JPH0674471B2 - High corrosion resistance Ni-based alloy - Google Patents

Description

BACKGROUND OF THE INVENTION <FIELD OF THE INVENTION> The present invention, a corrosive environment, so-called sour gas environment has been noted _{(H 2 S-CO 2 -Cl} - environment) particularly conventional further corrosive than is The present invention relates to a Ni-based alloy for oil country tubular goods that has excellent stress corrosion cracking resistance and hydrogen cracking resistance even in a sour gas environment where sulphur (S) is mixed as a simple substance, not as a sulfide such as FeS or NiS. .

<Prior art and its problems> In recent years, the energy situation has reached the point where deep wells in oil wells and wells under sour gas environments are unavoidable.
High-strength, high-resistance Ni-based alloys for oil country tubular goods that are expensive but that can sufficiently withstand the above-mentioned harsh environment have been developed and applied (for example, JP-A-54-107828 and (See Japanese Laid-Open Publication No. 54-127831).

However, according to recent oil well information, in addition to the sour gas environment which has been said to have severe corrosiveness, an environment in which sulfur (S) is further mixed as a simple substance in the sour gas environment has been found. In such an environment, it has become clear that even the Ni-based alloys for sour gas resistance proposed so far are not sufficiently satisfactory in terms of corrosion resistance.

To further elaborate on this point, as explained above,
Other recent new oil wells and oil and natural gas in gas wells, water and salts (Cl ^-, Br ^-, etc.) and filed in a mixed environment increases the tendency of corrosive gas such as H ₂ S and CO ₂ together However, according to the analysis results of these environmental components carried out on the ground, recently, sulfur (S) is a simple substance (a sulfide form such as FeS or NiS) in comparison with the corrosive gas, water, salts, etc. The existence of oil wells that belong to a new environment, as seen in (No. Sulfur (S) existing in such an environment exists as a simple substance S even when it becomes polysulfide (H ₂ S _x ) as shown by the formula H ₂ S _x H ₂ S + S _x-1 deep in the ground. It is also said that depending on the temperature and pressure (particularly H ₂ S partial pressure), the form of S or H ₂ SO _4, etc. can be obtained according to the formula 4S + 4H ₂ O 3H ₂ S + H ₂ SO _4. It cannot be denied that

Of these, H ₂ S _x has a function of increasing the H ₂ S concentration as a reservoir of H ₂ S gas, while H ₂ SO ₄ has a function of lowering the pH.

By the way, in order to confirm these phenomena, the present inventors have
H ₂ S-CO ₂ -Cl ^- environment and ^{_{H 2 S-CO 2 -Cl -}} Ni under -S environment
We carried out an investigation experiment on the difference in corrosion resistance on the base alloy (containing austenitic alloy). As a result, the effect on the corrosion resistance of the Ni-based alloy was different depending on whether sulfur (S) was added or not. Although it was confirmed that the existence significantly deteriorates the corrosion resistance of Ni-based alloys, no clear elucidation was made about the corrosion mechanism when sulfur (S) coexists, and it is roughly classified into H ₂ S _x H ₂ S. reservoir theory formula _{"H 2 S + S x-1} ⇔H 2 S x " to the slave go-between Porisarufuaido (H ₂ S
_x) occurs in a high temperature environment, so acts as a reservoir for H ₂ S, H ₂ S _x is the same action as the high H ₂ S environment in contact with the material, H ₂ SO ₄ by the low pH of theory H ₂ even in an environment of S only single S does not exist, if there is water _{"4S + 4H 2 O3H 2 S +} H 2 SO 4 " is H ₂ SO ₄ at the same time follow connexion H ₂ S occurs in the formula is also generated, which lowers the pH It was impossible to get out of the speculation that one of the two theories of "to let it happen" was influential.

