JP5842769B2 - Duplex stainless steel and manufacturing method thereof - Google Patents

Description

  The present invention relates to a duplex stainless steel composed of a ferrite phase and an austenite phase and a method for producing the same.

  The duplex stainless steel is excellent in corrosion resistance and weldability, and is particularly excellent in seawater corrosion resistance and strength compared to ferritic stainless steel or austenitic stainless steel. Therefore, it is possible to easily reduce the thickness of the material, and it has been widely used as an industrial material having economic efficiency for a long time.

  In particular, high Cr-high Mo duplex stainless steel has excellent corrosion resistance and strength, so it can be used in various fields such as line pipes, heat exchanger parts, process steel pipes / piping for oil and chemical industries, and oil well pipes. Has been. In recent years, umbilical tubes and the like for oil wells are required to have higher strength materials as the oil wells become deeper and thinner, and the performance of hydrogen embrittlement characteristics is also newly required. However, the higher the Cr and Mo contents in the duplex stainless steel, the easier the hard and brittle intermetallic compounds (σ phase, χ phase) precipitate in the temperature range of about 800 to 1000 ° C. This is due to the following reason.

  A solid billet of duplex stainless steel is made by cooling a long steel piece obtained by hot forging or hot rolling of a steel ingot and then subjecting the steel piece to machining such as cutting and cutting. Manufactured. In the high Cr-high Mo duplex stainless steel, the σ phase is precipitated particularly when allowed to cool, and the material is markedly hardened. Therefore, cracks are likely to occur, and cutting and cutting become difficult during various processes. Therefore, it is desirable in production to suppress the precipitation of the σ phase as much as possible. Conventionally, various proposals such as reduction of Cr and Mo contents, change of heat treatment conditions, change of cooling conditions, and the like have been made.

  For example, Patent Document 1 proposes a duplex stainless steel having a structure stability index PSI (= 3Si + Cr + 3.3Mo) of 40 or less. In Patent Document 1, it is assumed that no σ phase or the like is generated under the heating conditions, heat treatment conditions, and welding conditions during normal hot working of duplex stainless steel.

  In Patent Document 2, in a method of manufacturing a seamless steel pipe by heating a duplex stainless steel to 1110 ° C. or higher and then performing hot working, a temperature range satisfying 800 + 5Cr + 25Mo + 15W ≦ T (° C.) ≦ 1150 after the end of final rolling. There has been proposed a method for producing a duplex stainless steel that is rapidly reheated and then rapidly cooled. In Patent Document 2, it is said that a high-strength duplex stainless steel pipe having excellent corrosion resistance and no σ phase can be produced.

  Patent Document 3 proposes a duplex stainless steel in which the ferrite amount and the PRE value are in a predetermined range. In patent document 3, it is supposed that the duplex stainless steel excellent in seawater resistance will be obtained by this. Patent Document 4 proposes a duplex stainless steel in which the Mo content is reduced to suppress the generation of the σ phase, and the ferrite content and PREW are in a predetermined range. In Patent Document 4, it is said that this makes it possible to obtain a duplex stainless steel having excellent warm workability, crevice corrosion resistance and structural stability.

  Patent Documents 5 and 6 propose duplex stainless steels in which the ferrite content and the PREW values and ratios of the austenite phase and the ferrite phase are within a predetermined range. In both Patent Documents 5 and 6, it is said that this makes it possible to obtain a duplex stainless steel having good corrosion resistance and structural stability.

JP-A-5-132741 Japanese Patent Laid-Open No. 9-241746 JP-T-2002-529599 Special table 2003-503596 gazette JP 2005-501969 JP-T-2005-501970

  As described above, when the contents of Cr and Mo, which are corrosion resistance improving elements, are reduced, the corrosion resistance and strength of the duplex stainless steel are impaired. On the other hand, in steels with high Cr and Mo contents, the σ phase precipitates during cooling after hot forging or hot rolling, during welding, during hot bending, and during cooling after the final product heat treatment. It's easy to do. In particular, if the σ phase is precipitated by cooling after the final product heat treatment, the product performance is significantly impaired. For this reason, in the prior art, it is shown that the chemical composition of steel, a structure state, heat treatment conditions, etc. are managed. However, in order to prevent σ phase precipitation in the cooling process after heat treatment, it is necessary to set the cooling start temperature to be equal to or higher than the σ phase precipitation temperature, and since heat treatment at a high temperature is applied, the structure becomes coarse and hydrogen brittle. Adversely affects chemical properties.

