GB2123031A - High-nickel austenitic alloys for sour well service - Google Patents
High-nickel austenitic alloys for sour well service Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C30/00—Alloys containing less than 50% by weight of each constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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Abstract
The alloys consist of 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% or Cr, 4 to 7 wt% of Mo, and the balance of Fe and inevitable impurities provided that Cr + 3 Mo is at least 40 wt%. Optionally the alloys may also contain 1 to 3 wt% of Cu, up to 0.5 wt% of Al, and/or one or more of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb, and 0.6 to 1.5 wt% of V.
Description
SPECIFICATION
High nickel austenitic alloys primarily for use in sour well environments
This invention relates to high nickel austenitic alloys which have excellent corrosion resistance and can be used in corrosive environments such as in sour wells.
As petroleum resources are becoming exhausted, there has been a recent trend to reutilise very deep or sour oil wells which were previously laid aside. However, these wells, in most cases, contain large amounts of chlorides, CO2 and H2S and are highly corrosive. Carbon steels or low alloy steels which have ordinarily been used as materials for oil well pipe cannot withstand use in such corrosive wells. Accordingly, there is a demand for high alloy materials with excellent corrosion resistance.
High alloy materials which have been tried or proposed as oil well tubing up to now include, for example, 13Cr martensitic stainless steels, austenitic and ferritic dual phase stainless steels, austenitic high nickel alloys, nickel-base alloys, cobalt-base alloys, titanium-base alloys, and the like. Of these,
13Cr martensitic stainless steels and the dual phase stainless steels are highly resistant to corrosion by
CO2 but have the drawback that they are liable to suffer from sulphide stress corrosion cracking (SSCC) when H2S is present. Accordingly, these steels cannot be used in severe well environments where H2S large amounts are present.
Nickel-base alloys, cobalt-base alloys and titanium-base alloys are resistant to corrosion in environments of the above mentioned type in which chlorides, CO2 and H2S are contained. However, it is very expensive to use materials such as Ni, Mo, Co and Ti in large amounts.
According to the second embodiment of the invention, there is provided a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of
Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
According to the second embodiment of the invention, there is provided a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 1 to 3 wt% of Cu and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
A third embodiment of the invention resides in a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 0.5 wt% or less of Al and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
A fourth embodiment of the invention resides in a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 1 to 3 wt% of Cu, 0.5 wt% or less of Al, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
A fifth embodiment of the invention resides in a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
A sixth embodiment of the invention resides in a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 3 wt% or less of Cu, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
A seventh embodiment of the invention resides in a high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 0.5 wt% or less of Al, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb, and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
An eighth embodiment of the invention resides in a high nickel alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 3 wt% or less of Cu, 0.5 wt% or less of Al, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
In the drawings,
Figure 1 is a graph showing the relation between the Ni content and the Mo content and stress corrosion cracking;
Figure 2 is a graph showing the relation between the Fe content and the Ni content and susceptibility to hydrogen embrittlement; and,
Figure 3 is a graph showing the relation between the weight loss and the content of Cr + 3Mo.
Among various characteristics required as materials for sour well tubing, the following four characteristic properties are considered especially important.
(1) No stress corrosion cracking (SCC) in an environment of Cl--CO2-H2S.
(2) Little susceptibility to hydrogen embrittlement under conditions of contact with carbon steel in an environment of Cl--CO2-H2S.
(3) Little susceptibility to local corrosion such as pitting corrosion, crevice corrosion and the like.
(4) High mechanical strength.
Of these characteristics, with regard to the mechanical strength of (4), it would be sufficient to subject high nickel alloys to cold working. It is important however whether or not the properties (1), (2) and (3) can be assured when the alloys are cold worked.
In order to evaluate the alloys with respect to these properties, we have made tests using the following methods.
The stress corrosion cracking (1) above was determined using, as an accelerated corrosion test, a method in which a U-shaped test specimen was immersed in boiling MgCI2 solutions of high concentrations. In this connection, it is generally accepted that the test using MgCI2 solutions of high concentrations accelerates the chloride stress corrosion cracking phenomenon which occurs in a neutral environment. For simulation of an environment such as that of a sour well, this method is considered proper.
