AU2003289437B2

AU2003289437B2 - High-strength martensitic stainless steel with excellent resistances to carbon dioxide gas corrosion and sulfide stress corrosion cracking

Info

Publication number: AU2003289437B2
Application number: AU2003289437A
Authority: AU
Inventors: Hideki Takabe; Masakatsu Ueda
Original assignee: Nippon Steel Corp
Current assignee: Nippon Steel Corp
Priority date: 2002-12-20
Filing date: 2003-12-18
Publication date: 2007-09-20
Anticipated expiration: 2023-12-18
Also published as: RU2307876C2; US20050224143A1; AR042494A1; NO20052986L; BRPI0317550B1; CN100368579C; NO20052986D0; AU2003289437A1; MXPA05006562A; JPWO2004057050A1; CA2509581C; RU2005122929A; EP1584699A4; NO337858B1; BR0317550A; JP4428237B2; CA2509581A1; CN1729306A; EP1584699A1; WO2004057050A1

Description

DESCRIPTION

HIGH STRENGTH MARTENSITIC STAINLESS STEEL EXCELLENT IN CARBON DIOXIDE GAS CORROSION RESISTANCE AND SULFIDE STRESS-CORROSION CRACKING RESISTANCE FIELD OF THE INVENTION The present invention relates to a steel material suitable for its use in severe corrosion environment containing corrosive materials such as carbon dioxide gas, hydrogen sulfide, chlorine ions and the like. Specifically, the present invention relates to a steel material for a seamless steel tube and a seam welded steel tube such as an electric resistance welding steel tube, a laser welding steel tube, a spiral welding tube or the like, which is used in applications for petroleum or natural gas production facilities, facilities for eliminating carbon dioxide gas, or for geo-thermal power generation, or for a tank for liquid containing carbon dioxide gas, especially to a steel material for oil well tubes for oil wells or gas wells.

BACKGROUND ART From the viewpoint of exhaustion of petroleum resources, which is expected in the near future, development of an oil well under severe environment that is an oil well in a deeper layer, of a sour gas field or the like, has often been performed. Thus, high strength and excellent corrosion resistance and sulfide stress corrosion cracking resistance are required for oil well steel tubes, which are used in such uses.

As a steel material for oil well tubes or the like, carbon steel or a low-alloy steel has been generally used. However, as the environment of the well becomes severe, steel which contains increased amount of alloying elements, has been used.

For example, as oil wells for steel material which contain a large amount of carbon Idioxide gas, 13 Cr series martensitic stainless steel such as typical SUS 420 and the like tb3 ;have been used.

However, although the SUS 420 steel has excellent corrosion resistance to carbon dioxide gas, it has poor corrosion resistance to hydrogen sulfide. Thus, the SUS 420 steel is liable to generate sulfide stress-corrosion cracking (SSCC) under the environment containing carbon dioxide gas and hydrogen sulfide simultaneously.

¢€3 Therefore, various steel material in the place of the SUS 420 steel have been proposed.

o Japanese Patent No. 2861024, Japanese Patent Application Publication No. 00 S287455, and Japanese Patent Application Publication No. 07-62499 disclose steel O 10 having improved corrosion resistance by reducing carbon content of the SUS 420.

r However, such a low carbon-content steel described in these publications may not have the enough strength required for use in a deep well, that is proof stress of 860MPa or more.

Alternatively, Japanese Patent Application Publication No. 2000-192196 discloses steel of a martensitic single phase structure containing Co: 0.5-7% and Mo: 3.1-7% having high strength and excellent sulfide stress-corrosion cracking resistance.

The invention described in the publication is a steel containing Co in the abovementioned range to suppress the generation of retained austenite during cooling so that the structure is made to be a martensitic single phase. However, since Co is an expensive element, it is desirable not to use.

Any discussion of documents, acts, materials, devices, articles or the like which has been included in the present specification is solely for the purpose of providing a context for the present invention. It is not to be taken as an admission that any or all of these matters form part of the prior art base or were common general knowledge in the field relevant to the present invention as it existed before the priority date of each claim of this application.