  The present invention was made to solve such a problem, can be increased strength without impairing the corrosion resistance as a duplex stainless steel, heat treatment temperature can be lowered by suppressing σ phase precipitation, It is another object of the present invention to provide a duplex stainless steel that exhibits fine hydrogen embrittlement resistance and a method for producing the same by obtaining a fine grain structure by combining cold working at a high workability.

  As a result of intensive studies to solve the above-mentioned problems, the present inventors have obtained the following knowledge.

  (A) The influence of each element on the σ phase sensitivity, ie, the impact value after aging treatment (900 ° C x 600 seconds) simulating the thermal history of billet cooling and welding for various duplex stainless steels Then, the σ phase nose and the cooling curve when the billet was allowed to cool were studied repeatedly. As a result, it is possible to adjust the components so that the σ phase sensitivity index X comprehensively represented by Si, Cu, Ni, Cr, Mo, and W, which are elements that affect the σ phase sensitivity, satisfies a predetermined condition. I found it effective.

  (B) As a result of investigating the influence of each element on the strength, adjusting the components so that the strength index Y represented by Cr, Mo, W and N, which are elements contributing to high strength, satisfies a predetermined condition. Was found to be effective. By satisfying the predetermined conditions of the indexes X and Y at the same time, a high-strength duplex stainless steel with suppressed σ phase precipitation can be provided.

  (C) It has been found that a fine grain structure of the product can be obtained by optimizing the cold working degree and the heat treatment temperature in the cold finishing in the duplex stainless steel. By satisfying predetermined conditions, a duplex stainless steel having excellent hydrogen embrittlement resistance can be provided.

  The present invention has been made on the basis of the above findings, and the gist thereof is the following duplex stainless steel and a method for producing the same.

(1) By mass%, C: 0.03% or less, Si: 0.3% or less, Mn: 3.0% or less, P: 0.040% or less, S: 0.008% or less, Cu: 0 0.2 to 2.0%, Ni: 5.0 to 6.5%, Cr: 23.0 to 27.0%, Mo: 2.5 to 3.5%, W: 1.5 to 4.0 %, N: 0.24 to 0.40% and Al: 0.03% or less, with the balance being Fe and impurities,
The σ phase sensitivity index X represented by the following formula (i) is 52.0 or less,
The strength index Y represented by the following formula (ii) is 40.5 or more, and the pitting corrosion resistance index PREW represented by the following formula (iii) is 40 or more.
In a cross section in the thickness direction parallel to the rolling direction, when a straight line parallel to the thickness direction from the surface to a depth of 1 mm is drawn, the number of boundaries between the ferrite phase and the austenite phase intersecting the straight line is 160 or more. A duplex stainless steel characterized by comprising:
X = 2.2Si + 0.5Cu + 2.0Ni + Cr + 4.2Mo + 0.2W (i)
Y = Cr + 1.5Mo + 10N + 3.5W (ii)
PREW = Cr + 3.3 (Mo + 0.5W) + 16N (iii)
However, each element symbol in the formulas (i) to (iii) means the content (% by mass) of each element.

(2) instead of a part of Fe, by mass percent, further Ca: 0.02% or less, Mg: 0.02% or less and B: containing one or more selected 0.02% hereinafter or al The duplex stainless steel as set forth in (1) above, wherein

(3) By mass%, C: 0.03% or less, Si: 0.3% or less, Mn: 3.0% or less, P: 0.040% or less, S: 0.008% or less, Cu: 0 0.2 to 2.0%, Ni: 5.0 to 6.5%, Cr: 23.0 to 27.0%, Mo: 2.5 to 3.5%, W: 1.5 to 4.0 %, N: 0.24 to 0.40% and Al: 0.03% or less, with the balance being Fe and impurities,
The σ phase sensitivity index X represented by the following formula (i) is 52.0 or less,
For a steel having a chemical composition in which the strength index Y represented by the following formula (ii) is 40.5 or more, and the pitting corrosion resistance PREW represented by the following formula (iii) is 40 or more,
A method for producing a duplex stainless steel, characterized in that a cold working provides a workability of 75% or more, and a solution heat treatment is performed at 1020 to 1100 ° C.