In order to evaluate the susceptibility to hydrogen embrittlement (2) above, a test was conducted in which a U-shaped test specimen in contact with a carbon steel plate was immersed in a 5% NaCl-0.5% CH3COOH aqueous solution saturated with H2S at room temperature. By this test, hydrogen is generated on the surface of the U-shaped test specimen by the electrochemical action between the different types of metals contacting with each other, so that the susceptibility to hydrogen embrittlement in an environment of Cl--C02-H2S can properly be evaluated.
Further, we made use of a method of immersing in an aqueous 10% FeCI3 - 6H2O solution as an accelerated test of (3) above. This is because this solution is acidic.
The effect of alloy materials being investigated in a Cl--C02-H2S environment was confirmed from the results of these three accelerated tests.
A number of Ni-Cr-Mo alloys of the compositions shown in Table 1 were melted in a high frequency furnace and cast, followed by hot forging, hot rolling and cold rolling to obtain test specimens.
Each of these Ni-Cr-Mo alloy test specimens was subjected to the chloride stress corrosion cracking test in a boiling 35% MgCI2 solution and a boiling 42% MgCI2 solution. The test results are plotted in relation to Ni and Mo contents in Figure 1. As is seen in Figure 1, the synergistic effect of Ni and Mo is recognised. It is generally accepted that in order to prevent the stress corrosion cracking in 42% MgCI2 solution, the Ni content should exceed about 45 wt%. We found that no stress corrosion cracking was produced by the synergistic effect of Ni and Mo even when the Ni content is below 45 wt%. In Figure 1, the symbol "o" represents no occurrence of stress corrosion cracking and the mark "."represents occurrence of the stress corrosion cracking.
The materials of the compositions indicated in Table 1 were evaluated with respect to susceptibility to hydrogen embrittlement in a CI--CO2-H2S environment. The results are plotted in relation to Ni and Fe contents in Figure 2. As is seen in Figure 2, when the Ni content exceeds about 50%, the susceptibility to hydrogen embrittlement becomes considerably higher. In Figure 2, the symbol "o" represents no occurrence of the hydrogen embrittlement and the symbol "e" represents occurrence of the hydrogen embrittlement.
TABLE 1
Chemical Components (wt%) No. C Si Mn P S Ni Cr Mo Others 1 0.014 0.35 3.59 0.029 0.009 19.0 24.8 3.09 N: 0.30 V: 0.40 2 0.013 0.37 1.65 0.028 0.009 22.6 18.9 5.20 N: 0.19 3 0.015 0.31 0.72 0.030 0.010 29.8 21.9 5.12 Cu: 2.01 Ti: 0.88 Al: 0.14 4 0.015 0.30 1.50 0.019 0.010 31.2 26.7 3.41 Cu: 0.98 5 0.022 0.32 0.75 0.035 0.012 39.7 22.0 4.50 Cu: 2.0 Tl: 0.87 6 0.014 0.30 0.74 0.034 0.010 39.9 22.0 6.83 Cu: 1.99 Tl: 0.88 Al: 0.14 7 0.003 0.34 0.68 0.020 0.002 40.7 22.4 3.00 Cu: 2.00 Tl: 0.8 Al: 0.21 8 0.012 0.52 1.47 0.018 0.003 45.6 21.6 6.44 Cu: 1.96 Nb: 2.03 W: 0.2 9 0.052 0.13 0.03 0.005 < 0.001 51.8 19.2 3.05 Fe: 19.2 Nb: 4.95 10 0.018 0.23 0.19 0.005 0.003 Bal. 21.0 8.84 Nb: 3.44 Fe 2.43 11 0.033 0.21 0.21 0.002 0.001 Bal. 15.0 15.3 W: 2.77 Fe: 5.71 12 0.008 0.03 0.01 < 0.001 0.002 35.1 19.9 9.42 Tl: 0.65 Fe: 0.38 Co: Bal.
The materials of the same compositions as indicated in Table 1 were subjected to the crevice corrosion test in FeCI2 6H20 solution at 350C and 700 C. The results are summarised in Figure 3.
From Figure 3, it will be seen that the corrosion weight loss drastically decreases at a content of
Cr + 3Mo(%) of 40 wt%. Thus, it is essential that Cr + 3Mo is at least 40 wt%. Although it is known that an increase of Cr and/or Mo produces an improved resistance to crevice corrosion, we have first found that a specific ratio of Cr and Mo in a specific total amount of Cr and Mo is effective in improving the resistance to crevice corrosion. In Figure 3, the symbol "o" is for 350C and the symbol "e" is for 700 C.