SUMMARY OF THE INVENTION The present invention was made in consideration of the above-mentioned circumstances. It is desirable to provide a martensitic stainless steel having sufficient strength to use for oil well tubes for a deep well, that is high strength of a proof stress of 860 MPa or more, and excellent carbon dioxide 555215_1.doc gas corrosion resistance and sulfide stress-corrosion cracking resistance whereby it can be used even under the environment containing carbon dioxide gas, hydrogen sulfide or chlorine ions or two or more of them. The symbols of the respective elements in the following expression show the content (mass of each element.

Accordingly, the gist of the present invention is high strength martensitic stainless steels described in the following and A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 15 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 and N: 0.07 or less, and the balance Fe and impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises tempered martensite, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering.

Mo 2.3 0.89 Si 32. 2 C (1) wherein the symbols of the respective elements in the expression show the content (mass of each element.

Further, the gist of the present invention is martensitic stainless steels containing at least one of alloying elements selected from at least one group consisting of the following a first group, a second group and a third group, in addition to the components described in the above mentioned In this steel said expression is also satisfied and the microstructure is the same as mentioned above.

First group Ti: 0.005 0.25 V: 0.005 0.25 Nb: 0.005 0.25 and Zr: 0.005 0.25 Second group Cu: 0.05 1 Third group Ca: 0.0002 0.005 Mg: 0.0002 0.005 La: 0.0002 0.005 and Ce: 0.0002 0.005 A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including compositions defined in any one of and characterized in that steel, which satisfies the above mentioned expression is subjected to tempering in which (20 log t)(T 273) satisfies 13500 17700 when, after quenching the steel at a quenching temperature of 880 °C 1000 a range of a tempering temperature is set to 450 0 C 620 a tempering temperature is set to T (OC) and tempering time is set to t (hour), whereby the microstructure of said steel mainly comprises tempered martensite, carbide precipitated during tempering, and intermetallic compounds such as a Laves phase, a a phase and the like finely precipitated during tempering.

BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a view showing relationships between Mo contents of various types of steels tested in examples and the right side in the expression that is "2.3 0.89 Si 32. 2 C" (IM value).

FIG. 2 is a view for explaining tempering conditions defined in the present invention, which shows relationships between 0.2 proof stress obtained by changing values of (20 log t)(T 273) while changing tempering temperatures in 400 650 °C after quenching steel at 920 and the (20 log t)(T 273).

DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for restrictions of contents of various elements defined in the present inventors will be described hereinbelow. of the respective contents means mass C: 0.005-0.04 Although C (carbon) is an effective alloying element to enhance strength of steel, from a viewpoint of corrosion resistance small C content is preferable.

However, if the content of C is less than 0.005%, proof stress does not reach 860 Mpa or more. Thus, the lower limit of the C content was set to 0.005 On the other hand, if the C content exceeds 0.04 the hardness of the tempered steel becomes hard excessively, the steel has high sulfide stress-corrosion cracking sensibility.

Accordingly, the C content was set to 0.005 0.04 Si: 0.5 or less Si (Silicon) is an alloying element necessary as a deoxidizer. An amount of Si retained in the steel may be a level of impurities. However, to obtain a large deoxidation effect it is preferred that the Si content is set to 0.01% or more. On the other hand, if the Si content exceeds 0.5 the toughness of the steel is decreased and the workability of the steel is also decreased. Accordingly, the Si content was set to 0.5 or less.

Mn: 0.1 3.0 Mn (Manganese) is an effective alloying element to enhance the hot workability. To obtain this effect Mn content of 0.1 or more is needed. On the other hand, if the Mn content exceeds 3.0 the effect is saturated resulting in an increase in cost. Accordingly, the Mn content was set to 0.1 3.0 P: 0.04 or less P (Phosphorus) is an impurity element contained in the steel and the P content is better as low as possible. Particularly, if the P content exceeds 0.04 the sulfide stress-corrosion cracking resistance is remarkably decreased.

Accordingly, the P content was set to 0.04 or less.

S: 0.01% or less S (Sulfur) is an impurity element contained in the steel and the S content is better as low as possible. Particularly, if the S content exceeds 0.01 the hot workability, corrosion resistance and toughness are remarkably decreased.

Accordingly, the S content was set to 0.01 or less.

