Austenitic stainless steel welded joint
阅读说明:本技术 奥氏体系不锈钢焊接接头 (Austenitic stainless steel welded joint ) 是由 净德佳奈 山田健太 冈田浩一 小薄孝裕 于 2019-02-28 设计创作,主要内容包括:本申请提供耐连多硫酸SCC性以及耐环烷酸腐蚀性优异、并且蠕变延性也优异的奥氏体系不锈钢焊接接头。奥氏体系不锈钢焊接接头(1)具备母材(10)和焊接金属(20)。在焊接金属(20)的宽度中央位置且是厚度中央位置的化学组成以质量%计为C:0.050%以下、Si:0.01~1.00%、Mn:0.01~3.00%、P:0.030%以下、S:0.015%以下、Cr:15.0~25.0%、Ni:20.0~70.0%、Mo:1.30~10.00%、Nb:0.05~3.00%、N:0.150%以下、B:0.0050%以下、以及余量:Fe以及杂质。(Provided is an austenitic stainless steel welded joint which is excellent in polythionic acid (SCC) resistance, naphthenic acid corrosion resistance, and creep ductility. An austenitic stainless steel welded joint (1) is provided with a base metal (10) and a weld metal (20). The chemical composition in mass% at the widthwise central position and the thickness central position of the weld metal (20) is C: 0.050% or less, Si: 0.01 to 1.00%, Mn: 0.01-3.00%, P: 0.030% or less, S: 0.015% or less, Cr: 15.0 to 25.0%, Ni: 20.0 to 70.0%, Mo: 1.30-10.00%, Nb: 0.05-3.00%, N: 0.150% or less, B: 0.0050% or less, and the balance: fe and impurities.)
1. An austenitic stainless steel welded joint comprising a base metal and a weld metal,
the chemical composition of the base material is calculated by mass percent
C: less than 0.030%,
Si:0.10~1.00%、
Mn:0.20~2.00%、
P: less than 0.040%,
S: less than 0.010%,
Cr:16.0~25.0%、
Ni:10.0~30.0%、
Mo:0.10~5.00%、
Nb:0.20~1.00%、
N:0.050~0.300%、
sol.Al:0.001~0.100%、
B:0.0010~0.0080%、
Cu:0~5.00%、
W:0~5.0%、
Co:0~1.0%、
V:0~1.00%、
Ta:0~0.20%、
Hf:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities, and
satisfies formula (1);
in the case of the weld metal,
the chemical composition in mass% at the widthwise central position and the thickness central position of the weld metal
C: less than 0.050%,
Si:0.01~1.00%、
Mn:0.01~3.00%、
P: less than 0.030%,
S: less than 0.015%,
Cr:15.0~25.0%、
Ni:20.0~70.0%、
Mo:1.30~10.00%、
Nb:0.05~3.00%、
N: less than 0.150 percent,
B: less than 0.0050%,
sol.Al:0~1.000%、
Cu:0~2.50%、
W:0~1.0%、
Co:0~15.0%、
V:0~0.10%、
Ti:0~0.50%,
Ta:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities in the iron-based alloy, and the impurities,
B+0.004-0.9C+0.017Mo2≥0 (1)
wherein the content of the corresponding element in mass% is substituted at the symbol of the element in the formula (1).
2. The austenitic stainless steel weld joint of claim 1,
the chemical composition of the parent material comprises a chemical composition selected from the group consisting of
Cu:0.10~5.00%、
W:0.1~5.0%、
Co:0.1~1.0%、
V:0.10~1.00%、
Ta:0.01~0.20%、
Hf:0.01~0.20%、
Ca:0.001~0.010%、
Mg: 0.001 to 0.010%, and
rare earth elements: 0.001-0.100% of 1 or more elements in the group.
3. The austenitic stainless steel weld joint according to claim 1 or claim 2,
said chemical composition of said weld metal is selected from the group consisting of
sol.Al:0.001~1.000%、
Cu:0.01~2.50%、
W:0.1~1.0%、
Co:0.1~15.0%、
V:0.01~0.10%、
Ti:0.01~0.50%,
Ta:0.01~0.20%、
Ca:0.001~0.010%、
Mg: 0.001 to 0.010%, and
rare earth elements: 0.001-0.100% of 1 or more elements in the group.
4. The austenitic stainless steel weld joint according to any one of claims 1 to 3,
the chemical composition of the weld metal satisfies formula (2),
0.012Cr-0.005Ni+0.013Mo+0.023Nb+0.02Al-0.004Co≤0.176 (2)
wherein the content of the corresponding element in mass% is substituted at the symbol of the element in the formula (2).
Technical Field
The present invention relates to a welded joint, and more particularly, to an austenitic stainless steel welded joint.
Background
An austenitic stainless steel welded joint is produced by welding austenitic stainless steel materials, and includes a base material formed of austenitic stainless steel and a weld metal. The austenitic stainless steel welded joint can be used for welded structures of plant equipment such as thermal boilers, oil refining, petrochemical equipment and the like. Examples of the welded structure of the chemical plant equipment include peripheral equipment of a distillation column, a heating furnace tube, a reaction tube, a heat exchanger, and piping. Among the parts used in the welded structure of these chemical plant facilities, there are parts used in an environment containing corrosive fluids including sulfides and/or chlorides at a high temperature of 600 to 700 ℃. In the present specification, an environment of 600 to 700 ℃ high temperature and containing a corrosive fluid containing sulfide and/or chloride is referred to as a "high temperature corrosive environment".
