JP5387057B2 - Ferritic stainless steel with excellent heat resistance and toughness - Google Patents

Description

  TECHNICAL FIELD The present invention relates to Cr-containing steel, and particularly has high heat resistance (heat resistant) suitable for use in exhaust system members used in high-temperature environments such as exhaust pipes of automobiles and motorcycles, converter cases and exhaust ducts of thermal power plants. It relates to a ferritic stainless steel having excellent fatigue properties and oxidation resistance and toughness of the base material.

  Exhaust manifolds, exhaust pipes, converter cases, mufflers and other exhaust system members used in the exhaust system environment of automobiles are called thermal fatigue characteristics and oxidation resistance (hereinafter, both characteristics are collectively referred to as “heat resistance”). ). In applications where such heat resistance is required, Cr-containing steels such as Type 429 (14Cr-0.9Si-0.4Nb system) to which Nb and Si are added are currently widely used. However, when the exhaust gas temperature rises to a temperature exceeding 900 ° C. as the engine performance is improved, Type 429 has insufficient thermal fatigue characteristics.

  For this problem, Cr-containing steel with improved high-temperature proof stress by adding Nb and Mo, SUS444 (19Cr-0.5Nb-2Mo steel), Nb, Mo, and W specified in JIS G4305 are added. Ferritic stainless steel and the like have been developed (see, for example, Patent Document 1). However, due to the recent abnormal rise of rare metal raw materials such as Mo and W, development of materials having equivalent heat resistance using inexpensive raw materials has been required.

  As a material excellent in heat resistance that does not use expensive elements such as Mo and W, for example, in Patent Document 2, 10 to 20 mass% Cr steel, Nb: 0.50 mass% or less, Cu: 0.8 to Ferritic stainless steel for automobile exhaust gas flow channel member to which 2.0 mass%, V: 0.03 to 0.20 mass% is added, and Patent Document 3 discloses that 10-20 mass% Cr steel, Ti: 0.05 -0.30 mass%, Nb: 0.10-0.60 mass%, Cu: 0.8-2.0 mass%, B: ferritic stainless steel with excellent thermal fatigue properties with addition of 0.0005-0.02 mass% Steel and Patent Document 4 disclose ferritic stainless steel for automotive exhaust system parts in which Cu: 1 to 3 mass% is added to 15 to 25 mass% Cr steel. All of these steels are characterized by improving thermal fatigue properties by adding Cu.

JP 2004-018921 A WO2003 / 004714 pamphlet JP 2006-117985 A JP 2000-297355 A

  However, according to the researches of the inventors, when Cu is added as in the techniques of Patent Documents 2 to 4, although the thermal fatigue resistance is improved, the oxidation resistance of the steel itself is decreased, and the whole From a standpoint, it has become clear that heat resistance deteriorates. Further, SUS444 has a higher Cr content than Type 429, and a large amount of Mo is added, so that the toughness of the base material is inferior.

  Therefore, the object of the present invention is to develop a technique for preventing a decrease in oxidation resistance due to the addition of Cu, and is excellent in thermal fatigue characteristics and oxidation resistance without adding expensive elements such as Mo and W. An object of the present invention is to provide a ferritic stainless steel having toughness equivalent to or better than Type 429. Here, the “excellent oxidation resistance and thermal fatigue characteristics” as used in the present invention has characteristics equal to or higher than those of SUS444. Specifically, the oxidation resistance is oxidation resistance at 950 ° C. The thermal fatigue property means that the repeated thermal fatigue property between 100 ° C. and 850 ° C. is equal to or higher than that of SUS444. Further, toughness equivalent to Type 429 means that the brittle fracture surface ratio when a cold-rolled sheet having a thickness of 2 mm is subjected to a Charpy impact test at −40 ° C. is equivalent to Type 429.