Cr: 10- 15 Cr (Chromium) is an effective alloying element to enhance the carbon dioxide gas corrosion resistance. To obtain this effect Cr content of 10 or more is needed. On the other hand, if the Cr content exceeds 15 it becomes difficult to make the microstructure of tempered steel a martensite phase mainly. Accordingly, the Cr content was set to 10 15 Ni: 4.0 8 Ni (Nickel) is an alloying element, which is necessary for making the microstructure of tempered steel a martensite phase mainly. However, if the Ni content is 4.0 or less, a number of ferrite phases were precipitated in the microstructure of tempered steel and the microstructure of tempered steel does not become a martensite phase mainly. On the other hand, if the Ni content exceeds 8 the microstructure of tempered steel becomes an austenite phase mainly.

Accordingly, the Ni content was set to 4.0 8 More preferably the Ni content was set to 4 7 Mo: 2.8 5.0 Mo (Molybdenum) is an effective alloying element to enhance the sulfide stress-corrosion cracking resistance for a high strength material. To obtain this effect Mo content of 2.8 or more is needed. However, if the Mo content exceeds this effect is saturated, resulting in an increase in cost. Accordingly, the Mo content was set to 2.8 5.0 Al: 0.001 0.10 Al (Aluminum) is an alloying element, which is used as a deoxidizer in a melting process. To obtain this effect Al content of 0.001 or more is needed.

However, if the Al content exceeds 0.10 many inclusions are formed in the steel so that the corrosion resistance is lost. Accordingly, the Al content was set to 0.001 0.10%.

N: 0.07 or less N (Nitrogen) is an impurity element contained in the steel and the N content is better as low as possible. Particularly, if the N content exceeds 0.07 many inclusions are formed so that the corrosion resistance is lost. Accordingly, the N content was set to 0.07 or less.

One of martensitic stainless steels according to the present invention consists the above-mentioned chemical composition as well as the balance Fe and indispensable impurities. Another martensitic stainless steel according to the present invention further contains, in addition to the above-mentioned components, at least one alloying element selected from at least one group consisting of a first group, a second group and a third group shown as follows. The components (elements) of the respective groups will be described below.

First group (Ti, V, Nb, Zr: 0.005 0.25 respectively) Since Ti, V, Nb and Zr have effect to fix C so as to reduce variations of strength, one or more selected from these elements may be optionally contained.

However, if any one of the elements is less than 0.005%, the above-mentioned effect cannot be obtained. On the other hand, if any one of the elements exceeds 0.25 the microstructure of the steel cannot become a martensite phase mainly so that highly strengthening of the steel with a proof stress of 860 MPa or more cannot be attained. Accordingly, the respective contents in selectively containing these elements were set to 0.005 0.25 Second group (Cu: 0.05 1 Cu is an effective element to make the microstructure of tempered steel a martensite phase mainly like Ni. To obtain the effect by the addition of Cu the Cu content may be 0.05 or more. However, if the Cu content exceeds 1 the hot workability of the steel is lowered. Accordingly, when Cu is contained in the steel the Cu content was set to 0.05 1 Third group (Ca, Mg, La, Ce: 0.0002 0.005 respectively) Since Ca, Mg, La and Ce are effective elements to enhance the hot workability of the steel, one or more selected from these elements may be optionally contained. However, if any one of the elements is less than 0.0002 the above-mentioned effect cannot be obtained. On the other hand, if any one of the elements exceeds 0.005 coarse oxide is formed in the steel whereby the corrosion resistance of the steel is decreased. Accordingly, the respective contents in selectively containing these elements were set to 0.0002 0.005 Particularly, it is preferred to contain Ca and/or La in the steel.

The steel according to the present invention should have the above-mentioned chemical composition and satisfy the following expression This is because, if the steel satisfies the expression strength of the steel can be enhanced to proof stress of 860 MPa or more without deteriorating sulfide stress-corrosion cracking resistance.

Mo E12.3 0.89 Si 32.2 C (1) wherein the symbols of the respective elements in the expression show the content (mass of each element.

FIG. 1 is a view showing relationships between Mo contents of various types of steels tested in examples, which will be described later, and the right side in the expression that is "2.3 0.89 Si 32. 2 C" (IM value). Specifically, the results shown in FIG. 1 are based on steels of the present invention and comparative steels (test Nos. 18 21). The mark shows an example that did not generate rupture in a sulfide stress-corrosion cracking test, and the mark shows an example that generated rupture therein. Even if the Mo content exceeds 2.8 if the Mo content does not satisfy the expression the steel has a poor sulfide stress-corrosion cracking resistance.