Welded structures used in high temperature corrosive environments stop working during periodic maintenance of chemical plants. When the work stops, the temperature of the welding structure is reduced to normal temperature. At this time, air, moisture, and sulfide scale react to generate polythionic acid on the surface of the member of the welded structure. This polythionic acid induces stress corrosion cracking at grain boundaries (hereinafter referred to as polythionic acid SCC). Therefore, excellent polythionic acid SCC resistance is required for the member used in the high-temperature corrosive environment.
Steels having improved resistance to polythionic acid SCC have been proposed in Japanese patent application laid-open Nos. 2003-166039 (patent document 1) and 2009/044802 (patent document 2). The reason for the polythionic acid SCC is that Cr is expressed as M23C6The form of the type carbide precipitates at grain boundaries, and forms a Cr-deficient layer in the vicinity of the grain boundaries. Therefore, in
Specifically, the austenitic heat-resistant steel disclosed in
The austenitic stainless steel disclosed in
Disclosure of Invention
Problems to be solved by the invention
As a result, in chemical plant equipment, inferior crude oil may be used; not only the corrosion of polythionic acid SCC but also the corrosion of naphthenic acid. Naphthenic acids are cyclic saturated hydrocarbons having 1 or more carboxyl groups. Naphthenic acids do not cause SCC, as polythionic acid does, but instead cause general corrosion. Therefore, in the welded joint used in the plant equipment, it is preferable that not only the resistance to SCC, polythionic acid, but also the resistance to naphthenic acid corrosion be excellent.
In addition, in recent years, high creep ductility has been required for parts used in a high-temperature corrosive environment of 600 to 700 ℃. In chemical plant facilities, as described above, the facilities may be stopped and regular maintenance may be performed. In the periodic maintenance, parts that must be replaced in a welded structure of chemical plant equipment are investigated. In this case, if the creep ductility is high, the degree of deformation of the component can be checked at the time of regular maintenance, and this can be used as a criterion for determining replacement of the component.
Although patent documents 1 and 2 aim to improve the resistance to SCC of polythionic acid, they have studied naphthenic acid corrosion resistance and have not studied to improve creep ductility. Further, no studies have been made on the polythionic acid SCC resistance and naphthenic acid corrosion resistance of a weld joint including not only a base material but also a weld metal.
The purpose of the present application is to provide an austenitic stainless steel welded joint that is excellent in the resistance to SCC of polythionic acid and naphthenic acid corrosion, and also excellent in the creep ductility of the base metal.
Means for solving the problems
The austenitic stainless steel welded joint according to the present application includes a base metal and a weld metal,
the chemical composition of the base material is calculated by mass percent
C: less than 0.030%,
Si:0.10~1.00%、
Mn:0.20~2.00%、
P: less than 0.040%,
S: less than 0.010%,
Cr:16.0~25.0%、
Ni:10.0~30.0%、
Mo:0.10~5.00%、
Nb:0.20~1.00%、
N:0.050~0.300%、
sol.Al:0.001~0.100%、
B:0.0010~0.0080%、
Cu:0~5.00%、
W:0~5.0%、
Co:0~1.0%、
V:0~1.00%、
Ta:0~0.20%、
Hf:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities, and
satisfies formula (1);
in the case of the weld metal,
the chemical composition in mass% at the widthwise central position and the thickness central position of the weld metal
C: less than 0.050%,
Si:0.01~1.00%、
Mn:0.01~3.00%、
P: less than 0.030%,
S: less than 0.015%,
Cr:15.0~25.0%、
Ni:20.0~70.0%、
Mo:1.30~10.00%、
Nb:0.05~3.00%、
N: less than 0.150 percent,
B: less than 0.0050%,
sol.Al:0~1.000%、
Cu:0~2.50%、
W:0~1.0%、
Co:0~15.0%、
V:0~0.10%、
Ti:0~0.50%,
Ta:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities.
B+0.004-0.9C+0.017Mo2≥0 (1)
Wherein the content (mass%) of the corresponding element is substituted at the symbol of the element in the formula (1).
ADVANTAGEOUS EFFECTS OF INVENTION
The austenitic stainless steel welded joint according to the present application is excellent in polythionic acid SCC resistance and naphthenic acid corrosion resistance, and also excellent in creep ductility of the base metal.
Drawings
Fig. 1 is a plan view showing an example of an austenitic stainless steel welded joint according to the present embodiment.
Fig. 2 is a cross-sectional view of the austenitic stainless steel weld joint of fig. 1, taken in the width direction of the weld metal.
Fig. 3 is a sectional view of the austenitic stainless steel weld joint of fig. 1, taken in the weld metal extending direction L.
Fig. 4 is a cross-sectional view of an austenitic stainless steel weld joint different from that of fig. 3, taken along the weld metal extending direction L.
Fig. 5 is a cross-sectional view perpendicular to the weld metal extending direction L in the austenitic stainless steel welded joint according to the present embodiment.
FIG. 6 is a schematic view for explaining the groove shape of the parent material in the example.
Fig. 7 is a schematic view of a welded joint using the base material of fig. 6.
Fig. 8 is a schematic diagram showing the sampling position of the plate-like test piece used in the examples.
FIG. 9 is a schematic view showing the assumed position of the V-notch test piece used in the examples.
Detailed Description
The present inventors have studied a welded joint having excellent SCC resistance to polythionic acid, excellent naphthenic acid corrosion resistance, and excellent creep ductility of a base material.