(4) The method for producing a duplex stainless steel according to the above (3), wherein the chemical composition of the steel is in mass% instead of a part of Fe, and further Ca: 0.02% or less, Mg: 0.02% or less and B: method for producing duplex stainless steel which is characterized by containing one or more selected 0.02% hereinafter or al.

  According to the present invention, since the precipitation of the σ phase is suppressed, the product heat treatment temperature can be processed at a low temperature, and by providing an appropriate cold work degree, many ferrite phases and austenite phases per unit depth. It is possible to obtain a duplex stainless steel having the following structure and excellent hydrogen embrittlement resistance.

It is a figure which shows the relationship between (sigma) phase sensitivity index X and the impact value after aging of 600 second at 900 degreeC. It is a figure which shows the relationship between the strength index Y and 0.2% yield strength YS.

1. Chemical composition The reasons for limiting each element are as follows. In the following description, “%” for the content means “% by mass”.

C: 0.03% or less C is an element effective for stabilizing the austenite phase. However, when the content is excessive, carbides are liable to precipitate and the corrosion resistance is deteriorated. Therefore, the C content is 0.03% or less. The C content is preferably 0.02% or less. When it is desired to obtain the above effect, it is preferable to contain 0.010% or more of C.

Si: 0.3% or less Si is an element effective for deoxidation of steel. However, when the content is excessive, the generation of the σ phase is promoted. Therefore, the Si content is 0.3% or less. The Si content is preferably 0.25% or less. Although the above effect is exhibited even in a small amount, it is preferable to contain 0.01% or more particularly when Si is used as a deoxidizing agent.

Mn: 3.0% or less Mn is an element that is effective for desulfurization and deoxidation at the time of melting and is effective for stabilizing the austenite phase. Mn is also an element that contributes to improvement of hot workability. Furthermore, Mn has the effect of increasing the solubility of N. However, when the content is excessive, the corrosion resistance is deteriorated. Therefore, the Mn content is 3.0% or less. The Mn content is preferably 2.5% or less. Although the above effect is exhibited even in a trace amount, when Mn is contained for desulfurization or deoxidation, it is preferable to contain 0.01% or more.

P: 0.040% or less P is an impurity element inevitably mixed in steel. When the content is excessive, the corrosion resistance and toughness deteriorate significantly. Therefore, the P content is 0.040% or less. The P content is preferably 0.030% or less.

S: 0.008% or less S, like P, is an impurity element that is inevitably mixed in steel and degrades the hot workability of steel. In addition, the sulfide becomes a starting point of pitting corrosion and deteriorates pitting corrosion resistance. Therefore, it is better that the S content is small. If it is 0.008% or less, there is no particular problem in practical use. The S content is preferably 0.005% or less.

Cu: 0.2 to 2.0%
Cu is an element that is particularly effective for improving the corrosion resistance in a low pH environment that is considered to have low reducing properties, for example, an H ₂ SO ₄ or H ₂ S environment. In order to obtain these effects, it is necessary to contain 0.2% or more of Cu. However, when excessively contained, not only the hot workability is deteriorated, but also the generation of the σ phase is promoted. Therefore, the Cu content is 2.0% or less. The Cu content is preferably 0.3% or more, and more preferably 0.4% or more. Moreover, it is preferable that Cu content is 1.5% or less, and it is more preferable that it is 0.8% or less.

Ni: 5.0 to 6.5%
Ni is an essential element for stabilizing austenite. If the Ni content is low, the amount of ferrite increases too much and the characteristics as a duplex stainless steel are lost. Further, since the solid solubility of N in ferrite is small, when the amount of ferrite increases, nitrides are likely to precipitate and the corrosion resistance deteriorates. Therefore, Ni is contained by 5.0% or more. On the other hand, when the Ni content is excessive, the precipitation of the σ phase is facilitated and the toughness is deteriorated. Therefore, the Ni content is 6.5% or less. The Ni content is preferably 5.3% or more, and preferably 6.0% or less.