  The inventors have prevented the deterioration of oxidation resistance due to the addition of Cu, which the prior art has, and are excellent in thermal fatigue characteristics and oxidation resistance without adding expensive elements such as Mo and W, and also in toughness. We intensively studied to develop an excellent ferritic stainless steel. As a result, by adding Nb in a range of 0.3 to 0.55 mass% and Cu in a range of 1.0 to 2.5 mass%, high high-temperature strength is obtained in a wide temperature range, and thermal fatigue characteristics are improved. In addition, a decrease in oxidation resistance due to the addition of Cu can be prevented by adding Al in an amount of 0.2 mass% or more. Therefore, by controlling Nb, Cu and Al to the above appropriate ranges, Mo and W It has been found that heat resistance (thermal fatigue characteristics, oxidation resistance) equal to or higher than that of SUS444 can be obtained without addition of. Furthermore, the peel resistance of the Cu and Al-added steel by the repeated oxidation test is improved by optimizing the addition amount of Si (0.5 mass% or less), and the toughness is Mn, Al and Ti. The present invention has been found by optimizing the amount added (Mn: 0.5 mass% or less, Al: 1.2 mass% or less, Ti: 0.01 mass% or less), which can be equal to or higher than Type 429. I let you.

  That is, the present invention is C: 0.015 mass% or less, Si: 0.5 mass% or less, Mn: 0.5 mass% or less, P: 0.04 mass% or less, S: 0.006 mass% or less, Cr: 16 to 20 mass% or less, N: 0.015 mass% or less, Nb: 0.3 to 0.55 mass%, Ti: 0.01 mass% or less, Mo: 0.1 mass% or less, W: 0.1 mass% or less, Cu: 1 Ferritic stainless steel containing 0.0 to 2.5 mass%, Al: 0.2 to 1.2 mass%, the balance being Fe and inevitable impurities.

  In addition to the above component composition, the ferritic stainless steel of the present invention further includes B: 0.003 mass% or less, REM: 0.08 mass% or less, Zr: 0.5 mass% or less, V: 0.5 mass%. Hereinafter, it is characterized by containing one or more selected from Co: 0.5 mass% or less and Ni: 0.5 mass% or less.

  According to the present invention, a ferritic stainless steel having heat resistance (thermal fatigue characteristics, oxidation resistance) equivalent to or better than SUS444 and toughness equivalent to or better than Type 429, without adding expensive Mo or W. It can be obtained inexpensively. Therefore, the steel of the present invention is suitable for use in automobile exhaust system members.

It is a figure explaining a thermal fatigue test piece. It is a figure explaining the temperature in a thermal fatigue test, and constraint conditions. It is a graph which shows the influence of Cu content which acts on a thermal fatigue characteristic. It is a graph which shows the influence of Al content which affects oxidation resistance (oxidation increase). It is a graph which shows the influence of Al content which affects oxidation resistance (scale peeling amount). It is a graph which shows the influence of Si content which acts on oxidation resistance (scale peeling amount). It is a graph which shows the influence of Mn content which affects toughness (brittle fracture surface ratio). It is a graph which shows the influence of Al content which affects toughness (brittle fracture surface ratio). It is a graph which shows the influence of Ti content which affects toughness (brittle fracture surface ratio).

First, the basic experiment that led to the development of the present invention will be described.
C: 0.005-0.007 mass%, N: 0.004-0.006 mass%, Si: 0.3 mass%, Mn: 0.2 mass%, Cr: 17 mass%, Nb: 0.45 mass% and Al: A steel with a component composition of 0.35 mass% as a base and various amounts of Cu added thereto was melted in the laboratory to form a 50 kg steel ingot. After heating this steel ingot to 1170 ° C, A sheet bar having a thickness of 30 mm and a width of 150 mm was obtained by hot rolling. Thereafter, the sheet bar was forged into a bar of 35 mm × 35 mm, annealed at a temperature of 1030 ° C., machined, and processed into a thermal fatigue test piece having the dimensions shown in FIG. Then, as shown in FIG. 2, heat treatment for heating / cooling between 100 ° C. and 850 ° C. was performed at a constraint ratio of 0.35, and the thermal fatigue life was measured. The thermal fatigue life is calculated by dividing the load detected at 100 ° C. by the cross-sectional area of the test piece soaking parallel section shown in FIG. The minimum number of cycles when the stress began to decrease was taken. This corresponds to the number of cycles in which a crack occurred in the test piece. For comparison, the same test was performed on SUS444 (Cr: 19 mass% -Nb: 0.5 mass% -Mo: 2 mass% steel).