When Mo content is out of a range (that is less than 2.8 defined in the present invention, the 0.2 proof stress of the steel is less than 860 MPa. Further, even if Mo content is in a range (that is 2.8 5 defined in the present invention, if the Mo content does not satisfy the above-mentioned expression the 0.2 proof stress of the steel is less than 860 MPa.

However, if steel satisfies the above-mentioned expression the 0.2 proof stress of the steel reaches 860 MPa or more and the steel can endure the use of an oil well steel material due to its sufficient strength. Accordingly, the steel according to the present invention should be in a range of said chemical composition and satisfy the above-mentioned expression Further, the present inventors have checked the influences of microstructure. As a result the present inventors have found that if the microstructure is a structure mainly comprising tempered martensite, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering, the strength of the steel can be enhanced without deteriorating sulfide stress-corrosion cracking resistance.

It is noted that "mainly comprising tempered martensite" means that a vol or more of the microstructure of the steel is a tempered martensitic structure, and a retained austenitic structure and/or a ferritic structure other than a tempered martensitic structure may be present.

Further, the "intermetallic compounds such as Laves phase, a phase and the like" may contain intermetallic compounds such as p phase andx phase other than Laves phase such as Fe2Mo and the like and a phase.

The microstructure of the steel according to the present invention contains carbide precipitated during tempering. Although carbide is an effective microstructure to ensure the strength of the steel, high strength of proof stress of 860 MPa or more cannot be realized by only carbide contained in the steel.

Accordingly, in the present invention precipitation of carbide as well as fine precipitation of intermetallic compounds such as the above-mentioned Laves phase, a phase and the like are needed.

Heat treatment for the steel of the present invention is typical quenching-tempering. To precipitate fine intermetallic compounds during tempering it is necessary to sufficiently dissolve the intermetallic compounds during quenching. The quenching temperature is preferably 880 1000 "C.

Further, conditions in which intermetallic compounds such as a fine Laves phase, c phase and the like are precipitated and 0.2 proof stress of 860 MPa or more can be obtained resides in a case where when a temperature range for tempering is 450 620 as well as the tempering temperature is set to and the tempering time is set to t (hour), (20 log t)(T 273) can satisfy 13500 17700.

FIG. 2 is a view for explaining tempering conditions defined in the present invention. FIG. 2 shows relationships between 0.2 proof stress obtained by changing values of (20 log t)(T 273) while changing tempering temperatures in 400 650 °C after quenching steel at 920 and the (20 log t)(T 273).

As shown in FIG. 2,when (20 log t)(T 273) is in a range of 13500 17700, 0.2 proof stress reaches 860 MPa or more.

When tempering is performed at a condition that (20 log t)(T 273) exceeds 17700, dislocation density is reduced or imtermetallic compounds are dissolved in microstructure of the steel, whereby high strengthening of 0.2 proof stress of 860 MPa or more cannot be attained. On the other hand, when the steel is tempered at a condition of less than 13500, intermetallic compounds and carbide are not precipitated. Accordingly, 0.2 proof stress of 860 MPa or more cannot be attained.

From the above-mentioned principal, the steel of the present invention should have the above-mentioned chemical compositions and satisfy the expression and the microstructure of the steel should be mainly comprising tempered martensite, carbide precipitated during tempering, and intermetallic compounds such as a Laves phase, a phase and the like finely precipitated during tempering.

(Examples) Steels having chemical compositions shown in Tables 1 and 1 were melted and cast, and the obtained cast ingots were forged and hot rolled to prepare steel plates each having a thickness of 15 mm, a width of 120 mm and a length of 1,000 mm. These steel plates were subjected to quenching (water cooling at 920 "C) and tempering [air cooling after soaking at 550 "C for 30 min. ((20 log t)(T 273) 16212], and the obtained steel plates were provided in various tests as testing steel plates.