The present inventors <Means for Solving the Problems> etc., from the viewpoint as described above, typical sour gas environment _{(H 2 S-CO 2 -Cl} - environment) as well, this sulfur (S) As a result of further research to provide an alloy having sufficient corrosion resistance even in an environment where it is mixed alone, the following findings have been obtained. That is, (a) in an environment in which a simple substance of sulfur (S) is further mixed in the sour gas environment, there is no doubt that there is a corrosion mode different from the corrosion mechanism of the Ni-based alloy in the conventional sour gas environment, and the simple substance S has temperature and pressure. Depending on (particularly H ₂ S partial pressure), according to the reaction of “S _x-1 + H ₂ SH ₂ S _x ”, three states (S _x-1 , H ₂ S and
H ₂ S _x ), and when sulfur (S) or H ₂ S _x released as S _x-1 exists, this locally adheres to the oil country tubular goods member, and significant pitting corrosion occurs at that portion. However, in the conventional sour gas environment, the morphological change of sulfur (S) as shown in the above reaction formula is hardly recognized, and accordingly S _x-1 or H ₂ S _The specific corrosion morphology due to _x does not occur, but the reason why the specific corrosion morphology described above occurs in the sour gas environment in which sulfur (S) simple substance is mixed is that "4S + 4H ₂ O 3H ₂ S + H ₂ SO ₄ "
It is thought that this is because H ₂ S is generated and H ₂ SO ₄ is also generated at the same time as H ₂ S is generated, and it is considered that the pH of the environment is lowered. (C) An oil well in an environment exhibiting such a unique corrosion form In order to exhibit sufficient corrosion resistance for pipe materials, it is essential to form a protective film that is harder than the corrosion-resistant film formed in the conventional sour gas-use Ni-based alloy and has good repairability, On the other hand, it is necessary to take measures to improve the fracture characteristics of alloy members to prevent the progress of pitting corrosion and prevent stress corrosion cracking. (D) Protection of conventional Ni-base oil well pipe materials in sour gas environments The film strength and its repair ability are generally improved in proportion to the contents of Cr, Mo, and W, but in an environment containing elemental S, in addition to these, the role of Cu is extremely important, and 0.30% (hereinafter, Indicates the component ratio % Should be% by weight), and when the ambient temperature is 250 ° C or lower, Cr (%) + 10Mo (%) + 5W (%) ≧ 140 is secured, and the ambient temperature is higher. In the case of high temperature of 300 ° C or lower, unless Cr (%) + 10Mo (%) + 5W (%) ≥ 180 is secured, a sufficiently hard and protective coating with good repairability cannot be formed. (E) Furthermore, As described in the section (c), the protective film strengthening measure alone is not sufficient to alleviate the unique corrosion mode and improve the corrosion resistance of the alloy member, and the internal improvement for preventing the progress of pitting corrosion is not achieved. Although it is indispensable for this purpose, in addition to the component adjustment shown in the item (d) above, addition of Nb is also carried out, whereby the precipitation of Mo-W-Cr-C system carbide and its clustering are carried out. Suppressing is extremely effective.

This invention was made based on the above findings, Ni-based alloy, C: 0.10% or less, Si: more than 0.05 ~ 0.30%, Mn: 2.0% or less, P: 0.030% or less, S: 0.0050% Below, Ni: 45-60%, Cr: 15-30%, one or more of Mo and W: Mo is less than 16%, W is 5.0% or less, and Content of Cu: 0.30 to 3.0%, Ti: 2.0% or less, Nb: 0.30 to 3.0%, Al: 1.0% or less, N: 0.050% or less, and if necessary, Co: 5.0% or less, One or more of V, Ta, Zr and Hf: 1.0% or less, Rare earth element: 0.10% or less, Mg: 0.10% or less, Ca: 0.10% or less, Y: 0.20% or less , Fe and other unavoidable impurities: Oil and gas wells recently found by composing the composition of the components that satisfy the formula of Cr (%) + 10Mo (%) + 5W (%) ≥ 140, which is composed of the rest. In addition to the sulfur (S) as a simple substance, it is possible to exert extremely excellent stress corrosion cracking resistance and hydrogen cracking resistance even under a sour gas environment of about 250 ° C or less. is there.

Next, the reason why the component composition of the Ni-based alloy is numerically limited in the present invention will be described.