When the C content of the base material is reduced to 0.030% or less, M is suppressed in use under a high-temperature corrosive environment23C6The formation of the carbide suppresses the formation of a Cr-deficient layer in the vicinity of the grain boundary. The base material of the austenitic stainless steel welded joint of the present embodiment further contains 0.20 to 1.00% of Nb, so that C is fixed by Nb, and M is further reduced23C6The amount of solid solution C as a formation element of the form carbide. The base material of the austenitic stainless steel welded joint according to the present embodiment further contains 0.10 to 5.00% of Mo. Mo inhibition of M23C6Formation of type carbides. Therefore, the generation of the Cr-deficient layer is reduced. According to the above measures, the resistance to SCC, which is one of stress corrosion cracking, to polythionic acid can be improved.
Further, it is effective to contain the above-mentioned Mo against naphthenic acid corrosion. It is effective to contain Cu in the base material against general corrosion such as sulfuric acid corrosion. However, naphthenic acids, as described above, are cyclic saturated hydrocarbons having a carboxyl group, and even if Cu is contained, naphthenic acid corrosion resistance is not high. On the other hand, Mo is extremely effective for naphthenic acid corrosion. Mo is bonded with S in the high-temperature corrosion environment when used in the high-temperature corrosion environment of the austenitic stainless steel welding joint, and a sulfide coating is formed on the surface of the austenitic stainless steel welding joint. The sulfide film improves naphthenic acid corrosion resistance. Therefore, when the C content is 0.030% or less, the Nb content is 0.20 to 1.00%, and the Mo content is 0.10 to 5.00% in the chemical composition of the base material, the resistance to SCC of polythionic acid is high, and the resistance to naphthenic acid corrosion is also high.
However, the present inventors have investigated and found that when the C content of the base material is reduced to 0.030% or less, the creep ductility of the base material in a high-temperature corrosive environment of 600 to 700 ℃ is reduced. The reason for this is considered as follows. Precipitates formed at grain boundaries improve the grain boundary strength. When the grain boundary strength is increased, the creep ductility of the base material is increased. However, when the C content is reduced to 0.030% or less, precipitates (carbides and the like) formed in grain boundaries are also reduced. As a result, it is considered that it is difficult to obtain grain boundary strength, and creep ductility of the base material is reduced.
Therefore, the present inventors have further studied an austenitic stainless steel welded joint having excellent polythionic acid SCC resistance, excellent naphthenic acid corrosion resistance, and excellent creep ductility of the base material. The present inventors focused on B (boron) as an element contained in the base material. The present inventors have considered that B (boron) segregates in grain boundaries under the high temperature corrosive environment of 600 to 700 ℃ described above, and thus the grain boundary strength can be improved.
As a result of further investigation, the present inventors considered that the chemical composition of the base material of the austenitic stainless steel welded joint is, in mass%, a composition containing C: 0.030% or less, Si: 0.10 to 1.00%, Mn: 0.20-2.00%, P: 0.040% or less, S: 0.010% or less, Cr: 16.0 to 25.0%, Ni: 10.0 to 30.0%, Mo: 0.10 to 5.00%, Nb: 0.20-1.00%, N: 0.050 to 0.300%, sol.Al: 0.001-0.100%, B: 0.0010-0.0080%, Cu: 0-5.00%, W: 0-5.0%, Co: 0-1.0%, V: 0-1.00%, Ta: 0-0.20%, Hf: 0-0.20%, Ca: 0-0.010%, Mg: 0 to 0.010%, and a rare earth element: 0 to 0.100% and the balance of Fe and impurities, not only can excellent polythionic acid SCC resistance and naphthenic acid corrosion resistance be obtained, but also excellent creep ductility can be obtained.
However, it was found that although the resistance to polythionic acid SCC, the resistance to naphthenic acid corrosion, and the creep ductility of the base material of the austenitic stainless steel welded joint having the above chemical composition as the base material were investigated, excellent polythionic acid SCC resistance and excellent naphthenic acid corrosion resistance were obtained, but the excellent creep ductility of the base material was not necessarily obtained in some cases. Therefore, the present inventors have conducted further studies. As a result, the creep ductility of the base material is considered to be the following mechanism.
As described above, in the present embodiment, in order to improve the polythionic acid SCC resistance and the naphthenic acid corrosion resistance, the content of C is not more than 0.030%, and Nb is contained in an amount of 0.20 to 1.00%, and C is fixed to Nb to reduce solid solution C. Specifically, Nb is bonded to C by solution treatment or aging in a short time, and precipitates as MX-type carbonitride. However, the austenitic stainless steel welded joint according to the present embodiment is used for a long time (at least 3000 hours or more) in a high-temperature corrosive environment (a corrosive environment of 600 to 700 ℃). In such an environment, MX type carbonitrides are metastable phases. Therefore, when the base material having the above chemical composition is used for a long time in a high-temperature corrosive environment of 600 to 700 ℃, MX-type carbonitride of Nb changes into Z-phase (CrNbN) and M as steady-state phases23C6A type carbide. At this time, B and M segregated in the grain boundary23C6A part of C in the type carbide is replaced by M23C6And absorbed by the carbide. Therefore, the amount of B segregated in the grain boundaries decreases, and the grain boundary strength decreases. As a result, it is considered that sufficient creep ductility cannot be obtained.
Therefore, a method for suppressing the reduction of the amount of segregated B at the grain boundary in the use of an austenitic stainless steel welded joint under a high-temperature corrosive environment of 600 to 700 ℃ for a long time is further studied. As a result, the following mechanism is considered.