Table 1 (1) Test Chemical composition (mass o-V No. C Si I Mn I P S CeuJ Cr NiM.oI Al] N INb VI Ti Zr Ca Mg La Ce I au 0.014 1 0.17 1 .4 0.015 10.0010 11.81 j6.85 2.93 0.030 0.0055 2.60 0.33 2 0.016 0.17 .0.46 0.015 0.0010 12.08 6.90 2.93 0.030 0.0055 0.060 2.66 0.27 3 0.026 0.18 0.87 0.016 0.0011 0.08 12.02 7.67 4.50 0.028 0.0050 0.040 0.003 2.98 1.52 4 0.034 0.04 0.44 0.015 0.0010 0.04 12.01 7.39 3.88 0.034 0.0062 0.040 0.091 3.36 0.52 0.008 0.48 0.41 0.011 0.0010 0.98 11.98 7.87 3.98 0.024 0.0050 0.05 0.105 0.040 0.0009 0.0010 2.13 1.85 6 0.015 0.17 0.98 0.015 0.0010 10.11 4.21 2.98 0.030 0.0055 0.004 0,0005 2.63 0.35 7 0.017 0.17 1.02 0.015 0.0010 1 14.10 7.92 12.88 0.030 10.0066 0.060 2.70 0.18 8 0.016 0.15 0.23 0.013 0.0009 12.10 6.87 2.86 0.025 10.0065 0.004 2.68 0.28 9 0.015 0.15 1.44 0.012 0.0008 12.07 6.85 2.91 0.025 0.0066 0.060 1 2.65 0.26 0.014 0.18 0.44 0.015 0.0008 0.28 12.01 6.91 2.96 0.034 0.0062 10.040 0.091 2.59 0.37 11 0.014 0.21 0.44 0.015 0.0010 0.85 12.01 6.55 2.97 0.034 0.0062 0.040 0.092 2.56 0.41 12 0.014 0.20 0.44 0.015 0.0010 1.54 12.01 6.25 2.97 0.034 0.0062 0.040 0.091 2.57 0.40 13 0.015 0.18 0.43 0.017 0.0090 2.70 12.08 5.85 2.96 0.030 0.0642 0.060 0.088 2.62 0.34 14 0.014 0.17 0.47 0.014 0.0012 0.48 12.08 6.90 2.96 0.027 0.0074 2:60 0.36 0.016 0.15 10.67 0.015 [0.0010 12.01 6.78 2.94 0.030 .0.0059 0.0005 2.68 0.26 16 0.014 0.02 0.46 0.012 0.00091 11.99 6.89 2.91 0.025 0.0065 0.098 0.0004 2.74 0.17 0.015 0.17 0.44 0.014 10.0010 12.01 1 6.88 12.88 0.027 1 0.0067 0.0007 2.63 0.23 I 0. 0007 2.63 0.23 Note 1) Mark shows out of range defined in the present inventin. Note 2) IM value shows (2.3 0.89 Si 32.2C) Note 3) Mo IM value shows a calculated value of (Mo content IM value), and if this value is 0 or more, it satisfied the expression defined in the present invention.

Table 1 (2) Test Chemical composition (mass N. C Si Mn P S CU Cr Ni MO Al N Nb V Ti Zr Ca Mg La Ce I 1

-I

18 0.018 0.17 0.45 0.012 0.0012 0.04 10.50 6.11 2.44 0.048 0.0064 0.030 0.101 2.73 *-.29 19 0.012 0.11 0.44 0.011 .0.0010 0.03 12.08 6.15 2.46 0.043 0.0062 0.080 0.098 2.59 *-.13 008 00 .5 005 0011 00 27 .5 26 .5 .05 .4 .6 .6 0.028 0.05 0.45 0.015 0.0011 0.03 12.70 6.45 2.61 0.058 0.0055 0.040 0.067 2 .16 '.Q11 c~22 0.018 0.15 0.46 0.015 0.0009 0.03 12.30 6.34 *1.51 0.032 0.0060 0.040 0.003 2.75 *-.24 S 23 0.017 0.16 0.45 0.015 0.0011 0.03 11.98 6.38 *0.98 0.035 0.0061 0.050 0.100 0.098 2.71 *-.73 r 24 0.023 0.17 0.43 0.014 0.0011 0.03 11.97 6.48 *2.04 0.034 0.0058 0.040 0.097 2.89 0.015 0.35 0.44 0.013 0.0011 0.03 *9.50 6.01 2.46 0.011 0.0053 050 0.088 2.47 *-.01 N~ote 1) IVIark. shows out of range defined in the present invention.