A) If the C content in the C alloy exceeds 0.10%, the amount of M ₆ C type carbides (where M is Mo, Ni, Cr, W, etc.) significantly increases, and the ductility and toughness of the alloy deteriorate. Therefore, the C content is set to 0.10% or less. It is recommended to reduce the C content to 0.020% or less, but particularly if the C content is suppressed to 0.010% or less, the ductility, toughness and corrosion resistance are more remarkably improved.

B) Si Si is added because it is an effective component as a deoxidizer, but if added in a large amount, it is an intermetallic compound that is not preferable for ductility and toughness such as σ, P, and Laves phase (hereinafter,
Abbreviated as “TCP phase”). Besides, S
When the i content exceeds 0.30% in particular, microsegregation during solidification is promoted, and the formation of the M ₆ C and P phases tends to be significantly promoted. For this reason, the upper limit of the Si content was set to 0.30%, but if the content is reduced to 0.10% or less, ductility is also added with the effect of suppressing grain boundary precipitation of carbides,
The toughness and corrosion resistance are further improved. On the other hand, the Si content is 0.
Since reducing it to less than 05% compels the alloy manufacturing operations to be cumbersome, the Si content was set to exceed 0.05%.

C) Mn Mn is a component that is usually added as a desulfurizing agent. However, if its content exceeds 2.0%, it may accelerate the formation of TCP phase. Defined to be less than or equal to%.

D) P and S P and S are inevitably mixed impurities, and if they are present in a large amount in the alloy, they deteriorate the hot workability due to grain boundary segregation and also deteriorate the corrosion resistance. The content is
The content was 0.030% or less and the S content was 0.0050% or less.

However, if the S content is suppressed to 0.0007% or less, the hot workability of the alloy is dramatically improved, and the P content is reduced.
Since the hydrogen cracking resistance of the alloy is remarkably improved by suppressing the content to 0.0030%, it is preferable to reduce the P and S contents to such a level.

It should be noted that FIG. 1 shows that the parallel portion is 4.0 mmφ from the alloy prepared by adjusting the amount of P in the composition specified by the present invention to have high strength by cold working of about 30%. GL is 30m
5 m / cm ^{2 in} a H ₂ S-5% NaCl solution (25 ° C.) in which H ₂ S was saturated at 10 atmospheres
Was subjected to a tensile test at a constant strain rate of 1 × 10 ⁻⁷ 1 / sec under the condition that the cathode current was added, and its hydrogen cracking resistance was evaluated.

In addition, FIG. 2 shows that a high temperature ductility test (test piece 10 mmφ, strain rate: 11 / sec) was performed at 1150 ° C. by adjusting an alloy in which only the S content was changed within the components specified in the present invention. It shows the effect on hot workability.

From FIG. 1 and FIG. 2 as well, it is clear that the P and S contents are preferably reduced to an extremely low range if possible.

E) Ni The alloy of the present invention is basically strengthened by adding elements such as Mo, Cr, W, and Nb, which have good solid solution strengthening and work hardening ability, to the Ni matrix. Causes the destabilization of austenite, so the lower limit of the Ni content was set to 45%, which is the Ni content sufficient to stabilize the austenite matrix. On the other hand, Ni is an element that itself improves the work hardening ability, but if it exceeds 60%, the hydrogen cracking resistance deteriorates, so the upper limit of the Ni content was set to 60%.

F) Cr Cr is a component that improves the corrosion resistance and strength of the alloy together with Mo, but this effect is remarkable when it is contained in a proportion of 15% or more. On the other hand, if the Cr content exceeds 30%, the hot workability of the alloy deteriorates and the TCP phase is more likely to be formed, so the Cr content was set to 15-30%.

