beyond the conventional paint-based coatings to achieve significant breakthrough improvements in maintaining and enhancing the material-state of naval ships. Metallic coatings, if selected and applied appropriately, will outperform the paint coatings in the marine environment.  Historically, the cost and performance of metallic coatings, mainly thermal metal spray (TMS) coatings, prevented their widespread use in the marine industry.  The TMS coatings also have their own inherent application and performance related limitations that are widely reported in the literature.  However, the cold metal spray (CMS) coating process can overcome the application and performance related limitations that are typically associated with the TMS coatings, therefore creating an opportunity for widespread use of metallic coatings in shipbuilding and fleet upkeep/maintenance. In this paper, the ability of low-pressure (LP-CMS) coatings to repair and reclaim damaged marine components, and application of functional coatings to improve in-service damage tolerance of the damaged/new components is investigated.  The results of the investigation show that two LP-CMS coatings, Al-alloy and CuZn-alloy, can be used to repair and preserve both new and damaged components.  The accelerated salt-spray and natural immersion corrosion testing of the LP-CMS coatings showed that each coating will be better suited to a particular operational environment, i.e. CuZn-alloy coating performed well in both immersion and atmospheric corrosion environments, whereas Al-alloy coating performed well only in atmospheric corrosion environment. 

2009 ◽  
Vol 36 (8) ◽  
pp. 2187-2191 ◽  
Author(s):  
陈永哲 Chen Yongzhe ◽  
王存山 Wang Cunshan ◽  
李婷 Li Ting ◽  
姚标 Yao Biao

2008 ◽  
Vol 35 (10) ◽  
pp. 1632-1636 ◽  
Author(s):  
黄安国 Huang Anguo ◽  
李刚 Li Gang ◽  
汪永阳 Wang Yongyang ◽  
李磊 Li Lei ◽  
李志远 Li Zhiyuan

2020 ◽  
Vol 52 (10) ◽  
pp. 2299-2305 ◽  
Author(s):  
Dong Jun Park ◽  
Yang Il Jung ◽  
Jung Hwan Park ◽  
Young Ho Lee ◽  
Byoung Kwon Choi ◽  
...  

2019 ◽  
Vol 7 (46) ◽  
pp. 14471-14492
Author(s):  
David B. Lioi ◽  
Vikas Varshney ◽  
Sarah Izor ◽  
Gregory Neher ◽  
W. Joshua Kennedy

We provide a broad review of optically responsive materials with potential for in situ monitoring of material state properties in structural polymer-based materials with nanoscale spatial resolution.


2003 ◽  
Vol 54 (7) ◽  
pp. 483-487
Author(s):  
Naotsugu SHIRAISHI ◽  
Kazushige CHIBA ◽  
Yoshihiko HAGIWARA ◽  
Shinichi OHYA

2013 ◽  
Vol 575-576 ◽  
pp. 390-393 ◽  
Author(s):  
Guirong Li ◽  
Hong Ming Wang ◽  
Yun Cai ◽  
Xue Ting Yuan

In Mg-Al alloy β (Mg17Al12) phase is the main precipitate and reinforced phase. The microstructure and performance of alloy are strongly dependent on the morphology and behavior of β phases. In this paper, a kind of Mg-Al alloy is chosen as the research object with 8.92 weight percent aluminum element. The alloy is subjected to cycling cryogenic treatment. The microstructure evolution and thermodynamic balance are analyzed by scanning electronic microscope and Thermo-CALC software. The results show that after two cryogenic treatments the quantity of the precipitate hardening β phase increases and the sizes of the precipitates are refined from 8~10 μm to 2~4μm. This is expected to be due to the decreased solubility of aluminum in the matrix at low temperatures and the significant plastic deformation due to internal differences in thermal contraction between phases and grains.