  FIG. 3 shows the results of the thermal fatigue test. From this figure, it is possible to obtain a thermal fatigue life equal to or greater than that of SUS444 (about 1100 cycles) by adding Cu by 1.0 mass% or more. It can be seen that it is effective to add 1 mass% or more.

Next, from C: 0.006 mass%, N: 0.007 mass%, Mn: 0.2 mass%, Si: 0.3 mass%, Cr: 17 mass%, Nb: 0.49 mass% and Cu: 1.5 mass% Based on this component composition, steel with various addition amounts of Al was varied in the laboratory and made into a 50 kg steel ingot. This steel ingot was hot-rolled and hot-rolled sheet annealed, Cold-rolled and finish-annealed to obtain a cold-rolled annealed plate having a thickness of 2 mm. A test piece of 30 mm × 20 mm was cut out from the cold-rolled steel sheet obtained as described above, a hole of 4 mmφ was made in the upper part of the test piece, the surface and the end surface were polished with # 320 emery paper, degreased, and then subjected to the following test. It was used for.
<Continuous oxidation test>
The test piece is held in a furnace in an air atmosphere heated to 950 ° C. for 300 hours, the difference in the mass of the test piece before and after the heating test is measured, and the increase in oxidation per unit area (g / m ² ) is obtained. It was.
<Repetitive oxidation test>
Using the above test piece, 600 cycles of heat treatment that repeats heating and cooling to temperatures of 100 ° C. × 1 min and 950 ° C. × 25 min in the atmosphere were performed, and the amount of scale peeled from the test piece surface from the mass difference before and after the test ( g / m ² ) was measured. The heating and cooling rates in the above test were performed at 5 ° C./sec and 1.5 ° C./sec, respectively.

FIG. 4 shows the measurement result of the oxidation increase amount, and FIG. 5 shows the measurement result of the scale peeling amount. From these figures, it can be seen that by adding 0.2 mass% or more of Al, oxidation resistance equal to or higher than that of SUS444 (oxidation increase amount: 27 g / m ² or less, scale peeling amount: less than 4 g / m ² ) can be obtained. Recognize.

  Next, from C: 0.006 mass%, N: 0.007 mass%, Mn: 0.2 mass%, Al: 0.45 mass%, Cr: 17 mass%, Nb: 0.49 mass%, Cu: 1.5 mass% Based on this component composition, steel with various amounts of Si added to this was melted in the laboratory to form a 50 kg steel ingot, a cold-rolled annealed plate with a thickness of 2 mm in the same manner as above, In the same manner as described above, the oxidation test was repeatedly performed, the amount of scale peeling was measured, and the result is shown in FIG. From this, it has been found that even when an appropriate amount of Al is added, when Si exceeds 0.5%, the adhesion to the scale is lowered and the amount of peeling is increased, so that heat resistance equivalent to SUS444 cannot be obtained.

  Finally, C: 0.006 to 0.007 mass%, N: 0.006 to 0.007 mass%, Si: 0.3 mass%, Cr: 17 mass%, Nb: 0.45 mass%, and Cu: 1.5 mass% Based on the component composition consisting of the above, steel with various contents of Mn, Al and Ti being melted in the laboratory was made into a 50 kg steel ingot, which was hot-rolled and hot rolled. Sheet annealing, cold rolling, and finish annealing were performed to obtain a cold-rolled annealing sheet having a thickness of 2 mm. From this cold-rolled annealed plate, a sub-size Charpy impact test piece was collected, subjected to a Charpy impact test at a temperature of −40 ° C., the brittle fracture surface ratio was measured, and the toughness was evaluated.