G) Mo and W These components are alloy strength and corrosion resistance in the presence of Cr,
In particular, since it has the effect of remarkably improving the pitting corrosion resistance, it is possible to add one or more kinds, but the content is When the value of is less than 12, the desired effect cannot be obtained on the above-mentioned action, while the Mo content is 16% or more and the W content is
Over 5.0%, or A value of 16 or more leads to destabilization of the austenite matrix, which is observed when a large amount of Cr is added. Therefore, when Mo and W are added, Mo is less than 16% and W is 5.0%.
% Or less, and The content was set to a value that satisfies

Cu) Cu In a sour gas environment where sulfur (S) is found alone, together with Cr, Mo, and W, Cu is an extremely effective component for improving corrosion resistance, but if the Cu content is less than 0.30%, the desired corrosion resistance can be obtained. On the other hand, on the other hand, if the Cu content exceeds 3.0%, the effect is saturated, so the Cu content is 0.30 to 3.0.
Defined as%.

K) Ti Ti is effective in stabilizing a trace amount of C in the alloy, but if the content exceeds 2.0%, the TCP phase is likely to be generated, so the Ti content was set to 2.0% or less. The required Ti amount is determined according to the C content, and its lower limit is not particularly determined.

(C) Nb Nb is a component that significantly improves the corrosion resistance performance of the alloy in the sour gas environment in which sulfur (S) is recognized alone,
Moreover, it has a stabilizing effect on C as well as Ti and contributes to the increase in strength, but if its content is less than 0.30%, the desired effect cannot be obtained for the above-mentioned effect. If it is contained in excess of 10%, the TCP phase will be easily generated.
The b content was set to 0.30 to 3.0%.

It should be noted that FIG. 3 shows the effect of Nb on the stress corrosion cracking resistance by changing only the amount of Nb within the components specified in the present invention. The test material has a strength (0.2% proof stress) of 80 to 85k.
Using a constant gf / mm ² , 4.0 mmφ, GL: 30 mm
After creating the test pieces, 20% NaCl-0.5% CH 3 COOH-1g / l
S-10atmH ₂ S-20atmCO ₂ in solution (250 ℃) 1 × 10
^-7 1 / sec constant strain rate tensile test was performed to measure the elongation, and the stress corrosion cracking resistance was evaluated by comparing this with the elongation in the atmosphere.

It is clear from FIG. 3 that excellent stress corrosion cracking resistance can be obtained when the Nb content exceeds 0.30%.

Al) Al is added as an effective deoxidizer, but when the content exceeds 1.0%, the TCP phase is likely to form, so the Al content was determined to be 1.0% or less.

4) If the N content in the N 2 alloy exceeds 0.050%, coarse nitrides will be formed and the ductility and toughness will deteriorate, so the N content was defined as 0.050% or less.

S) Co, V, Ta, Zr, and Hf These components have the action of improving the ductility and toughness of the alloy as well as the corrosion resistance, so one or more of them may be contained if necessary. Hereinafter, the reason why the content ratio of each element is limited will be described together with the characteristic action.

i) Co The Co component is particularly effective for improving the hydrogen cracking resistance of the alloy. However, if the content exceeds 5.0%, the TCP phase is likely to form, so the Co content is 5.0% or less. I decided.

ii) V, Ta, Zr, and Hf These components are effective in stabilizing C. However, if each of them exceeds 1%, a TCP phase is easily formed. , And Hf, the content of one or more of them was set to 1.0% or less.

(C) Rare earth element (REM), Mg, Ca, and Y These components have the action of improving the hot workability of the alloy by adding at least one of the trace amounts, so one or more of them may be included if necessary. However, when the rare earth element content exceeds 0.10%, the Mg content exceeds 0.10%, the Ca content exceeds 0.10%, and the Y content exceeds 0.20%, a low melting point compound is selected. Since it is easy to generate and conversely deteriorates the hot workability, the rare earth element content is 0.10% or less, the Mg content is 0.10% or less, the Ca content is 0.10% or less, and Y The content was determined to be 0.20% or less.

So) Fe Fe has the effect of securing the strength of the alloy and reducing the Ni content to reduce the alloy price, so the balance component was essentially Fe.