As described hereinabove, the present invention is based on the results of the above tests and provides high nickel alloys which are suitable for use in sour wells.
The present invention is defined by the eight embodiments described before. The high nickel alloys are described in more detail with respect to constituent compartments and ratios thereof.
Higher contents of C result in better mechanical strength but if its content exceeds 0.05 wt% it will cause intergranular corrosion because of intergranular precipitation of Cr carbide. Accordingly, the content of C is 0.05 wt% or less.
N serves to improve mechanical strength and resistance to crevice corrosion. However, when it exceeds 0.04 wt% in the high nickel alloys, intergranular corrosion results with poor workability.
Accordingly, the content of N is 0.04 wt% or less.
Si and Mn which are used as deoxidisers in steel making impede workability and tenacity when each exceeds 1 wt% Accordingly, the contents of Ni and Mn are both within a range of 1 wt% or less.
Ni affects stress corrosion cracking and this effect becomes remarkable when Ni is used in combination with Mo. If the content is smaller than 35 wt%, there is little effect on the stress corrosion cracking even when a predetermined amount of Mo is contained. This will be apparent from Figure 1.
On the other hand, Ni increases susceptibility to hydrogen embrittlement and when its content exceeds about 50 wt%, there is an appreciable embrittlement as seen in Figure 2. Accordingly, the content of Ni should preferably be limited to below 45 wt%, inclusive, making allowances for safety. Accordingly, the content of Ni is in the range of 35 to 45 wt%.
Cr has an excellent effect on crevice corrosion in combination with Mo. When the content of Cr is in the range of 20 to 30 wt% and the total amount of Cr and 3Mo is at least 40%, crevice corrosion is sharply lowered as particularly seen in Figure 3. A content of Cr less than 20 wt% requires Mo in excess of 7% and is thus nor economical. On the other hand, a content of Cr in excess of 30 wt% is not advantageous because any further effect cannot be expected and hot workability becomes poor. Thus, the content of Cr is in the range of 20 to 30 wt%.
Mo reduces the stress corrosion cracking and crevice corrosion by a synergistic effect with Ni and
Cr respectively. Mo content should be in an amount of at least 4 wt% in relation to the contents of Ni and Cr and also in view of the results of Figures 1 and 3. However, when the content of Mo exceeds 7 wt%, no further effect can be expected. In view of economy, the upper limit of Mo is 7 wt%. Accordingly, the content of Mo is in the range of 4 to 7 wt%.
Cu is used to improve corrosion resistance and is an element which is especially effective in improving the resistance to crevice corrosion. Its content depends on well conditions. In this connection, when the content exceeds 3 wt%, the effect of Cu remains constant with a considerable lowering of hot workability. Accordingly, the content of Cu is 3 wt% or less. With a Cu content of less than 1 wt%, the resistance to corrosion is not improved much. Preferably, the content of Cu is in the range of 1 to 3 wt%.
It will be noted that where Cu is present but Ti, Nb and V which also serve to improve the resistance to corrosion are not present, the Cu content should be in the range of 1 to 3 wt% in order to retain the improving effect of Cu on the corrosion resistance.
Al is an element serving to improve the workability of alloys as a deoxidiser. A content exceeding 0.5 wt% results in poor workability. Accordingly, the content of Al is 0.5 wt% or less.
Ti, Nb and V are elements which act to improve the corrosion resistance and mechanical strength.
That is, Ti, Nb and V have the capability of forming carbides and can effectively prevent intergranular corrosion. Mechanical strength is improved by precipitation hardening of fine carbides as well as by reinforcement with solid solution of Ti, Nb and V, so that at least one member selected from Ti, Nb and
V may be incorporated depending on well conditions. They are not effective if their contents are less than 0.6 wt%. On the other hand, contents exceeding 1.5 wt% considerably impede workability.
Accordingly, the contents of Ti, Nb and V are, respectively, within a range of 0.6 to 1.5 wt%.
Examples of high nickel alloys for use in sour wells according to the invention are illustrated along with comparative examples.