FIG. 7 shows the effect of Mn content on toughness when Al: 0.25 mass% and Ti: 0.006 mass%. FIG. 8 shows the effect when Mn: 0.1 mass% and Ti: 0.005 mass%. FIG. 9 shows the influence of the Ti content on toughness when Al content is 0.25 mass% and Mn: 0.1 mass%. From these figures, it was found that Mn: 0.3 mass% or less, Al: 1.2 mass% or less, and Ti: 0.01 mass% or less were required to obtain toughness equivalent to or better than Type 429.
The present invention has been completed by further studying the above findings.

Next, the component composition of the ferritic stainless steel of the present invention will be described.
C: 0.015 mass% or less C is an element effective for increasing the strength of steel, but if it exceeds 0.015 mass%, the toughness and formability are significantly reduced. Therefore, in this invention, C shall be 0.015 mass% or less. From the viewpoint of securing moldability, C is preferably as low as possible, and is preferably 0.008 mass% or less. On the other hand, in order to ensure the strength as an exhaust system member, C is preferably 0.001 mass% or more. More preferably, it is the range of 0.002-0.008 mass%.

Si: 0.5 mass% or less Si is an element added as a deoxidizing material, and it is preferable to add 0.05 mass% or more. In addition, Si has an effect of improving the oxidation resistance which is the main subject of the present invention, but cannot be as effective as Al. On the other hand, as can be seen from FIG. 6, excessive addition of Si exceeding 0.5 mass% decreases the scale peel resistance, and the oxidation resistance equal to or higher than that of SUS444 cannot be obtained. Therefore, the upper limit of Si is 0.5 mass%.

Mn: 0.5 mass% or less Mn is an element that increases the strength of steel, and also has an action as a deoxidizer, so it is preferable to add 0.05 mass% or more. However, excessive addition tends to generate a γ phase at a high temperature and reduces heat resistance. Further, as can be seen from FIG. 7, when the addition exceeds 0.5 mass%, the toughness equal to or higher than Type 429 cannot be obtained, and the object of the present invention cannot be achieved. Therefore, in the present invention, Mn is 0.5 mass% or less.

P: 0.04 mass% or less P is a harmful element that lowers toughness, and is desirably reduced as much as possible. Therefore, in the present invention, P is set to 0.04 mass% or less. Preferably, it is 0.03 mass% or less.

S: 0.006 mass% or less S is a harmful element that lowers the elongation and r value, adversely affects the formability, and lowers the corrosion resistance, which is a basic characteristic of stainless steel, so it is desirable to reduce it as much as possible. Therefore, in the present invention, S is set to 0.006 mass% or less. Preferably, it is 0.003 mass% or less.

Cr: 16-20 mass%
Cr is an important element effective for improving the corrosion resistance and oxidation resistance, which are the characteristics of stainless steel, but if it is less than 16 mass%, sufficient oxidation resistance cannot be obtained. On the other hand, Cr is an element that solidifies and strengthens steel at room temperature, and makes it harder and lower ductile. Especially when it exceeds 20 mass%, the above-described adverse effects become remarkable, and workability and toughness equivalent to or better than Type 429 are obtained. It can no longer be obtained. Therefore, in this invention, Cr is taken as the range of 16-20 mass%. Preferably, it is the range of 16-19 mass%.

N: 0.015 mass% or less N is an element that decreases the toughness and formability of steel. When the content exceeds 0.015 mass%, the above-described decrease becomes significant. Therefore, N is set to 0.015 mass% or less. In addition, when higher toughness is calculated | required, N reduces further, and it is preferable to set it as less than 0.010 mass%.

Nb: 0.3-0.55 mass%
Nb forms and fixes C, N and carbonitrides, and has the effect of improving corrosion resistance and formability, intergranular corrosion resistance of welded parts, and increasing the high temperature strength and improving the thermal fatigue characteristics. It is an element having Such an effect is recognized by addition of 0.3 mass% or more. On the other hand, when it exceeds 0.55 mass%, the Laves phase is likely to precipitate, and the brittleness decreases. Therefore, Nb is set to a range of 0.3 to 0.55 mass%. Preferably, it is in the range of 0.4 to 0.5 mass%.