Cr: 23.0-27.0%
Cr is an essential element for ensuring corrosion resistance and strength. If the Cr content is low, corrosion resistance sufficient to be called a so-called super duplex stainless steel cannot be obtained. Therefore, Cr is contained 23.0% or more. On the other hand, when the Cr content is excessive, the precipitation of the σ phase becomes remarkable, leading to a decrease in hot workability and a deterioration in weldability as well as a decrease in corrosion resistance. Therefore, the Cr content is 27.0% or less. The Cr content is preferably 25.0% or more, and preferably 26.0% or less.

Mo: 2.5-3.5%
Mo, like Cr, is an element effective for improving corrosion resistance, particularly for improving pitting corrosion resistance and crevice corrosion resistance. It is also an effective element for increasing the strength of steel. Therefore, it is necessary to contain 2.5% or more of Mo. On the other hand, when the content is excessive, the σ phase is likely to precipitate, so the Mo content is set to 3.5% or less. The Mo content is preferably 2.7% or more. Moreover, it is preferable that Mo content is 3.2% or less, and it is preferable that it is less than 3.0%.

W: 1.5-4.0%
W is an element that produces less intermetallic compounds such as the σ phase and improves corrosion resistance, particularly pitting corrosion resistance and crevice corrosion resistance, compared to Mo. Further, it is an element that is very effective for increasing the strength of steel. If an appropriate amount of W is contained, high corrosion resistance can be ensured without increasing the contents of Cr, Mo, and N. Therefore, it is necessary to contain 1.5% or more of W. However, even if W is excessively contained, the effect of improving the corrosion resistance is saturated, so the W content is 4.0% or less. The W content is preferably 1.8% or more, and more preferably 2.0% or more. Moreover, it is preferable that W content is 3.8% or less.

N: 0.24 to 0.40%
N is a strong austenite-forming element, and is an element effective for improving the thermal stability and corrosion resistance of duplex stainless steel and increasing the strength. In order to achieve an appropriate balance between the ferrite phase and the austenite phase, it is necessary to contain an appropriate amount of N in relation to the contents of Cr and Mo, which are ferrite forming elements. N, like Cr, Mo and W, also has an effect of improving the corrosion resistance of the alloy. Therefore, it is necessary to contain 0.24% or more of N. On the other hand, when the content is excessive, the toughness and corrosion resistance of the steel are deteriorated due to defects due to the generation of blowholes, the formation of nitrides due to the thermal effect during welding, and the like. Therefore, the N content is 0.40% or less. N is preferably contained in an amount exceeding 0.30%, and more preferably contained in an amount exceeding 0.32%.

Al: 0.03% or less Al is used as a deoxidizing agent, but if nitride (AlN) is formed, there is a concern that the toughness is lowered. Therefore, the Al content is 0.03% or less.

X: 52.0 or less Since each element of Si, Cu, Ni, Cr, Mo, and W is an element that easily generates a σ phase, each content is set within a predetermined range, and the following formula (i) Is required to be 52.0 or less. By adjusting the chemical composition so that the σ phase sensitivity index X is 52.0 or less, the impact value after aging at 900 ° C. for 600 seconds (JIS Z 2242: 2005) can be easily set to 20 J / cm ² or more. Excellent brittle cracking resistance is obtained. The σ phase sensitivity index X is preferably 51.0 or less. The lower limit of the σ phase sensitivity index X is not particularly defined, but is preferably 46.0 or more from the viewpoint of securing strength and corrosion resistance.
X = 2.2Si + 0.5Cu + 2.0Ni + Cr + 4.2Mo + 0.2W (i)
However, each element symbol in the formula (i) means the content (% by mass) of each element.

Y: 40.5 or more Since each element of Cr, Mo, W and N is a solid solution strengthening type element contributing to high strength, the respective contents are set within a predetermined range, and the following (ii) The strength index Y expressed by the formula needs to be 40.5 or more. By adjusting the chemical composition so that the strength index Y is 40.5 or more, the 0.2% proof stress YS becomes 620 MPa, and high strength can be achieved. The strength index Y is preferably 41.5 or more in order to obtain a sufficient strength enhancement effect. Although the upper limit of the strength index Y is not particularly defined, it is preferably 48.0 or less in order to suppress the σ phase precipitation.
Y = Cr + 1.5Mo + 10N + 3.5W (ii)
However, each element symbol in the formula (ii) means the content (% by mass) of each element.

