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Traditional solutions for the chemical passivation of stainless steel are nitric acid based, with the addition of sodium dichromate as an inhibitor for precipitation hardened and free machining stainless steels. These passivation chemistries are difficult to handle from an environmental health and safety point of view, particularly the dichromate inhibited versions. Citric acid passivation has been pursued as a replacement for both nitric acid and inhibited nitric acid based chemistries for many years, and has been incorporated into consensus specifications such as ASTM A967 and SAE AMS2700.
Citric acid passivation offers a promising alternative to nitric acid passivation, particularly for free machining and precipitation hardened stainless steels where the latter requires the addition of sodium dichromate. While citric acid passivation is defined in industry specifications such as ASTM(1) A967 and SAE(2) AMS2700, it is done with much less specificity than nitric acid passivation. This lack of specificity allows for conditions to be applied where inadequate passivation is achieved for some alloys. In this work, the citric acid passivation method has been explored and optimized for a range of common stainless steel alloys including a common austenitic alloy, AISI(3) 304L (UNS S30403), an austenitic free-machining alloy, 303 (UNS S30300), a ferritic free-machining alloy, 416 (UNS S41600), and precipitation hardened alloy, 17-4 PH (UNS S17400). A series of commercially available chemistries have also been explored.
Industrial usage of Plasma Electrolytic Oxidation (PEO) has grown consistently in recent years, thanks to the improved characteristics imparted to the oxide film in terms of surface adhesion, hardness, crystallinity, uniformity, and corrosion resistance. The metallic substrate is not subjected to elevated temperature and the overall equipment complexity is relatively simple, making the technique a good candidate for surface functionalization. In PEO treatments, high voltages are employed (~ 150-750 V 1) allowing for the formation of an insulating, or at least semiconductive, oxide layer that’s limits ion transport responsible for the initial coating growth. Beyond the spark voltage (prerequisite the enter the PEO regime) oxidation does not occur only as the result of a continuous flow of ions but rather it takes place after the cooling of a plasma discharge.
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Martensitic stainless steel (MSS) well tubulars are favorable due to their high strength and relatively low cost and are therefore widely applied in the Oil & Gas industry. This is especially the case for 13Cr and Super13Cr grades, which are often selected for mildly sour gas fields, where a relatively low content of H2S is present. When selecting martensitic stainless steels for sour service, the susceptibility to Stress Corrosion Cracking (SCC) and Sulfide Stress Cracking (SSC), determined by standard laboratory tests, are the most important selection criteria.
Underground natural gas storage (UGS) is an important component of the overall natural gas transportation and distribution system. It enables the utilities to supply natural gas during high seasonal demand periods and store gas during periods of lower demand. There are approximately 627 underground gas storage sites worldwide with a working gas capacity of 319.3 Billion m3 ( about 11.8 Trillion Cubic feet). The U.S. has a total of 414 natural gas storage fields, out of which 25 are inactive.