Ti: 0.01 mass% or less Ti is an element that is easier to bond with N than Nb and easily forms coarse TiN, and this coarse TiN acts as a notch and significantly reduces toughness. In particular, as shown in FIG. 9, when the Ti content exceeds 0.01 mass%, this adverse effect becomes significant. Therefore, in the present invention, Ti is limited to 0.01% or less.

Mo: 0.1 mass% or less Mo is an expensive element, and is not actively added for the purpose of the present invention. However, it may be mixed in by 0.1 mass% or less from raw materials such as scrap. Therefore, Mo is set to 0.1 mass% or less.

W: 0.1 mass% or less W is an expensive element like Mo and is not actively added from the gist of the present invention. However, it may be mixed in by 0.1 mass% or less from raw materials such as scrap. Therefore, W is set to 0.1 mass% or less.

Cu: 1.0-2.5 mass%
Cu is an extremely effective element for improving thermal fatigue characteristics. As shown in FIG. 3, it is necessary to add 1.0 mass% or more of Cu in order to obtain the heat fatigue characteristics equivalent to or higher than that of SUS444. However, addition exceeding 2.5 mass% causes ε-Cu to precipitate during cooling after heat treatment, hardens the steel, and easily causes embrittlement during hot working. More importantly, the addition of Cu improves the thermal fatigue resistance, but decreases the oxidation resistance of the steel itself, and the overall heat resistance decreases. The cause of this is not sufficiently clear, but it is because Cu concentrates in the deCr layer formed directly under the scale, and suppresses the re-diffusion of Cr, which is an element that improves the original oxidation resistance of stainless steel. Conceivable. Therefore, Cu is set to a range of 1.0 to 2.5 mass%. Preferably, it is the range of 1.1-1.8 mass%.

Al: 0.2-1.2 mass%
As shown in FIGS. 4 and 5, Al is an indispensable element for improving the oxidation resistance of the Cu-added steel. In particular, in order to obtain oxidation resistance equal to or higher than that of SUS444 which is the object of the present invention, addition of 0.2 mass% or more is necessary. On the other hand, as shown in FIG. 8, if added exceeding 1.2 mass%, the steel becomes hard and toughness equal to or higher than Type 429 cannot be obtained, so the upper limit is set to 1.2 mass%. Preferably, it is in the range of 0.3 to 1.0 mass%.

In the ferritic stainless steel of the present invention, in addition to the essential components, one or more selected from B, REM, Zr, V, Co and Ni should be added within the following range. Can do.
B: 0.003 mass% or less B is an element effective for improving workability, particularly secondary workability. This remarkable effect can be obtained by addition of 0.0005 mass% or more. However, addition of a large amount exceeding 0.003 mass% generates BN and deteriorates workability. Therefore, when adding B, it is made into 0.003 mass% or less. More preferably, it is the range of 0.0005-0.002 mass%.

REM: 0.08 mass% or less, Zr: 0.5 mass% or less REM (rare earth element) and Zr are both elements that improve oxidation resistance. , 0.05 mass% or more is preferably added. However, the addition exceeding 0.08 mass% of REM causes the steel to become brittle, and the addition exceeding 0.5 mass% of Zr causes the Zr intermetallic compound to precipitate and embrittles the steel. When adding REM, 0.08 mass% or less, and when adding Zr, 0.5 mass% or less.

V: 0.5 mass% or less V is an element effective for improving workability and oxidation resistance. In particular, in order to obtain an effect of improving oxidation resistance, addition of 0.15 mass% or more is preferable. However, excessive addition exceeding 0.5 mass% precipitates coarse V (C, N) and degrades the surface properties. Therefore, when adding V, it is preferable to add 0.5 mass% or less, and it is more preferable to add in the range of 0.15-0.4 mass%.

Co: 0.5 mass% or less Co is an element effective for improving toughness, and is preferably added in an amount of 0.02 mass% or more. However, Co is an expensive element, and the above effect is saturated even if it is added in an amount exceeding 0.5 mass%. Therefore, when adding Co, it is preferable to set it as 0.5 mass% or less. More preferably, it is the range of 0.02-0.2 mass%.