CORROSION ◽  
10.5006/2370 ◽  
2017 ◽  
Vol 74 (1) ◽  
pp. 134-143 ◽  
Author(s):  
I.G. Ogunsanya ◽  
C.M. Hansson

A study has been conducted of the chloride-induced corrosion behavior of four different batches of galvanized steel reinforcement embedded in sound and in cracked concrete. One batch of bars was of conventionally produced hot-dipped galvanized (HDG) steel, two were prototypes of continuously galvanized rebar, and the fourth was a hot-dipped bar with an experimental Zn-Al alloy coating. Carbon (black) steel bars were also tested for comparison purposes. The continuously galvanized process is aimed at producing a thinner, but more ductile coating than that formed by conventionally hot-dipped galvanizing process. Metallographic examination of the as-received galvanized bars showed a wide variation of the coating thickness around and along the bars, and the continuously galvanized coatings were consistently thinner than specified. All bars were cast in concrete which was subsequently cracked either parallel to or perpendicular to the embedded bars. Additional specimens were tested in the sound (non-cracked) concrete. All specimens were constantly exposed to a chloride brine for 64 weeks, and were electrochemically assessed bi-weekly during the exposure period. The electrochemical results and visual examination after autopsy showed that no active corrosion was initiated in either the galvanized or black rebar reinforced non-cracked concrete specimens. Therefore, the data in this project give no indication of initiation time or chloride threshold concentration for corrosion of these bars. On the other hand, in all cracked concrete specimens, corrosion initiated at the base of the crack and extended along or around the bars. In the cracked specimens, all galvanized bars exhibited lower current densities than the black bars, with the HDG being the lowest. Recommendations are given for appropriate interpretation of half-cell potentials of the galvanized bars investigated in terms of high or low probability of active corrosion.


2014 ◽  
Vol 238 ◽  
pp. 139-142 ◽  
Author(s):  
Du Guangyu ◽  
Tan Zhen ◽  
Ba Dechun ◽  
Liu Kun ◽  
Sun Wei ◽  
...  

1998 ◽  
Vol 84 (10) ◽  
pp. 734-739 ◽  
Author(s):  
Yukio UCHIDA ◽  
Atsushi ANDOH ◽  
Atsushi KOMATSU ◽  
Koji YAMAKAWA
Keyword(s):  

Metals ◽  
2021 ◽  
Vol 11 (11) ◽  
pp. 1688
Author(s):  
Dawei Wang ◽  
Zhiguo Liu ◽  
Wenrui Liu

Titanium alloys have been widely used in aerospace engineering due to their excellent mechanical properties, especially their strength-to-weight ratio. In addition, Ti6Al4V (TC4) alloy is the most widely used among α+β alloys. The main three elements of TC4 alloy are titanium (Ti), aluminum (Al) and vanadium (V). Since the boiling point of aluminum is much lower than the melting point of the other two elements, the consistency of TC4 alloy during smelting, additive manufacturing and surface treatment is difficult to control. Therefore, in order to study the difficult problem of composition control in TC4 alloy production, we measured the vacuum evaporation of Al, Ti and V in Ti-Al, V-Al and TC4 alloys, and tracked the changes of molten pool temperature, heating time and weight. According to the results, the Al started to evaporate near 1300 ± 10 °C in vacuum and totally evaporated after 225 s heating to 1484 °C at 10−2 Pa. However, V and Ti barely evaporated below 2000 °C. The Al in Ti-Al alloy started to evaporate at 1753 ± 10 °C and lost 20.6 wt.% aluminum during 500 s at 1750~1957 °C. The Al in V-Al alloy started to evaporate at 1913 ± 10 °C and lost 26.4 wt.% aluminum during 543s at 1893~2050 °C. The Al in TC4 alloy started to evaporate at 1879 ± 10 °C and lost 79.6 wt. % aluminum after 113 s at 1879~1989 °C. The results indicate that smelting TC4 alloy with Ti-Al and V-Al alloys by EBM below 1900 °C improves the consistency and performance. Additionally, the lowest loss of Al occurred in the additive manufacturing of TC4 alloy below 1900 °C.


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