PREW: 40 or more For each element of Cr, Mo, W and N, the respective contents are set within a predetermined range, and in order to improve the corrosion resistance of the duplex stainless steel of the present invention, particularly the seawater corrosion resistance. The pitting corrosion resistance index PREW represented by the following formula (iii) needs to be 40 or more. The pitting corrosion resistance index PREW is generally adjusted to be 35 or more, but in the duplex stainless steel of the present invention, the content of Cr, Mo and N is increased so that PREW is 40 or more. Thereby, remarkably excellent corrosion resistance can be obtained. The upper limit of the pitting corrosion resistance PREW is not particularly defined, but is preferably 48.0 or less in order to suppress the σ phase precipitation.
PREW = Cr + 3.3 (Mo + 0.5W) + 16N (iii)
However, each element symbol in the formula (iii) means the content (% by mass) of each element.

  The duplex stainless steel according to the present invention contains each of the above elements, with the balance being Fe and impurities. “Impurity” is a component that is mixed due to various factors of raw materials such as ores and scraps and the manufacturing process when manufacturing duplex stainless steel industrially, and does not adversely affect the present invention. Means what is allowed.

  The duplex stainless steel according to the present invention may contain at least one selected from Ca, Mg, B and rare earth elements in the following amounts in mass% instead of a part of Fe.

Ca: 0.02% or less Mg: 0.02% or less B: 0.02% or less Rare earth element: 0.2% or less All of Ca, Mg, B and rare earth elements segregate S of impurities at the grain boundaries. Since it is an element that suppresses this and improves hot workability, it may be contained in the welding material for duplex stainless steel according to the present invention. However, if these contents are excessive, a large amount of sulfides, oxides, carbides and nitrides as starting points of pitting corrosion are formed in the steel, and the corrosion resistance deteriorates. Therefore, when one or more selected from these elements is contained, Ca, Mg and B are preferably contained in a range of 0.02% or less, and rare earth elements in a range of 0.2% or less. In order to obtain the effect of improving the hot workability, it is preferable that Ca, Mg and B are each contained in 0.0003% or more, and the rare earth element is contained in 0.01% or more. Said Ca, Mg, B, and rare earth elements can contain only 1 type in them, or 2 or more types of composites. When two or more of these elements are contained, the total content is preferably 0.25% or less.

  The rare earth element is a general term for a total of 17 elements of Sc, Y and lanthanoid, and can contain one or more selected from these elements. The rare earth element content means the total amount of the above elements.

2. Metal structure The duplex stainless steel according to the present invention has a ferrite phase and an austenite phase that intersect the straight line when a straight line parallel to the thickness direction from the surface to a depth of 1 mm is drawn in the cross section in the thickness direction parallel to the rolling direction. The metal structure has a boundary number of 160 or more.

When the metal structure of the duplex stainless steel becomes coarse, it adversely affects the hydrogen embrittlement resistance. In order to obtain excellent hydrogen embrittlement resistance, it is necessary to have a fine-grained metal structure. In particular, in the thickness direction parallel to the rolling direction, the ferrite phase and austenite phase present per unit length. It is necessary to increase the number of layers. Therefore, in the present invention, in the cross section in the thickness direction parallel to the rolling direction of the duplex stainless steel, the number of straight lines drawn in the thickness direction from the surface to a depth of 1 mm intersects the boundary between the ferrite phase and the austenite phase is 160. That's it. The number of boundaries between the ferrite phase and the austenite phase intersecting the straight line is preferably 180 or more.

The structure observation method is not particularly limited. For example, the cross section in the thickness direction parallel to the rolling direction is etched with a 10% aqueous solution of oxalic acid, and the depth from the surface to 1 mm depth is 100 times using an optical microscope. The number of straight lines from the surface to the depth of 1 mm intersects with the boundary between the ferrite phase and the austenite phase in the continuous photographs taken in the depth direction is measured. The measurement of the number of ferrite phase / austenite phase boundaries may be performed at one location, but it is desirable to perform measurement at about 5 locations at a pitch of 2 to 3 mm and use the average value.