Ni: 0.5 mass% or less Ni is an element that improves toughness. However, since Ni is expensive and is a strong γ-phase forming element, it generates a γ-phase at a high temperature and reduces oxidation resistance. Therefore, when adding Ni, it is preferable to set it as 0.5 mass% or less. More preferably, it is the range of 0.05-0.4 mass%.

Next, the manufacturing method of the ferritic stainless steel of this invention is demonstrated.
The method for producing stainless steel of the present invention can be suitably used as long as it is a normal method for producing ferritic stainless steel, and is not particularly limited. For example, steel is melted in a melting furnace such as a converter or an electric furnace, or is further subjected to secondary refining such as ladle refining or vacuum refining to obtain a molten steel having the above-described component composition of the present invention. Is formed into a steel slab by continuous casting or ingot-bundling, and hot-rolled into a hot-rolled sheet, subjected to hot-rolled sheet annealing as necessary, and the hot-rolled sheet is pickled. Then, it is preferable to form a cold-rolled annealed plate through processes such as cold rolling, finish annealing, and pickling. The cold rolling may be performed once or twice or more with intermediate annealing, and the steps of cold rolling, finish annealing, and pickling may be performed repeatedly. Further, depending on the case, the hot-rolled sheet annealing may be omitted, and when the gloss of the steel sheet surface is required, a skin pass may be applied after cold rolling or after finish annealing. In addition, it is preferable that the slab heating temperature before the said hot rolling is 1000-1250 degreeC, the hot-rolled sheet annealing temperature is 900-1100 degreeC, and a finish annealing temperature is the range of 900-1120 degreeC.

  The ferritic stainless steel of the present invention obtained as described above is then subjected to processing such as cutting, bending, pressing, etc. according to each application, and the exhaust pipe, converter case, etc. of automobiles and motorcycles. Various exhaust system members used in a high temperature environment such as an exhaust duct of a thermal power plant. The stainless steel of the present invention used for the above-mentioned member is not limited to the cold-rolled annealed plate, and may be used as a hot-rolled plate or a hot-rolled plate annealed, and further, descaled as necessary. May be. Moreover, the welding method at the time of assembling to the said member is not specifically limited, It uses for normal arc welding, such as MIG, TIG, and MAG, electric resistance welding, such as spot welding and seam welding, and electric resistance welding. Methods such as high-frequency resistance welding, high-frequency induction welding, and laser welding can be used.

  No. having the component composition shown in Table 1. Steels 1 to 27 were melted in a vacuum melting furnace, cast into a 50 kg steel ingot, and forged into two parts. Thereafter, one of the two steel ingots was heated to 1170 ° C., and then hot-rolled to form a hot-rolled sheet having a thickness of 5 mm. Cold-rolled, finish-annealed at a temperature of 1030 ° C., cooled at an average cooling rate of 20 ° C./sec, pickled to form a cold-rolled annealed plate having a thickness of 2 mm, and the following oxidation resistance test and impact test It was used for. For reference, No. 1 in Table 1 was used. For the SUS444, Type 429, and invention steels of Patent Documents 2 to 4 shown in 28 to 32, cold-rolled annealed plates were produced in the same manner as described above and subjected to the same evaluation test.

