Stress Corrosion Cracking of Steel in Liquid Ammonia

Nakai, Youichi; Uesugi, Yasuji; Kurahashi, Hayao

doi:10.2355/tetsutohagane1955.67.14_2234

Tetsu-to-Hagane

1981

DOI: 10.2355/tetsutohagane1955.67.14_2234

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Stress Corrosion Cracking of Steel in Liquid Ammonia

Youichi Nakai

Yasuji Uesugi

Hayao Kurahashi

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1985

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Cited by 5 publications

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“…However, the mechanism of Cu rolls on HIC prevention has not been fully clarified. It was found that Cu addition remarkably decreased hydrogen entry into steel [2] and Cu was enriched in the corrosion product based on EPMA micron order analysis [3]. In present paper, corrosion test under H 2 S environments are carried out with measuring the amount of hydrogen permeation.…”

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confidence: 97%

Effect of Cu on Hydrogen Permeation for the Low Carbon Steel under Mildly Sour Environments

Nakamichi¹,

Baba²,

Mizuno³

et al. 2015

Microsc Microanal

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Hydrogen Induced Cracking (HIC) and Sulfide Stress Cracking (SSC) are the major issue for low carbon alloyed steels applied to sour line pipes at oil and natural gas fileds. It is caused by the presence of hydrogen sulfide, which enhances hydrogen entry into steels and causes the environmental cracking. It is well known that Cu is effective element for preventing HIC in mildly sour environments in which the solution pH is more than 5.0[1]. However, the mechanism of Cu rolls on HIC prevention has not been fully clarified. It was found that Cu addition remarkably decreased hydrogen entry into steel [2] and Cu was enriched in the corrosion product based on EPMA micron order analysis [3]. In present paper, corrosion test under H 2 S environments are carried out with measuring the amount of hydrogen permeation. Microstructural morphologies of corrosion products, especially Cu distribution and morphologies are investigated through FIB/SEM and STEM analysis for understanding its rolls on preventing the corrosions.Two samples, concentration of 0.06C-1.7Mn-0.1Si with and without 0.3wt%Cu, were prepared through a vacuum melting.Corrosion tests were performed under 100%H 2 S gas environment in 5%NaCl+1N(CH3COOH+CH3COONa) solution for 96hrs. The hydrogen permeation was measuring during corrosion test. For evaluating effects of solution environment on corrosion product, two pH conditions of 5.0 and 5.3 were performed. After corrosion test, samples were picked up from the solution and SEM and TEM observations were carried out. Cross section samples of SEM and TEM were prepared by FIB techniques. Distribution of alloy elements in the corrosion product and steel were measured through EDS analysis equipped with SEM and TEM Fig.1 shows plane view SEM images of corrosion product of Cu added steel immersed in the pH 5.3 and 5.0 solutions. It is observed that the surface morphology of corrosion products formed in high pH solution were smooth compared with that of in low pH solution. Micrographs of SEM cross sectioning are show in Fig. 2, together with the hydrogen permeation value at 90 hours of corrosion test. Several micro-meter thickness of corrosion product is formed during immersion test and there are roughly two layers in that product. Different microstructure is recognized dependent on the Cu concentration and pH value. The upper layer formed on the Cu added steel in high pH solution is uniform even though it structure is porous. On the other hand, that of formed on non-Cu added steel in low pH solution is very rough and has many large cracks. The bottom layer formed on the Cu added steel in high pH solution has dense structure and no cracks. The hydrogen permeated value is increasing when the corrosion layer has large cracks. It is supposed that adding Cu is very useful for forming uniform tight corrosion layer without large cracks for preventing hydrogen permeation. For evaluating the Cu distribution in the corrosion film, cross sectional TEM analysis is carried out and the STEM images shown in Fig.3. It is found that the...

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mentioning

confidence: 97%

Effect of Cu on Hydrogen Permeation for the Low Carbon Steel under Mildly Sour Environments

Nakamichi¹,

Baba²,

Mizuno³

et al. 2015

Microsc Microanal

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Spannungsrißkorrosion von unlegierten Stählen in flüssigem ammoniak

Gräfen

Hennecken

Horn

et al. 1985

Materials & Corrosion

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In dieser Arbeit wird über Untersuchungen zur SpRK von Stählen in flüssigem Ammoniak berichtet, deren Ziel es war, Einflußgrößen und ihre Wirkgrenzen zu bestimmen, Aufschluß über den Mechanismus der an Kugeldruckbehältern aufgetretenen Schäden zu erlangen und Schutzmaßnahmen zu ermitteln. Zu diesem Zweck wurden langzeitige Auslagerungsversuche mit geschweißten Jones‐Proben aus verschiedenen unlegierten und niedriglegierten Stählen unterschiedlicher Wärmebehandlungszustände in einer Ammoniakkugel durchgeführt. Für Laborversuche wurde eigens eine Apparatur entwickelt, mit der Untersuchungen in flüssigem Ammoniak an Rundzugstäben unter CERT ‐Bedingungen beim Freien Korrosionspotential und unter elektrochemischer Kontrolle durchgeführt werden konnten. Gezielt zugesetzte Verunreinigungen wurden hierbei mittels eines Gaschromatographen quantitativ bestimmt. Aus den Untersuchungen geht der entscheidende Einfluß des Sauerstoffgehalts im Ammoniak auf die Entstehung von Spannungsrißkorrosion an unlegierten Stählen hervor. Bereits geringe O2‐Mengen (ßß 2 ppm) bewirken eine Spannungsrißkorrosionsgefahr. Wassergehalte können die Spannungsrißkorrosion inhibieren. Hierbei werden bezüglich der erforderlichen Menge Unterschiede zwischen den einzelnen Werkstoffen sichtbar (StE 355: > 500 ppm, H I: > 650 ppm, StE 460: > 1000 ppm H2O). Eine werkstoffseitige Differenzierung wird auch in bezug auf den Einfluß von Eigen‐ und Betriebsspannungen deutlich. Lediglich Jones‐Proben aus StE 355 blieben ohne Spannungsarmglühung rißfrei. Versuche zur Potentialabhängigkeit der Rißbildung weisen aus, daß die Schädigung einem anodischen Rißbildungsmechanismus folgt, da sie anodisch verstärkt und kathodisch verhindert werden kann. Ebenso wird die inhibitive Wirkung des Wassers durch eine anodische Polarisation eingeschränkt. Jedoch ist durch anodische Polarisation allein, d.h. ohne Gegenwart von O2, Spannungsrißkorrosion nicht zu erzielen. Für die Praxis kann zusammengefaßt werden: Sauerstoffgehalte – auch in Spuren – sind zu vermeiden. Wasserzusatz inhibiert die Spannungsrißkorrosion; Zusätze von Wasser sind daher – soweit möglich – zu empfehlen. Behälter sollen aus StE 355 gebaut und spannungsarm geglüht werden. Kathodischer Schutz ist denkbar, sofern es gelingt, diesen in der Praxis zu verwirklichen.

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Increasing the safety of vessels with liquid ammonia

Tretyak

Slipchenko

1990

Mater Sci

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Stress Corrosion Cracking of Steel in Liquid Ammonia

Cited by 5 publications

References 4 publications

Effect of Cu on Hydrogen Permeation for the Low Carbon Steel under Mildly Sour Environments

Effect of Cu on Hydrogen Permeation for the Low Carbon Steel under Mildly Sour Environments

Spannungsrißkorrosion von unlegierten Stählen in flüssigem ammoniak

Increasing the safety of vessels with liquid ammonia

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