3. Production method The method for producing the duplex stainless steel according to the present invention is not limited as long as the above-mentioned metal structure is obtained. In particular, cold working and solution heat treatment are performed within the range satisfying the following conditions. Is desirable. Each will be described.

Cold work degree: 75% or more By increasing the cold work degree, a finer grain structure can be obtained than when heat treatment is performed at the same temperature. Moreover, the recrystallization temperature can be lowered as the degree of processing increases. In order to obtain these two merits, it is desirable that the cold work degree is 75% or more. On the other hand, if the degree of work is excessively high, damage to the tool becomes severe, so the degree of cold work is desirably 90% or less.

Solution heat treatment temperature: 1020 to 1100 ° C
Duplex stainless steel is difficult to sufficiently dissolve the precipitate even if it is subjected to a solution heat treatment at a temperature of less than 1020 ° C., and the σ phase does not appear between the completion of soaking in the heat treatment and the start of water cooling. Precipitates easily. On the other hand, when heat treatment exceeds 1100 ° C., the coarsening of the structure becomes significant. Therefore, the solution heat treatment is performed in a temperature range of 1020 to 1100 ° C.

  Since the duplex stainless steel of the present invention is very difficult to precipitate the σ phase due to the component design, a heat treatment temperature lower than that of normal duplex stainless steel can be employed. A uniform and fine two-phase structure can be obtained on the surface layer by synthesizing with the influence of the cold work degree described above. Since hydrogen embrittlement generally occurs in the ferrite phase portion, a structure in which such ferrite is not coarse but finely dispersed is extremely effective in preventing hydrogen embrittlement.

  EXAMPLES Hereinafter, although an Example demonstrates this invention more concretely, this invention is not limited to these Examples.

  10 kg of duplex stainless steel having the chemical composition shown in Table 1 was melted in a VIM melting furnace, this slab was held at 1250 ° C. for 2 hours, and then hot forged to produce a 30 mm thick plate. . Next, the obtained plate material was subjected to a solution heat treatment at 1110 ° C. for 30 minutes, and then subjected to water quenching.

  The σ phase sensitivity was evaluated by an impact value after aging at 900 ° C. for 600 seconds. That is, after aging the V-notch test piece collected from the plate material after solution heat treatment, the impact value was measured according to JIS Z 2242 (2005). For corrosion resistance (seawater corrosion resistance), a pitting corrosion test was performed on the plate material after solution heat treatment, and a critical pitting corrosion temperature CPT was measured. The pitting corrosion test was performed according to the pitting corrosion test method using ferric chloride specified in ASTM G48. For strength, a JIS Z2201 (1998) No. 10 test piece was sampled from the plate material after solution heat treatment, and a tensile test at normal temperature was performed. These results are shown in Table 2.

  FIG. 1 is a graph showing the relationship between the σ phase sensitivity index X expressed by equation (i) and the impact value after aging at 900 ° C. for 600 seconds for the examples shown in Tables 1 and 2. As shown in FIG. 1, the lower the σ phase sensitivity index X, the higher the impact value and the σ phase precipitation is suppressed. In particular, the precipitation of the σ phase is remarkably suppressed by adjusting the components so that the σ phase sensitivity index X is 52.0 or less. As described above, the σ phase sensitivity index X is useful as an evaluation method for the amount of precipitation of the σ phase and, as a result, an evaluation method for crack sensitivity when the billet is allowed to cool.

  FIG. 2 is a diagram showing the relationship between the strength index Y and the 0.2% yield strength YS. As shown in FIG. 2, the higher the strength index, the higher the 0.2% proof stress YS, and in particular, by adjusting the components so as to be 41.5 or more, a further high strength effect can be obtained. Thus, the strength index Y is useful as a material strength evaluation method.

As shown in Table 2, in each of Reference Examples a to i, the impact value after aging at 900 ° C. for 600 seconds was 18 J / cm ² or more, and σ phase precipitation was significantly suppressed. For this reason, the crack at the time of billet cooling can be suppressed, and also the machinability in various processes can be improved. In each of Reference Examples a to i, the strength index Y is 40.5 or more, and the 0.2% proof stress YS is 620 MPa or more, thereby achieving high strength. Furthermore, in all of Reference Examples a to i, the pitting corrosion resistance index PREW was 40 or more, and the critical pitting corrosion temperature CPT was 70 ° C. or more.