<Atmospheric continuous oxidation test>
Cut out a 30mm x 20mm sample from the various cold-rolled annealed plates obtained as described above, drill a 4mmφ hole at the top of the sample, polish the surface and end face with # 320 emery paper, degrease, and heat to 950 ° C It was suspended in a furnace in a maintained atmospheric atmosphere and held for 300 hours. After the test, the mass of the sample was measured, the difference from the pre-measured mass before the test was determined, and the increase in oxidation (g / m ² ) was calculated. In addition, the test was implemented twice and the continuous oxidation resistance was evaluated by the average value.
<Atmospheric repeated oxidation test>
Samples of 30 mm × 20 mm were cut out from the various cold-rolled annealed plates, 4 mmφ holes were made in the upper part of the sample, the surface and end surfaces were polished with # 320 emery paper, degreased, and then at 100 ° C. and 950 in the atmosphere. An oxidation test was repeated in which the temperature was raised and lowered between the temperatures. The temperature increase and decrease rates were 5 ° C./sec and 1.5 ° C./sec, respectively, and the holding times were 100 ° C. for 1 min and 950 ° C. for 25 min, and this was performed for 600 cycles. For the evaluation of the repeated oxidation resistance, the mass of the sample after the test was measured, and the difference from the pre-test mass that had been measured in advance was determined to determine the scale peeling amount (g / m ² ). The test was performed twice, and the oxidation resistance was evaluated with the average value.
<Charpy impact test>
Three Charpy impact test pieces with V notches perpendicular to the rolling direction were sampled from each of the various cold-rolled annealed plates, and Charpy impact tests were performed at a temperature of −40 ° C. to measure the brittle fracture surface ratio. And the average value of three was calculated | required and toughness was evaluated.

  The remaining steel ingot of the 50 kg steel ingot divided into two in Example 1 was heated to 1170 ° C. and hot-rolled to obtain a sheet bar having a thickness of 30 mm × width: 150 mm. Thereafter, this sheet bar is forged into a 35 mm × 35 mm bar, annealed at a temperature of 1030 ° C., machined, processed into a thermal fatigue test piece having the dimensions shown in FIG. 1, and subjected to the following thermal fatigue test. did. As a reference example, similarly to Example 1, samples were similarly prepared for SUS444, Type 429, and invention steels of Patent Documents 2 to 4, and subjected to a thermal fatigue test.

<Thermal fatigue test>
In the thermal fatigue test, the thermal fatigue life was measured by repeatedly raising and lowering the temperature between 100 ° C. and 850 ° C. with a restraint ratio of 0.35. At this time, the temperature increase / decrease rate was 10 ° C./sec, the retention time at 100 ° C. was 2 min, and the retention time at 850 ° C. was 5 min. The thermal fatigue life is calculated by dividing the load detected at 100 ° C by the cross-sectional area of the test piece soaking parallel part, and when the stress begins to decrease continuously with respect to the stress of the previous cycle. The minimum number of cycles.

  Table 2 summarizes the results of the atmospheric continuous oxidation test, the atmospheric repeated oxidation test, and the Charpy impact test of Example 1 and the heat fatigue resistance test of Example 2. As is clear from Table 2, all of the steels of the inventive examples conforming to the present invention have oxidation resistance and thermal fatigue characteristics equivalent to or better than SUS444, and have toughness equivalent to or better than Type 429. And meets the goals of the present invention. On the other hand, the steel of the comparative example which is out of the scope of the present invention or the steel of the reference example of the prior art does not have excellent oxidation resistance, heat fatigue resistance and toughness of the base material at the same time. The characteristics are not obtained.

  The steel of the present invention is not only suitable for exhaust system members such as automobiles, but also suitably used as exhaust system members for thermal power generation systems and solid oxide fuel cell members that require similar characteristics. be able to.

Claims (2)

C: 0.015 mass% or less,
Si: 0.5 mass% or less,
Mn: 0.5 mass% or less,
P: 0.04 mass% or less,
S: 0.006 mass% or less,
Cr: 16-20 mass% or less,
N: 0.015 mass% or less,
Nb: 0.3 to 0.55 mass%,
Ti: 0.01 mass% or less,
Mo: 0.1 mass% or less,
W: 0.1 mass% or less,
Cu: 1.0 to 2.5 mass%,
Al: Ferritic stainless steel containing 0.2 to 1.2 mass%, with the balance being Fe and inevitable impurities. In addition to the above component composition, B: 0.003 mass% or less, REM: 0.08 mass% or less, Zr: 0.5 mass% or less, V: 0.5 mass% or less, Co: 0.5 mass% or less, and Ni The ferritic stainless steel according to claim 1, comprising one or more selected from: 0.5 mass% or less.

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