B) Balance of Cr, Mo and W contents Elution (corrosion) of Ni alloy in H ₂ S-CO ₂ -Cl ^-- S environment is
Depends on Cr, Ni, Mo, W, and Cu and Nb. That is, the corrosion resistance is ensured by the surface coating made of these elements, and the content balance of these elements in the surface coating is the most important factor in determining the corrosion resistance.
For stress corrosion cracking under the above oil well environment, Mo is
It has 10 times the effect, and W has 5 times the effect of Cr. The content of Cr is 15 to 30% and Cu is 0.30 to
When 3.0%, Nb is 0.30 to 3.0% and Ni is 45% or more, a corrosion resistant coating having excellent resistance to stress corrosion cracking can be obtained even in an environment containing elemental sulfur (S).

That is, when the content balance of Cr, Mo and W is in the range of Cr (%) + 10Mo (%) + 5W (%) <140, it is sufficient in the H ₂ S-CO ₂ -Cl ^-- S environment of about 250 ° C or less. Corrosion resistance is lost.

Other elements such as B, Sn, Zn, and Pb do not have any adverse effect on the characteristics of the alloy of the present invention in a trace amount, so 0.10% of each is allowed as an impurity, but exceeds this upper limit. Therefore, care must be taken as it will adversely affect the workability and corrosion resistance.

Next, the present invention will be described with reference to Examples and comparison with Comparative Examples.

<Example> First, after melting each alloy having the chemical composition shown in Table 1, it is hot-worked into a plate material, which is cold-worked to about 20% to obtain a desired strength (room temperature). At 0.2% proof stress of 70
~100kgf / mm ²⁾ was obtained. From this plate material, test pieces to be subjected to a tensile test, an impact test and a corrosion test were sampled, and various tests were carried out in the following manner.

In addition, the material that has been subjected to the hydrogen crack resistance test is 1000 hours at 300 ° C.
After being subjected to a heat treatment of r for a long time, a test piece was prepared.

(A) Tensile test Test temperature: Room temperature, Specimen: 4.0mmφ, GL is 20mm, (B) Sharpy impact test Test temperature: 0 ℃, Specimen: 10mm × 10mm × 55mm with 2mm V notch, (c) Stress corrosion cracking test Corrosion solution: 20% NaCl-1g / ls- (0.1, 1, 10) atmH ₂ S-20 atmCO ₂ , test temperature: 250 ° C, immersion time: 500hr, additional stress: 1σ _y , test piece: 10mm width × 2mm Thickness x 75 mm with R0.25U notch, (D) Hydrogen crack resistance test NACE condition: 5% NaCl-0.5% CH ₃ COOH -1 atmH ₂ S, test temperature: 25 ° C, immersion time: 720 hr, additional stress: 1σ _y , Test piece: 10mm width x 2mm thickness x 75mm length with R0.25U notch.

The test results thus obtained are also shown in Table 1.

The results of the corrosion test are shown by "◯" for "no crack or pitting corrosion" and "x" for "cracking or pitting corrosion after the test".

From the results shown in Table 1, it is clear that the alloy of the present invention exhibits excellent corrosion resistance even in a harsh corrosive environment, while the composition of the alloy is in accordance with the conditions specified by the present invention. It can be seen that none of the comparative alloys that have deviated exhibit sufficient corrosion resistance.

In addition, Fig. 4 shows these results as "Ni content" of the alloy.
It is a graph arranged by the relation between "Cr (%) + 10Mo (%) + 5W (%)". Also from this Fig. 4, "Cr (%) + 10
It is clear that sufficient corrosion resistance is not exhibited unless the value of “Mo (%) + 5W (%)” is 140 or more.

<Overall Effect> As described above, according to the present invention, sulfur (S)
Has excellent corrosion resistance even under sour gas environment where there is a simple substance, especially high strength Ni-based alloy suitable for oil country tubular goods having stress corrosion cracking resistance and hydrogen cracking resistance, etc. Is obtained.

[Brief description of drawings]

FIG. 1 is a graph showing the relationship between P content and hydrogen cracking resistance (elongation in corrosive solution / elongation in air) in the alloy of the present invention, and FIG. 2 is S content in the alloy of the present invention. 3 is a graph showing the relationship between the amount and hot workability (drawing ratio at 1150 ° C.), and FIG. 3 shows the Nb content and stress corrosion cracking resistance (corrosion resistance) in alloys having the same composition as the present invention except Nb. FIG. 4 is a graph showing the relationship between (elongation in solution / elongation in air), and FIG.
It is a graph arranged by the relationship between "content" and "Cr (%) + 10Mo (%) + 5W (%)".