EXAMPLES
Ingots were made by a known manner so that constituent components and constituent ratios indicated in Table 2 and 4 were attained, followed by working and machining to make test specimens.
In Tables 3 and 5, the test results are shown with regard to mechanical properties and crevice corrosion. TABLE 2
Chemical Components (wt %) No. C Si Mn Nl Cr Mo Cu Al Cr + 3Mo 1 0.035 0.38 0.12 38.8 25.3 5.03 - - 40.39 2 0.045 0.89 0.31 43.8 20.7 6.88 - - 41.34 3 0.012 0.30 0.85 44.5 29.1 4.12 - - 41.46 4 0.033 0.25 0.32 42.7 25.2 5.19 2.09 - 40.77 5 0.041 0.51 0.38 43.2 26.3 4.85 1.23 - 40.85 6 0.022 0.29 0.39 44.3 22.7 6.12 2.79 - 41.06 7 0.028 0.31 0.37 42.8 25.8 5.45 - 0.32 42.15 8 0.034 0.26 0.36 40.9 24.0 5.55 1.48 0.38 40.65 9 0.026 0.45 0.73 42.1 23.8 6.32 2.83 0.19 42.76 10 0.018 0.27 0.45 41.9 24.5 5.21 1.19 0.22 40.13 11 0.17 0.25 0.52 0.48 13.0 - - - SUS 420 12 0.021 0.36 0.54 5.99 20.4 1.92 Tl: 0.30 - Dual phase Stainless Steel 13 0.028 0.38 1.85 19.7 25.2 - - - SUS 310S TABLE 3
Tensile Properties of Corrosion Resistance in 25% Cold Worked Material Cl-CO2-H2 S" Yield Tensile Stress St. St. Elongation Corrosion Crevice**" No. (kg /mm2) (kg/mm2) (%) Cracking Corrosion 1 78.5 85.8 23.2 o o ( < 1) 2 79.4 86.1 23.0 o o ( < 1) 3 75.8 83.2 25.6 o o ( < 1) 4 79.3 87.6 22.4 o o ( < 1) 5 79.8 88.2 21.5 o 0 ( < 1) C 6 6 81.2 .89.7 20.3 o o ( < 1) 7 76.6 84.3 24.2 o o ( < 1) 8 I 79.2 86.1 22.5 o o ( < 1) 9 1 82.3 91.6 20.3 o o ( < 1) 10 78.3 86.3 22.1 o o ( < 1) 11 .> 63.7** 80.5** 23.0** x x (1700) pS 12 "P 94.5 97.3 11.3 x x (25.4) o 0 13 84.2 88.1 17.2 x x (8.5) *: 1 atm. , H2S-0.5% CH3 COOH-5%NaCl aqueous solution, room temperature.
**: Quenching (980 C), tempering (700 C) heat-treated material ***: Corrosion weight loss is indicated in brackets in terms of m/year. TABLE 4
Chemical Components (wt %) No. C Si Mn Nl Cr Mo Cu Al Ti,Nb, V Cr + 3Mo 14 0.036 0.42 0.18 42.3 25.6 5.24 - - Ti: 0.94 41.32 15 0.021 0.36 0.27 44.5 24.8 6.32 - - V: 0.85 43.76 16 0.042 0.55 0.81 39.2 23.9 5.72 - - Nb: 1.26 41.06 17 0.035 0.25 0.38 41.1 23.8 5.50 1.61 - Ti: 1.02 40.30 18 0.034 0.27 0.35 41.2 23.6 5.52 1.49 - Nb: 1.33 40.16 19 0.033 0.28 0.34 41.4 23.9 5.49 1.48 - V: 1.05 40.37 20 0.015 0.21 0.50 42.2 26.7 5.63 - 0.18 Ti: 0.88 43.59 21 0.011 0.26 0.73 42.4 27.3 4.92 2.04 0.21 Nb: 1.12 42.06 22 0.027 0.25 0.41 36.7 25.8 4.93 1.03 0.23 Ti: 0.68 40.59 23 0.010 0.33 0.64 41.5 24.9 5.86 2.54 0.23 Nb: 0.65 42.48 V: 0.65 24 0.17 0.25 0.52 0.46 13.0 - - - - SUS420 25 0.21 0.36 0.54 5.99 20.4 1.92 - - Ti: 0.30 * 26 0.028 0.38 1.85 19.7 25.2 - - - - SUS310S *: Dual phase stainless steel.