Mo is in the above-mentioned range, and M is suppressed23C6Formation of type carbides. Mo is further present with M23C6A part of M in the type carbide is substituted at M23C6The case of solid solution in the form of carbide. In this specification, M having Mo dissolved therein will be described23C6Type carbide is defined as "Mo solid solution M23C6Type carbide ". Mo solid solution M23C6The type carbide is not easy to dissolve B in solid. Therefore, even if MX-type carbonitride containing Nb is changed to Z phase and M phase in the use of welded austenitic stainless steel joints in high-temperature corrosive environments23C6In the case of type carbide, if M23C6The carbide type is Mo solid solution M23C6Type carbide, B can be inhibited from going to M23C6The solid solution of the form carbide suppresses the reduction of the amount of B segregated at the grain boundary. As a result, it is considered that excellent polythionic acid SCC resistance, excellent naphthenic acid corrosion resistance, and excellent creep ductility can be obtained.
Therefore, in the austenitic stainless steel welded joint having the base material having the above chemical composition, further studies have been made on the transformation of MX type carbonitride containing Nb into Z phase and M phase in the use thereof in a high temperature corrosive environment at 600 to 700 ℃23C6In the case of the type carbide, Mo solid solution M is also formed23C6And a type carbide, whereby the chemical composition of the base material in which the amount of segregated B at the grain boundaries is reduced can be suppressed. As a result, it was found that M is dissolved in Mo as a solid solution23C6The segregation B amount is suppressed by the formation of the type carbide, and B, C and Mo in the chemical composition are closely related to each other. Further, it is known that B, C and Mo in the chemical composition of the base material satisfy formula (1), and thus the base material can have excellent polythionic acid SCC resistance, excellent naphthenic acid corrosion resistance, and excellent creep ductility of the base material even when used in a high-temperature corrosion environment of 600 to 700 ℃.
B+0.004-0.9C+0.017Mo2≥0 (1)
Here, the content (mass%) of the corresponding element is substituted into each element symbol of formula (1).
As a result of further studies, the present inventors have found that when Cu is contained in the base material of the austenitic stainless steel welded joint as an arbitrary element, excellent creep strength is obtained and creep ductility can be maintained even if Cu is contained at 5.00% or less, and that when the upper limit of the Cu content is 1.70% or less, creep strength can be further improved and high creep ductility of the base material can be further maintained. The reason for this is considered as follows. When used in a high-temperature corrosive environment, Cu precipitates in the grains to form a Cu phase. The Cu phase may increase creep strength but decrease creep ductility. Therefore, the Cu content in the base material of the welded joint having the chemical composition and satisfying the formula (1) is more preferably 1.70% or less. When the Cu content is 1.70% or less, excellent creep ductility can be maintained more effectively.
As a result of further studies, the present inventors have found that the creep ductility of the base material is further improved when the Mo content in the chemical composition of the base material of the austenitic stainless steel welded joint is 0.50% or more. The reason is not clear, but the following is considered. When the content of Mo in the base material of the austenitic stainless steel welded joint having the chemical composition satisfying the formula (1) is further 0.50% or more, Mo is further segregated in grain boundaries or generates intermetallic compounds during use in a high-temperature corrosive environment at 600 to 700 ℃. The grain boundary strength is further improved by the segregation and intermetallic compound of the grain boundary. As a result, the creep ductility is further improved. In particular, when the Mo content of the base material is 1.00% or more, the base material can obtain very excellent creep ductility.
The present inventors have also found that, in an austenitic stainless steel welded joint, when the chemical composition at the center of the width and the center of the thickness of the weld metal is set to C: 0.050% or less, Si: 0.01 to 1.00%, Mn: 0.01-3.00%, P: 0.030% or less, S: 0.015% or less, Cr: 15.0 to 25.0%, Ni: 20.0 to 70.0%, Mo: 1.30-10.00%, Nb: 0.05-3.00%, N: 0.150% or less, B: 0.0050% or less, sol. Al: 0-1.000%, Cu: 0-2.50%, W: 0-1.0%, Co: 0-15.0%, V: 0-0.10%, Ti: 0 to 0.50%, Ta: 0-0.20%, Ca: 0-0.010%, Mg: 0-0.010%, rare earth elements: 0 to 0.100%, and the balance of Fe and impurities, the solder joint has excellent resistance to SCC of polythionic acid and naphthenic acid corrosion, and further has excellent weldability.
Further, it has been found that when the above chemical composition of the weld metal satisfies formula (2), the austenitic stainless steel weld joint is excellent in polythionic acid corrosion resistance and naphthenic acid corrosion resistance, and the base metal has excellent creep ductility, and the weld metal has high toughness after high-temperature aging.
0.012Cr-0.005Ni+0.013Mo+0.023Nb+0.02Al-0.004Co≤0.176 (2)
Wherein the content (mass%) of the corresponding element is substituted into the symbol of the element in the formula (2).
The gist of the austenitic stainless steel welded joint according to the present embodiment completed based on the above findings is as follows.