  On the other hand, Comparative Examples j to m are examples in which the σ phase sensitivity index X exceeds 52.0 and the strength index Y is less than 40.5. In particular, Comparative Example j has a Ni content outside the range defined by the present invention, and Comparative Example k has a chemical composition within the range defined by the present invention, but the σ phase sensitivity index X and the strength index Y are Out of the range defined in the present invention, Comparative Example 1 is outside the range defined in the present invention, and Comparative Example m is out of the range defined in the present invention in terms of Cu and Ni content. It is an example. In each of these comparative examples, the impact value after aging at 900 ° C. for 600 seconds was low, and the precipitation suppression of the σ phase was insufficient. For this reason, it is expected that cracking occurs when the billet is allowed to cool. In these comparative examples, the 0.2% proof stress YS was less than 620 MPa, and the increase in strength was insufficient. Comparative Example n is an example in which the chemical composition and the σ phase sensitivity index X are within the range defined by the present invention, but the strength index Y is outside the range defined by the present invention. In this comparative example, the 0.2% yield strength YS was less than 620 MPa, and the increase in strength was insufficient.

  10 kg of duplex stainless steel having the chemical composition shown in Table 3 was melted in a VIM melting furnace, this slab was held at 1250 ° C. for 2 hours, and then hot forged to produce a 30 mm thick plate. . Next, the obtained plate material was subjected to cold rolling with the workability shown in Table 4 and subjected to solution heat treatment at the temperature shown in Table 4, and then subjected to water quenching.

  The σ phase sensitivity was evaluated by an impact value after aging at 900 ° C. for 600 seconds. That is, after aging the V-notch test piece collected from the plate material after solution heat treatment, the impact value was measured according to JIS Z 2242 (2005). For corrosion resistance (seawater corrosion resistance), a pitting corrosion test was performed on the plate material after solution heat treatment, and a critical pitting corrosion temperature CPT was measured. The pitting corrosion test was performed according to the pitting corrosion test method using ferric chloride specified in ASTM G48. For strength, a JIS Z2201 (1998) No. 10 test piece was sampled from the plate material after solution heat treatment, and a tensile test at normal temperature was performed. These results are also shown in Table 4.

The structure is determined by applying a structure etch to the cross section in the thickness direction parallel to the rolling direction, and using an optical microscope to determine how many straight lines from the surface to the depth of 1 mm intersect the boundary between the ferrite phase and the austenite phase. It confirmed in the continuous photograph of the depth direction imaged at 100-times magnification. In addition, said ferrite phase / austenite phase boundary number was performed about five places at 2-3 mm pitch, and the average value was calculated | required.

  In the hydrogen embrittlement test, a test piece having a diameter of 2.54 mm and a length of 55 mm cut out from a plate material was used. Charged with 1000 ppm of hydrogen in 5% hydrogen sulfide + 1 g / l thiourea aqueous solution maintained at 35 ° C and immersed for 100 hours, 60%, 70%, 80%, 90%, 100% of 0.2% proof stress % Tensile load was applied. After the test, the presence or absence of cracks on the surface of the test piece was evaluated. In Table 4, the case where there was no crack was indicated as ◯, and the case where there was a crack was indicated as x.

As shown in Table 4, test No. which is an example of the present invention. In all of Nos. 1 to 8, the impact value after aging at 900 ° C. for 600 seconds was 20 J / cm ² or more, and σ phase precipitation was greatly suppressed. For this reason, the crack at the time of billet cooling can be suppressed, and also the machinability in various processes can be improved. In addition, Test No. In each of Nos. 1 to 8, the strength index Y is 40.5 or more, and the 0.2% proof stress YS is 620 MPa or more, so that high strength can be achieved. Furthermore, test no. In all of Nos. 1 to 8, the pitting corrosion resistance index PREW was 40 or more, and the critical pitting corrosion occurrence temperature CPT was 70 ° C or more.