TABLE 5
Tensile Properties of Corrosion Reistance in 25% Cold Worked Material Cl CO2+2SCI--CO,-H,S' I Yield Tensile Stress Crevice*** St. St. Elongation Corrosion Corrosion No. (kg /mm2) (kg /mm2) (O/o) Cracking 14 78.2 88.3 23.2 o o ( < 1) 15 77.9 87.5 23.8 o o ( < 1) 16 79.3 88.4 22.7 o o ( < 1) 17 79.6 86.3 22.4 o o ( < 1) 18 v, 81.1 90.3 2z2 o o ( < 1) Co 0 19 < : 82.2 91.5 21.3 o o ( < 1) 20 77.4 84.2 24.0 o o ( < 1) 21 81.5 90.0 22.1 o o ( < 1) 22 80.3 89.6 22.5 o o ( < 1) 23 81.6 90.8 21.8 o o ( < 1) 24 > 63.7"" 80.5** 23.0" x x (1700) Co coo 25 E < 94.5 97.3 11.3 x x (25.4) Oo .
0 26 84.2 88.1 17.2 x x (8.5) *: 1 atm. H2S-0.5% CH3OOH-5%NaCl aqueous solution, room temperature.
** : Quenching (9800 C), tempering (700 C) heat-treated material.
***: Corrosion weight loss is indicated in brackets in terms of m/year.
As will be apparent from Tables 3 to 5, the high nickel alloys according to the invention show better mechanical properties than the comparative steels with their corrosion resistance being much better than all the comparative steels.
The present invention provides high nickel alloys which are suitable for use in CI--C02-H2S environments with excellent corrosion resistance. These alloys are applicable not only as materials for sour wells, but also as materials which are required to have high resistance to corrosion such as with heat-exchanger tubes of apparatus being used in similar corrosive environment (Cl-, CO2 and/or H2S environments).
Claims (9)
1. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
2. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 1 to 3 wt% of Cu, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
3. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 0.5 wt9/o or less of Al, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
4. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, wt% or less of Mn,35 35 to 45 wt% ofNi, 20 to 30 wt% of Cr,4 to 7 wt% of Mo, 1 to 3 wt% of Cu, 0.5 wt% or less of Al, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
5. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
6. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 3 wt% or less of Cu, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb, and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that
Cr + 3Mo is at least 40 wt%.
7. A high nickel austenitic alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 0.5 wt% or less of Al, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1 5 wt% of V, and the balance of Fe and inevitable impurities provided that
Cr + 3Mo is at least 40 wt%.
8. A high nickel alloy comprising 0.05 wt% or less of C, 0.04 wt% or less of N, 1.0 wt% or less of Si, 1.0 wt% or less of Mn, 35 to 45 wt% of Ni, 20 to 30 wt% of Cr, 4 to 7 wt% of Mo, 3 wt% or less of Cu, 0.5 wt% or less of Al, at least one member selected from the group consisting of 0.6 to 1.5 wt% of Ti, 0.6 to 1.5 wt% of Nb and 0.6 to 1.5 wt% of V, and the balance of Fe and inevitable impurities provided that Cr + 3Mo is at least 40 wt%.