[1] The austenitic stainless steel welded joint of (1) comprises a base metal and a weld metal,
the chemical composition of the base material is calculated by mass%
C: less than 0.030%,
Si:0.10~1.00%、
Mn:0.20~2.00%、
P: less than 0.040%,
S: less than 0.010%,
Cr:16.0~25.0%、
Ni:10.0~30.0%、
Mo:0.10~5.00%、
Nb:0.20~1.00%、
N:0.050~0.300%、
sol.Al:0.001~0.100%、
B:0.0010~0.0080%、
Cu:0~5.00%、
W:0~5.0%、
Co:0~1.0%、
V:0~1.00%、
Ta:0~0.20%、
Hf:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities, and
satisfies formula (1);
in the case of the weld metal,
the chemical composition in mass% at the widthwise central position and the thickness central position of the weld metal
C: less than 0.050%,
Si:0.01~1.00%、
Mn:0.01~3.00%、
P: less than 0.030%,
S: less than 0.015%,
Cr:15.0~25.0%、
Ni:20.0~70.0%、
Mo:1.30~10.00%、
Nb:0.05~3.00%、
N: less than 0.150 percent,
B: less than 0.0050%,
sol.Al:0~1.000%、
Cu:0~2.50%、
W:0~1.0%、
Co:0~15.0%、
V:0~0.10%、
Ti:0~0.50%,
Ta:0~0.20%、
Ca:0~0.010%、
Mg:0~0.010%、
Rare earth elements: 0 to 0.100%, and
and the balance: fe and impurities.
B+0.004-0.9C+0.017Mo2≥0 (1)
Wherein the content (mass%) of the corresponding element is substituted at the symbol of the element in the formula (1).
Here, the width center position of the weld metal means a center position of a length (width) of the weld metal in a width direction perpendicular to an extending direction of the weld metal. The thickness center position of the weld metal means a position at which the weld metal is at a depth of t/2 from the surface at the width center position of the weld metal in a cross section perpendicular to the extending direction of the weld metal when the thickness of the weld metal is defined as tmm in the cross section perpendicular to the extending direction of the weld metal.
In the austenitic stainless steel welded joint according to the present embodiment, the chemical composition of the base material contains the elements in the above-described ranges and satisfies the formula (1), and further, the chemical composition of the welded metal at the center of the width and the center of the thickness contains the elements in the above-described ranges. Therefore, the austenitic stainless steel weld joint of the present embodiment is excellent in polythionic acid SCC resistance and naphthenic acid corrosion resistance. Furthermore, the base material has excellent creep ductility under a high-temperature corrosion environment at 600-700 ℃.
[2] The austenitic stainless steel welded joint of [1], wherein,
the chemical composition of the base material is selected from the group consisting of
Cu:0.10~5.00%、
W:0.1~5.0%、
Co:0.1~1.0%、
V:0.10~1.00%、
Ta:0.01~0.20%、
Hf:0.01~0.20%、
Ca:0.001~0.010%、
Mg: 0.001 to 0.010%, and
rare earth elements: 0.001-0.100% of 1 or more elements in the group.
[3] The austenitic stainless steel welded joint of [1] or [2], wherein,
the aforementioned chemical composition of the aforementioned weld metal comprises a composition selected from the group consisting of
sol.Al:0.001~1.000%、
Cu:0.01~2.50%、
W:0.1~1.0%、
Co:0.1~15.0%、
V:0.01~0.10%、
Ti:0.01~0.50%,
Ta:0.01~0.20%、
Ca:0.001~0.010%、
Mg: 0.001 to 0.010%, and
rare earth elements: 0.001-0.100% of 1 or more elements in the group.
[4] The austenitic stainless steel welded joint of (1) to (3), wherein,
the chemical composition of the weld metal satisfies formula (2).
0.012Cr-0.005Ni+0.013Mo+0.023Nb+0.02Al-0.004Co≤0.176 (2)
Wherein the content (mass%) of the corresponding element is substituted into the symbol of the element in the formula (2).
In this case, the austenitic stainless steel welded joint is excellent in polythionic acid corrosion resistance and naphthenic acid corrosion resistance, and also excellent in creep ductility of the base metal, and further excellent in toughness after high-temperature aging of the weld metal.
The austenitic stainless steel welded joint according to the present embodiment will be described in detail below. In the present specification, "%" of an element means mass% unless otherwise specified.
[ constitution of Austenitic stainless Steel welded Joint ]
Fig. 1 is a plan view showing an example of an austenitic stainless steel welded joint 1 according to the present embodiment. Referring to fig. 1, an austenitic stainless steel welded joint 1 according to the present embodiment includes a
In fig. 1, a direction in which the
Fig. 3 is a sectional view of the austenitic stainless steel welded joint 1 shown in fig. 1 cut in the weld metal extending direction L, and fig. 4 is a sectional view of the austenitic stainless steel welded joint 1 different from fig. 3 cut in the weld metal extending direction L. As shown in fig. 3, the
[ base Material 10]
[ chemical composition ]
The chemical composition of the
C: less than 0.030%
Carbon (C) is inevitably contained. That is, the C content exceeds 0%. C in the use of the austenitic stainless steel welded joint of the present embodiment in a high temperature corrosive environment of 600 to 700 ℃, M is generated at the grain boundary in the base material23C6The carbonitride reduces the polythioacid SCC resistance of the
Si:0.10~1.00%
Silicon (Si) deoxidizes steel. Si further improves the oxidation resistance and steam oxidation resistance of the
Mn:0.20~2.00%
Manganese (Mn) deoxidizes steel. Mn further stabilizes austenite, and improves creep strength of the
P: less than 0.040%
Phosphorus (P) is an impurity inevitably contained. That is, the P content exceeds 0%. P reduces hot workability and toughness of the steel. Therefore, the P content is 0.040% or less. The upper limit of the content of P is preferably 0.035%, more preferably 0.032%, further preferably 0.028%, further preferably 0.026%. The P content is preferably as low as possible. However, an excessive reduction in the P content increases the manufacturing cost. Therefore, the lower limit of the P content is preferably 0.001%, more preferably 0.002% in industrial production.