  On the other hand, test No. which is a comparative example. 9 to 12 are examples in which the σ phase sensitivity index X exceeds 52.0 and the strength index Y is less than 40.5. Test No. which is a comparative example. 13 to 16 are examples in which the σ phase sensitivity index X is 52.0 or less, but the strength index Y is less than 40.5. In these comparative examples, the 0.2% proof stress YS was less than 620 MPa, and the increase in strength was insufficient.

  Further, Test No. which is an example of the present invention. Nos. 1 to 8 have excellent hydrogen embrittlement resistance without cracking even at 80% of 0.2% proof stress in the hydrogen embrittlement test.

On the other hand, test No. which is a comparative example. In Nos. 17 to 20, the number of ferrite phase / austenite phase boundaries where straight lines from the surface to a depth of 1 mm intersect is less than 160, and this is not within the scope of the present invention. The results are insufficient in terms of hydrogen embrittlement resistance.

  According to the alloy of the present invention, σ phase precipitation is suppressed by setting the alloy component design so that PREW is increased and the σ phase sensitivity index X and the strength index Y satisfy predetermined conditions. Furthermore, a fine grain structure can be obtained by applying an appropriate cold work degree and heat treatment temperature, and it is possible to provide a duplex stainless steel having high strength, excellent σ phase sensitivity and excellent hydrogen embrittlement resistance. . The alloys of the present invention include, in particular, umbilical tubes, whose strength and hydrogen embrittlement resistance are important due to the deep sea of oil wells, line pipes, heat exchanger parts, process steel pipes and piping for the petroleum and chemical industries, Suitable for oil well pipes and the like.

Claims (4)

In mass%, C: 0.03% or less, Si: 0.3% or less, Mn: 3.0% or less, P: 0.040% or less, S: 0.008% or less, Cu: 0.2 to 2.0%, Ni: 5.0 to 6.5%, Cr: 23.0 to 27.0%, Mo: 2.5 to 3.5%, W: 1.5 to 4.0%, N : 0.24-0.40% and Al: 0.03% or less, the balance consists of Fe and impurities,
The σ phase sensitivity index X represented by the following formula (i) is 52.0 or less,
The strength index Y represented by the following formula (ii) is 40.5 or more, and the pitting corrosion resistance index PREW represented by the following formula (iii) is 40 or more.
In a cross section in the thickness direction parallel to the rolling direction, when a straight line parallel to the thickness direction from the surface to a depth of 1 mm is drawn, the number of boundaries between the ferrite phase and the austenite phase intersecting the straight line is 160 or more. A duplex stainless steel characterized by comprising:
X = 2.2Si + 0.5Cu + 2.0Ni + Cr + 4.2Mo + 0.2W (i)
Y = Cr + 1.5Mo + 10N + 3.5W (ii)
PREW = Cr + 3.3 (Mo + 0.5W) + 16N (iii)
However, each element symbol in the formulas (i) to (iii) means the content (% by mass) of each element. Instead of a part of Fe, by mass percent, further Ca: 0.02% or less, Mg: 0.02% or less and B: in that it contains at least one selected 0.02% hereinafter or al The duplex stainless steel according to claim 1, characterized in that In mass%, C: 0.03% or less, Si: 0.3% or less, Mn: 3.0% or less, P: 0.040% or less, S: 0.008% or less, Cu: 0.2 to 2.0%, Ni: 5.0 to 6.5%, Cr: 23.0 to 27.0%, Mo: 2.5 to 3.5%, W: 1.5 to 4.0%, N : 0.24-0.40% and Al: 0.03% or less, the balance consists of Fe and impurities,
The σ phase sensitivity index X represented by the following formula (i) is 52.0 or less,
For a steel having a chemical composition in which the strength index Y represented by the following formula (ii) is 40.5 or more, and the pitting corrosion resistance PREW represented by the following formula (iii) is 40 or more,
A method for producing a duplex stainless steel, characterized in that a cold working provides a workability of 75% or more, and a solution heat treatment is performed at 1020 to 1100 ° C. It is a manufacturing method of the duplex stainless steel of Claim 3, Comprising: The chemical composition of steel is replaced with a part of Fe, and is mass%, Ca: 0.02% or less, Mg: 0.02% following and B: method for producing duplex stainless steel which is characterized by containing one or more selected 0.02% hereinafter or al.