Note 2) IM value shows (2.3 0.89 Si 32.2C) Note 3) Mo IM value shows a calculated value of (Mo content TM value), and if this value is 0 or more, it satisfied the expression (1) defined in the present invention.

First, round bar test pieces each having a diameter of 6.35 mm and a length of the parallel portion of 25. 4 mm were taken from the respective testing steel plates and subjected to tensile tests at normal temperatures. The obtained 0.2 proof stresses are shown in Table 2.

Then, test pieces each having a thickness of 3 mm, a width of 20 mm and a length of 50 mm were taken from the respective testing steel plates and these testing pieces were polished with a No. 600 emery paper and degreased and dried. Then the obtained testing pieces were immersed into 25% NaC1 water solution saturated with 0.973 MPa CO 2 gas and 0.0014 MPa H 2 S gas (temperature: 165 for 720 hours.

After the immersion weight reductions of the test pieces by corrosion [(mass before testing) (mass after testing)] were measured and the presence and absence of local corrosion on surfaces of the testing pieces were confirmed by a visual test.

As a result the corrosion rate of the steel according to the present invention is mm/year or less, and no local corrosion on its surface could be found.

Subsequently, examples in which 0.2 proof stresses were 860 MPa or more in the tensile tests were subjected to fixed load tests by use of a spring type (proof ring type) testing machine in accordance with TM0177-96 Method A of NACE.

Specifically, round bar test pieces each having a diameter of 6.3 mm and a length of the parallel portion of 25. 4 mm were taken from the respective testing steel plates and subjected to 0.2 proof stress-85 (test stress) fixed load tests at a test temperature of 25 for 720 hours by use of 0.003 MPa H 2 S gas (CO 2 bal.) saturated NaC1 water solution (pH As a result all test pieces were not ruptured.

The Microstructures of the test pieces were observed by an optical microscope and an extraction replica. These results are also shown in Table 2.

Table 2 Te 0 Poof Carbon dioxide SSC Test 0.2 Poof No. stress (MPa) gas corrosion Corrosion Microstructure test test 1 951 o o M IM C 2 944 o o M IM C 3 1,007 o o M IM C 4 1,027 o o M IM C 1,020 o o M IM C 6 910 o o M IM C W 7 882 o o M F+ IM+ C 8 944 o o M IM C 9 965 o o M IM C S 10 972 o o M IM C S 11 958 o o M IM C 2 12 951 o o M IM C 13 965 o o M IM C 14 958 o o M IM C 972 o o M IM C 16 882 o o M IM C 17 979 o o M IM C m 18 841 o x M+C 1 19 843 o x M+C 858 o x M+C 21 840 o x M+C S 22 829 o x M+C S 23 832 o x M+C o 24 849 o x M+C 841 x x M+C Note 1) In carbon dioxide gas corrosion test a steel, whose corrosion rate is 0.5 mm/y or less, and which did not generate local corrosion, is shown by and otherwise Note 2) In SSC test, a steel, which did not generate rupture, is shown by and a steel, which generated rupture, is shown by Note 3) In microstructure, tempered martensite is shown by ferrite is shown by intermetallic compounds are shown by "IM" and carbide is shown by As shown in Table 2, examples Nos. 1 to 17 of the present invention each have 0.2 proof stress of 860 MPa or more and excellent carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance. On the other hand, comparative examples Nos. 22 to 25, which have Cr and/or Mo contents out of range defined in the present invention, and comparative examples Nos. 18 to 21, which have the content ranges of the respective components are in the range defined in the present invention but the expression previously described was not satisfied, were not sufficient in carbon dioxide gas resistance and/or stress cracking resistance.

INDUSTRIAL APPLICABILITY The martensitic stainless steel according to the present invention can have high strength of 0.2 proof stress of 860 MPa or more and excellent carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance by limiting the steel composition of specified elements and defining Mo content in the steel by relationships with IM values as well as by forming microstructure of the steel with tempered martensite mainly, carbide precipitated during tempering, and intermetallic compounds such as a Laves phase, a a phase and the like. As a result the martensitic stainless steels of the present invention can be applied to practical steels, which can be widely used in oil well tubes and the like under environment including carbon dioxide gas, hydrogen sulfide, chlorine ions or two or more of them, in wide fields.