S: 0.010% or less
Sulfur (S) is an impurity inevitably contained. That is, the S content exceeds 0%. S reduces hot workability and creep ductility of the steel. Therefore, the S content is 0.010% or less. The upper limit of the S content is preferably 0.007%, more preferably 0.006%, and still more preferably 0.005%. The S content is preferably as low as possible. However, an excessive reduction in the S content increases the manufacturing cost. Therefore, the preferable lower limit of the S content is 0.001% in industrial production.
Cr:16.0~25.0%
Chromium (Cr) improves the polythioacid SCC resistance and naphthenic acid corrosion resistance of the
Ni:10.0~30.0%
Nickel (Ni) stabilizes austenite and improves creep strength of the
Mo:0.10~5.00%
When molybdenum (Mo) is used in a high-temperature corrosion environment at 600-700 ℃, M is inhibited from being generated in grain boundaries23C6A type carbide. This improves the resistance of
When the Mo content is 0.50% or more, Mo is further segregated in the grain boundary or an intermetallic compound is generated, and the grain boundary strength is further improved. In this case, even more excellent creep ductility can be obtained in a high-temperature corrosive environment. Therefore, the lower limit of the Mo content is more preferably 0.50%, still more preferably 0.80%, still more preferably 1.00%, and still more preferably 2.00%. When the Mo content is 1.00% or more, the
Nb:0.20~1.00%
When used in a high-temperature corrosive environment of 600-700 ℃, niobium (Nb) bonds with C to form MX-type carbonitride, thereby reducing the amount of solid solution C in the
N:0.050~0.300%
Nitrogen (N) is dissolved in the matrix (parent phase) to stabilize austenite, thereby improving the creep strength of the
sol.Al:0.001~0.100%
Aluminum (Al) deoxidizes steel. If the Al content is too low, the above-mentioned effects cannot be obtained. On the other hand, if the Al content is too high, the cleanliness of the steel decreases, and the workability and ductility of the steel decrease. Therefore, the Al content is 0.001 to 0.100%. The lower limit of the Al content is preferably 0.002%, and more preferably 0.003%. The upper limit of the Al content is preferably 0.050%, more preferably 0.030%, and still more preferably 0.025%. In the present embodiment, the Al content means the content of acid-soluble Al (sol.al).
B:0.0010~0.0080%
Boron (B) is segregated in the grain boundary and improves the grain boundary strength when used in a high-temperature corrosion environment at 600-700 ℃. As a result, the creep ductility of the
The remainder of the chemical composition of the
[ for any element ]
[ any element of group 1]
The chemical composition of the
Cu:0~5.00%
Copper (Cu) is an arbitrary element, and may not be contained. That is, Cu may be 0%. When Cu is contained, Cu precipitates as a Cu phase in grains when used in a high-temperature corrosive environment of 600 to 700 ℃, and the creep strength of the
W:0~5.0%
Tungsten (W) is an arbitrary element, and may not be contained. That is, W may be 0%. If contained, W is dissolved in the matrix (parent phase) to improve the creep strength of the
Co:0~1.0%
Cobalt (Co) is an arbitrary element, and may or may not be contained. That is, the Co content may be 0%. When contained, Co stabilizes austenite and improves creep strength of the
[ any element of group 2]
The chemical composition of the
V:0~1.00%
Vanadium (V) is an arbitrary element, and may or may not be contained. That is, the V content may be 0%. When V is contained, V bonds with C to form carbonitride, reduces solid solution C, and improves the resistance of the
Ta:0~0.20%
Tantalum (Ta) is an arbitrary element, and may not be contained. That is, the Ta content may be 0%. When Ta is contained, Ta bonds with C to form carbonitride when used in a high-temperature corrosive environment of 600 to 700 ℃, reduces solid solution C, and improves the polythionic acid SCC resistance of the
Hf:0~0.20%
Hafnium (Hf) is an arbitrary element, and may not be contained. That is, the Hf content may be 0%. When contained, Hf bonds with C to form carbonitride in use in a high-temperature corrosive environment of 600 to 700 ℃, thereby reducing solid solution C and improving the polythionic acid SCC resistance of the
[ any element of group 3]
The chemical composition of the
Ca:0~0.010%
Calcium (Ca) is an arbitrary element, and may or may not be contained. That is, the Ca content may be 0%. If it is contained, Ca fixes O (oxygen) and S (sulfur) as inclusions, and improves hot workability and creep ductility of the
Mg:0~0.010%
Magnesium (Mg) is an arbitrary element, and may or may not be contained. That is, the Mg content may be 0%. If contained, Mg fixes O (oxygen) and S (sulfur) as inclusions, and improves hot workability and creep ductility of the
Rare earth elements: 0 to 0.100 percent
The rare earth element (REM) is an arbitrary element and may or may not be contained. That is, the REM content may be 0%. When contained, REM fixes O (oxygen) and S (sulfur) as inclusions, and improves hot workability and creep ductility of the base material. However, if the REM content is too high, hot workability and creep ductility of the base material decrease. Therefore, the REM content is 0 to 0.10%. The lower limit of the REM content is preferably more than 0%, more preferably 0.001%, and still more preferably 0.002%. The upper limit of the REM content is preferably 0.080%, and more preferably 0.060%.
REM in the present specification contains at least 1 or more of Sc, Y and lanthanoid (La of atomic number 57-71 Lu), and the REM content means the total content of these elements.