9. A high nickel austenitic alloy as set out in Example numbers 1 to 10 of Table 2 or Example numbers 14 to 23 of Table 4.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8268982A JPS58199851A (en) | 1982-05-17 | 1982-05-17 | High nickel alloy for acidic oil well |
| JP22570682A JPS58199852A (en) | 1982-12-22 | 1982-12-22 | High nickel alloy for acidic oil well |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| GB8313515D0 GB8313515D0 (en) | 1983-06-22 |
| GB2123031A true GB2123031A (en) | 1984-01-25 |
| GB2123031B GB2123031B (en) | 1985-09-25 |
Family
ID=26423704
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB08313515A Expired GB2123031B (en) | 1982-05-17 | 1983-05-17 | High-nickel austenitic alloys for sour well service |
Country Status (3)
| Country | Link |
|---|---|
| GB (1) | GB2123031B (en) |
| NL (1) | NL8301757A (en) |
| NO (1) | NO831752L (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0136998A1 (en) * | 1983-08-10 | 1985-04-10 | Voest-Alpine Stahl Aktiengesellschaft | Wrought nickel-base alloy and process for its thermal treatment |
| FR2698883A1 (en) * | 1992-12-09 | 1994-06-10 | Sima Sa | Nickel base alloy of the quaternary Ni-Fe-Cr-Mo system with hardening by precipitation of gamma prime phase and resistant to the corrosion modes encountered in particular in the petroleum industry. |
| FR2845098A1 (en) * | 2002-09-26 | 2004-04-02 | Framatome Anp | NICKEL-BASED ALLOY FOR ELECTRIC WELDING OF NICKEL ALLOYS AND WELDED STEEL STEELS AND USE THEREOF |
| WO2015120832A1 (en) * | 2014-02-13 | 2015-08-20 | VDM Metals GmbH | Titanium-free alloy |
| CN111020106A (en) * | 2019-12-13 | 2020-04-17 | 湖南众鑫新材料科技股份有限公司 | Vanadium-nitrogen alloy additive and preparation method thereof |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3810336A1 (en) * | 1988-03-26 | 1989-10-05 | Vdm Nickel Tech | CURABLE NICKEL ALLOY |
-
1983
- 1983-05-16 NO NO831752A patent/NO831752L/en unknown
- 1983-05-17 NL NL8301757A patent/NL8301757A/en not_active Application Discontinuation
- 1983-05-17 GB GB08313515A patent/GB2123031B/en not_active Expired
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0136998A1 (en) * | 1983-08-10 | 1985-04-10 | Voest-Alpine Stahl Aktiengesellschaft | Wrought nickel-base alloy and process for its thermal treatment |
| FR2698883A1 (en) * | 1992-12-09 | 1994-06-10 | Sima Sa | Nickel base alloy of the quaternary Ni-Fe-Cr-Mo system with hardening by precipitation of gamma prime phase and resistant to the corrosion modes encountered in particular in the petroleum industry. |
| EP0601915A1 (en) * | 1992-12-09 | 1994-06-15 | Sima S.A. | Nickel base alloy of the quaternary system Ni-Fe-Cr-Mo, gamma prime precipitation-hardening and resisting to corrosive environments, typically occurring in the oil industry |
| AU666784B2 (en) * | 1992-12-09 | 1996-02-22 | S I M A, Sa | Nickel based alloy in the quaternary Ni-Fe-Cr-Mo system hardened by precipitation of the gamma prime phase and withstanding modes of corrosion to be found, in particular, in the oil industry |
| FR2845098A1 (en) * | 2002-09-26 | 2004-04-02 | Framatome Anp | NICKEL-BASED ALLOY FOR ELECTRIC WELDING OF NICKEL ALLOYS AND WELDED STEEL STEELS AND USE THEREOF |
| EP1408130A1 (en) * | 2002-09-26 | 2004-04-14 | Framatome ANP | Nickel based alloy for electrical welding of nickel alloys and steels, welding wire and its use |
| WO2015120832A1 (en) * | 2014-02-13 | 2015-08-20 | VDM Metals GmbH | Titanium-free alloy |
| KR20160135168A (en) * | 2014-02-13 | 2016-11-25 | 파우데엠 메탈스 인테르나티오날 게엠베하 | Titanium-free alloy |
| KR101865406B1 (en) | 2014-02-13 | 2018-06-07 | 파우데엠 메탈스 인테르나티오날 게엠베하 | Titanium-free alloy |
| US10174397B2 (en) | 2014-02-13 | 2019-01-08 | Vdm Metals International Gmbh | Titanium-free alloy |
| CN111020106A (en) * | 2019-12-13 | 2020-04-17 | 湖南众鑫新材料科技股份有限公司 | Vanadium-nitrogen alloy additive and preparation method thereof |
| CN111020106B (en) * | 2019-12-13 | 2021-07-27 | 湖南众鑫新材料科技股份有限公司 | Vanadium-nitrogen alloy additive and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| GB8313515D0 (en) | 1983-06-22 |
| NO831752L (en) | 1983-11-18 |
| GB2123031B (en) | 1985-09-25 |
| NL8301757A (en) | 1983-12-16 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PCNP | Patent ceased through non-payment of renewal fee |