Claims

2. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 and N: 0.07 or less, and further containing one or more selected from a group consisting of Ti: 0.005 0.25 V: 0.005 0.25 Nb: 0.005 0.25 and Zr: 0.005 0.25 and the balance Fe and impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises a tempered martensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element.
3. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 N: 0.07 or less, and Cu: 0.05 I and the balance Fe and impurities, and also characterized by satisfying the 555215 l.doc expression given below wherein the microstructure mainly comprises a tempered Smartensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element. 00
4. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 N: 0.07 or less, and Cu: 0.05 1 and further containing one or more selected from a group consisting of Ti: 0.005 0.25 V: 0.005 0.25 Nb: 0.005 0.25 and Zr: 0.005 0.25 and the balance Fe and impurities, and also characterized by satisfying the expression (1) given below wherein the microstructure mainly comprises a tempered martensite of volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 and N: 0.07 or less, and further containing one or more selected from a group consisting of Ca: 0.0002 0.005 Mg: 0.0002 0.005 La: 0.0002 0.005 and Ce: 0.0002 0.005 and the balance Fe and impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises a tempered martensite of volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo- 2.3 0.89Si 32.2C...(1) 555215 1.doc 1 wherein the symbols of the respective elements in the expression show the content S(mass of each element.
6. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 00 15 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 and N: 0.07 or less, and further containing one or more selected from a group consisting of Ti: 0.005 0.25 0 10 V: 0.005 0.25 Nb: 0.005 0.25 and Zr: 0.005 0.25 and one or more CNI selected from a group consisting of Ca: 0.0002 0.005 Mg: 0.0002 0.005 La: 0.0002 0.005 and Ce: 0.0002 0.005 and the balance Fe and impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises a tempered martensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element.
7. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 15 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 N: 0.07 or less, and Cu: 0.05 1 and further containing one or more selected from a group consisting of Ca: 0.0002 0.005 Mg: 0.0002 0.005 La: 0.0002 0.005 and Ce: 0.0002 0.005 and the balance Fe and impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises a tempered martensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element. 555215 1.doc S8. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including, by mass C: 0.005 0.04 Si: 0.5 or less, Mn: 0.1 3.0 P: 0.04 or less, S: 0.01 or less, Cr: 10 Ni: 4.0 8 Mo: 2.8 5.0 Al: 0.001 0.10 N: 0.07 or less, and Cu: 0.05 1 and further containing one or more selected from a group consisting of Ti: 0.005 0.25 V: 0.005 0.25 Nb: 0.005 0.25 and Zr: 0.005 0.25 and one or more selected from a group consisting of Ca: 0.0002 0.005 Mg: 0.0002 O 10 0.005 La: 0.0002 0.005 and Ce: 0.0002 0.005 and the balance Fe and CN impurities, and also characterized by satisfying the expression given below wherein the microstructure mainly comprises a tempered martensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, o phase and the like finely precipitated during tempering: Mo 2.3 0.89Si 32. 2 wherein the symbols of the respective elements in the expression show the content (mass of each element.
9. A high strength martensitic stainless steel excellent in carbon dioxide gas corrosion resistance and sulfide stress-corrosion cracking resistance and having 0.2 proof stress of 860 MPa or more, characterized by including compositions defined in any one of Claims 1 to 8 and characterized in that steel, which satisfies the expression given below, is subjected to tempering in which (20 log t)(T 273) satisfies 13500 17700 when, after quenching the steel at a quenching temperature of 880 "C 1000 a range of a tempering temperature is set to 450 °C 620 a tempering temperature is set to T and tempering time is set to t (hour), whereby the microstructure of said steel mainly comprises a tempered martensite of 70 volume or more, carbide precipitated during tempering, and intermetallic compounds such as Laves phase, a phase and the like finely precipitated during tempering: Mo_ 2.3 0.89Si 32.2C...(1) wherein the symbols of the respective elements in the expression show the content (mass of each element. 555215 1.doc