[ for formula (1) ]
The chemical composition of the
B+0.004-0.9C+0.017Mo2≥0 (1)
The content (mass%) of the corresponding element is substituted into each element symbol in the formula (1).
As described above, in the present embodiment, in order to improve the polythionic acid SCC resistance and the naphthenic acid corrosion resistance, the C content is 0.030% or less and Nb is contained in an amount of 0.20 to 1.00%. Therefore, the high-temperature corrosion environment at 600-700 ℃ is realizedIn the following use, MX-type carbonitride of Nb is formed, and the amount of solid-solution C is reduced. However, MX-type carbonitride of Nb is a metastable phase, and therefore, during long-term use under the above-described high-temperature corrosive environment, MX-type carbonitride of Nb changes into a Z-phase and M-phase23C6A type carbide. In this case, B segregated in the grain boundary is in M23C6The form carbide is dissolved in the matrix carbide, and the amount of B segregation in the grain boundary is reduced. As a result, the creep ductility of the
However, if Mo is in M23C6Form carbide is dissolved in solid solution to form' Mo solid solution M23C6Type carbide ", M is dissolved in Mo as a solid23C6B in the carbide is not easily dissolved in a solid. Therefore, the B segregation amount at the grain boundary is maintained, and not only excellent polythionic acid SCC resistance and naphthenic acid corrosion resistance are obtained, but also excellent creep ductility is obtained in the
Definition of F1 ═ B +0.004-0.9C +0.017Mo2. F1 represents a plurality of M species generated in the
When the chemical composition of the base material contains Cu, the upper limit of the Cu content is preferably 1.70% or less, as described above. That is, in view of improving creep strength and further obtaining excellent creep ductility, the Cu content is preferably more than 0% and 1.70% or less. When the Cu content is 1.70% or less, excellent creep strength can be obtained due to precipitation strengthening of the Cu phase, and excellent creep ductility of the base material can be maintained.
In the chemical composition of the base material, the lower limit of the Mo content is preferably 0.50%. In this case, Mo is segregated in grain boundaries or forms intermetallic compounds in the use under a high-temperature corrosive environment of 600 to 700 ℃. The grain boundary strength is further improved by the segregation and intermetallic compound of the grain boundary. As a result, the creep ductility of the base material is further improved. Therefore, the lower limit of the Mo content is preferably 0.50%. When the lower limit of the Mo content is 1.00% or more, the creep ductility of the base material is significantly improved. When the Mo content is 0.50% or more, the F1 value is preferably 0.00500 or more, more preferably 0.00800 or more, more preferably 0.01000 or more, and more preferably 0.02000 or more.
[ for weld metal 20]
[ chemical composition ]
Fig. 5 is a cross-sectional view perpendicular to the weld metal extending direction L in the austenitic stainless steel welded joint 1 according to the present embodiment. Referring to fig. 5, in a cross section of the
C: 0.050% or less
Carbon (C) is inevitably contained. Namely, the C content exceeds 0%. C in the use of the austenitic stainless steel welded
Si:0.01~1.00%
Silicon (Si) deoxidizes the
Mn:0.01~3.00%
Manganese (Mn) deoxidizes the
P: less than 0.030%
Phosphorus (P) is an impurity inevitably contained. That is, the P content exceeds 0%. P decreases the toughness of the weld metal. P further increases the hot crack sensitivity of the
S: less than 0.015%
Sulfur (S) is an impurity inevitably contained. That is, the S content exceeds 0%. S reduces the ductility of the weld metal and increases the high temperature crack sensitivity of the
Cr:15.0~25.0%
Chromium (Cr) improves the polythionic acid SCC resistance and naphthenic acid corrosion resistance of the
Ni:20.0~70.0%
Nickel (Ni) stabilizes austenite and improves creep strength of the
Mo:1.30~10.00%
Molybdenum (Mo) inhibits the grain boundary formation M in the
Nb:0.05~3.00%
When the niobium (Nb) is used in a high-temperature corrosion environment at 600-700 ℃, the Nb and C are bonded to generate MX-type carbonitride, and the amount of solid solution C in the
N: less than 0.150%
Nitrogen (N) is inevitably contained. That is, the N content exceeds 0%. N is dissolved in the matrix (parent phase) to stabilize austenite, thereby improving the creep strength of the
B: 0.0050% or less
Boron (B) is inevitably contained. Namely, the B content exceeds 0%. And B is segregated in the grain boundary when used in a high-temperature corrosion environment at 600-700 ℃, so that the grain boundary strength is improved. As a result, the creep ductility of the
The balance of the chemical composition of the
[ for any element ]
[ any element of group 1]
The chemical composition of the
sol.Al:0~1.000%
Aluminum (Al) is an arbitrary element, and may not be contained. That is, the Al content may be 0%. When contained, Al deoxidizes the
[ any element of group 2]
The chemical composition of the
Cu:0~2.50%
Copper (Cu) is an arbitrary element, and may not be contained. That is, the Cu content may be 0%. When Cu is contained, Cu precipitates as a Cu phase in grains when used in a high-temperature corrosive environment of 600 to 700 ℃, and the creep strength of the
W:0~1.0%
Tungsten (W) is an arbitrary element, and may not be contained. That is, the W content may be 0%. When W is contained, W is dissolved in the
Co:0~15.0%
Cobalt (Co) is an arbitrary element, and may or may not be contained. That is, the Co content may be 0%. When contained, Co stabilizes austenite and improves creep strength of the
[ any element of group 3]
The chemical composition of the
V:0~0.10%
Vanadium (V) is an arbitrary element, and may or may not be contained. That is, the V content may be 0%. When V is used in a high-temperature corrosion environment at 600-700 ℃, V bonds with C to generate carbonitride, reduces solid solution C, and improves the polythionic acid (SCC) resistance of the