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Shiro Mukai 1-3, Nishi-Nagasumotodori, Amagasaki City, Hyogo Prefecture Sumitomo Metal Industries, Ltd. Central Research Laboratory (56) Reference JP-A-60-110856 (JP, A) JP-A-60-2563 (JP, A)

Claims (4)

[Claims] 1. By weight ratio, C: 0.10% or less, Si: more than 0.05 to 0.30%, Mn: 2.0% or less, P: 0.030% or less, S: 0.0050% or less, Ni: 45 to 60%, Cr : 15 to 30%, one or more of Mo and W: Mo is less than 16%, W is 5.0% or less, and Satisfying the following conditions: Cu: 0.30-3.0%, Ti: 2.0% or less, Nb: 0.30-3.0%, Al: 1.0% or less, N: 0.050% or less, Fe and other unavoidable impurities: A highly corrosion-resistant Ni-based alloy having excellent stress corrosion cracking resistance and hydrogen cracking resistance, characterized by having a composition that satisfies the formula Cr (%) + 10 Mo (%) + 5W (%) ≥ 140. 2. By weight ratio, C: 0.10% or less, Si: more than 0.05 to 0.30%, Mn: 2.0% or less, P: 0.030% or less, S: 0.0050% or less, Ni: 45 to 60%, Cr : 15 to 30%, one or more of Mo and W: Mo is less than 16%, W is 5.0% or less, and Content of Cu: 0.30 to 3.0%, Ti: 2.0% or less, Nb: 0.30 to 3.0%, Al: 1.0% or less, N: 0.050% or less, and further Co: 5.0% or less, V, Ta , One or more of Zr and Hf: each including one or more of 1.0% or less, Fe and other unavoidable impurities: Consist of the rest, and (%) + 10Mo (%) + 5W (%) ≧ 140 A highly corrosion-resistant Ni-based alloy excellent in stress corrosion cracking resistance and hydrogen cracking resistance, characterized in that it has a composition that satisfies the formula. 3. By weight ratio, C: 0.10% or less, Si: more than 0.05 to 0.30%, Mn: 2.0% or less, P: 0.030% or less, S: 0.0050% or less, Ni: 45 to 60%, Cr : 15 to 30%, one or more of Mo and W: Mo is less than 16%, W is 5.0% or less, and Content of Cu: 0.30 to 3.0%, Ti: 2.0% or less, Nb: 0.30 to 3.0%, Al: 1.0% or less, N: 0.050% or less, and a rare earth element: 0.10% or less, Mg: Includes at least one of 0.10% or less, Ca: 0.10% or less, Y: 0.20% or less, Fe and other unavoidable impurities: consisting of the rest, and Cr (%) + 10Mo (%) + 5W (%) A highly corrosion-resistant Ni-based alloy excellent in stress corrosion cracking resistance and hydrogen cracking resistance, characterized by having a composition that satisfies the formula ≧ 140. 4. By weight ratio, C: 0.10% or less, Si: more than 0.05 to 0.30%, Mn: 2.0% or less, P: 0.030% or less, S: 0.0050% or less, Ni: 45 to 60%, Cr : 15 to 30%, one or more of Mo and W: Mo is less than 16%, W is 5.0% or less, and Content of Cu: 0.30 to 3.0%, Ti: 2.0% or less, Nb: 0.30 to 3.0%, Al: 1.0% or less, N: 0.050% or less, and further Co: 5.0% or less, V, Ta , One or more of Zr and Hf: 1.0% or less of each, and one of rare earth elements: 0.10% or less, Mg: 0.10% or less, Ca: 0.10% or less, Y: 0.20% or less Including the above, Fe and other unavoidable impurities: the rest, and the composition is such that Cr (%) + 10Mo (%) + 5W (%) ≥ 140 High corrosion resistance Ni-based alloy with excellent stress corrosion cracking resistance and hydrogen cracking resistance.