Ti:0~0.50%
Titanium (Ti) is an arbitrary element, and may not be contained. That is, the Ti content may be 0%. When Ti is contained, Ti is bonded with C to generate carbide in the use under the high-temperature corrosion environment of 600-700 ℃, solid solution C is reduced, and the resistance of the
Ta:0~0.20%
Tantalum (Ta) is an arbitrary element, and may not be contained. That is, the Ta content may be 0%. When the Ta is contained, in the use of the high-temperature corrosion environment at 600-700 ℃, the Ta is bonded with C to generate carbonitride, solid solution C is reduced, and the polythionic acid SCC resistance of the
[ any element of group 4]
The chemical composition of the
Ca:0~0.010%
Calcium (Ca) is an arbitrary element, and may or may not be contained. That is, the Ca content may be 0%. If it is contained, Ca fixes O (oxygen) and S (sulfur) as inclusions, thereby improving the resistance to the reheat cracking of the
Mg:0~0.010%
Magnesium (Mg) is an arbitrary element, and may or may not be contained. That is, the Mg content may be 0%. If contained, Mg fixes O (oxygen) and S (sulfur) as inclusions, and improves the resistance to reheat cracking of the
Rare earth elements: 0 to 0.100 percent
The rare earth element (REM) is an arbitrary element and may or may not be contained. That is, the REM content may be 0%. When contained, REM fixes O (oxygen) and S (sulfur) as inclusions to improve the resistance of the
The austenitic stainless steel welded joint 1 according to the present embodiment includes a
[ for formula (2) ]
The chemical composition of the region P at the center of the width and the center of the thickness of the
0.012Cr-0.005Ni+0.013Mo+0.023Nb+0.02Al-0.004Co≤0.176 (2)
Wherein the content (mass%) of the corresponding element is substituted into the symbol of the element in the formula (2).
Definition of F2 ═ 0.012Cr-0.005Ni +0.013Mo +0.023Nb +0.02Al-0.004 Co. As described above, when the austenitic stainless steel welded joint 1 according to the present embodiment is used as a member of a welded structure of chemical plant equipment, it is used in a high-temperature corrosive environment of 600 to 700 ℃ during operation, as described above. Therefore, the
F2 is an index of toughness of the
In F2, Ni and Co, which are elements that improve the toughness of the weld metal, are negative values, and Cr, Mo, Nb, and Al, which are elements that reduce the toughness of the weld metal, are positive values. If F2 is greater than 0.176, the ratio of the element that decreases the toughness of the weld metal to the element that increases the toughness of the weld metal increases. In this case, the austenitic stainless steel welded joint 1 is excellent in polythionic acid corrosion resistance and naphthenic acid corrosion resistance, and also excellent in creep ductility of the
If F2 is 0.176 or less, it is assumed that the chemical composition of the
The upper limit of the F2 value is preferably 0.174, more preferably 0.172, still more preferably 0.170, and yet more preferably 0.165.
As described above, in the austenitic stainless steel welded joint 1 according to the present embodiment, the contents of the respective elements of the chemical composition of the
[ production method ]
An example of the method for producing the austenitic stainless steel welded joint 1 according to the present embodiment will be described. One example of the manufacturing method includes a step of preparing a base material 10 (base material preparation step) and a step of welding the
[ base material preparation Process ]
In the base material preparation step, a
When manufacturing the
[ preparation Process ]
Molten steel having the chemical composition described above and satisfying the formula (1) is produced. The molten steel is produced, for example, by using an electric furnace, an AOD (argon Oxygen Decarburization) furnace, and a VOD (Vacuum Oxygen Decarburization) furnace. The molten steel produced is subjected to a known degassing treatment as necessary. A billet is produced from the molten steel subjected to the degassing treatment. The method of manufacturing the billet is, for example, a continuous casting method. A continuous casting material (billet) was produced by a continuous casting method. Examples of the continuous casting material include a slab, a billet, and a bar. The molten steel may be cast into an ingot by an ingot casting method.
[ Hot working Process ]
The prepared billet (continuous casting material or ingot) is hot worked to produce a base material. For example, the billet is hot-rolled to produce a steel sheet as the
[ Cold working Process ]
The base material after the hot working step may be cold worked as necessary. When the
[ solution treatment Process ]
After the hot working step or after the cold working step, the
Preferable solution treatment temperature: 1000-1250 deg.C
When the solution treatment temperature is 1000 ℃ or higher, the carbonitride of Nb is sufficiently dissolved in a solid state, and the creep strength is further improved when used in a high-temperature corrosive environment. When the heat treatment temperature is 1250 ℃ or lower, excessive solid solution of C is suppressed, and the resistance to polythionic acid SCC is further improved.
The holding time at the solution treatment temperature in the solution treatment is not particularly limited, and is, for example, 2 to 60 minutes.
In place of the solution treatment, the
[ welding Process ]
The
The welding material can be melted, for example, in the same manner as the
In the welding step, when the
Through the above-described manufacturing steps, the austenitic stainless steel welded joint 1 according to the present embodiment can be manufactured. The method for manufacturing the austenitic stainless steel welded joint 1 according to the present embodiment is not limited to the above-described manufacturing method. The austenitic stainless steel welded joint 1 having the
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