WO2013133429A1 - フェライト系ステンレス鋼板 - Google Patents
フェライト系ステンレス鋼板 Download PDFInfo
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- WO2013133429A1 WO2013133429A1 PCT/JP2013/056531 JP2013056531W WO2013133429A1 WO 2013133429 A1 WO2013133429 A1 WO 2013133429A1 JP 2013056531 W JP2013056531 W JP 2013056531W WO 2013133429 A1 WO2013133429 A1 WO 2013133429A1
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
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- F01N2530/00—Selection of materials for tubes, chambers or housings
- F01N2530/02—Corrosion resistive metals
- F01N2530/04—Steel alloys, e.g. stainless steel
Definitions
- the present invention relates to a ferritic stainless steel sheet used for an exhaust system member that particularly requires oxidation resistance.
- Exhaust system members such as automobile exhaust manifolds pass high-temperature exhaust gas exhausted from the engine, so the materials that make up the exhaust members are required to have various characteristics such as high-temperature strength, oxidation resistance, and thermal fatigue properties. Ferritic stainless steel with excellent heat resistance is used.
- the exhaust gas temperature varies depending on the vehicle type, but in recent years it is often around 800-900 ° C.
- the temperature of the exhaust manifold through which the high-temperature exhaust gas discharged from the engine passes is as high as 750 to 850 ° C. Due to the recent increase in environmental problems, exhaust gas regulations have been further strengthened and fuel economy has been improved. As a result, the exhaust gas temperature is considered to rise to around 1000 ° C.
- Ferritic stainless steels used in recent years include SUS429 (JIS standard, Nb-Si added steel) and SUS444 (JIS standard, Nb-Mo added steel). Based on Nb addition, Si and Mo are added. It improves high temperature strength and oxidation resistance. However, SUS444 does not have sufficient high-temperature strength and oxidation resistance for increasing the exhaust gas temperature to over 850 ° C. Therefore, a ferritic stainless steel having a high temperature strength and oxidation resistance equal to or higher than SUS444 is desired.
- the oxidation resistance is evaluated by the amount of increase in oxidation and the amount of scale peeling in the continuous oxidation test in the atmosphere. Since automobiles are used for a long time, oxidation resistance is required when kept at 1000 ° C. for 200 hours.
- Patent Documents 1 to 4 disclose techniques for performing Cu—Mo—Nb—Mn—Si composite addition.
- Cu—Mo is added to improve the high-temperature strength and toughness
- Mn is added to improve the scale peel resistance.
- each additive element is mutually adjusted to improve the oxidation resistance of the Cu-added steel.
- the temperature of the continuous oxidation test is up to 950 ° C., and the test at 1000 ° C.
- Patent Document 3 discloses a method for dramatically improving the repeated oxidation characteristics of steel by optimizing the contents of Si and Mn. However, the total heat treatment time at the highest temperature of the repeated oxidation test is about 133 hours, and further long-term oxidation resistance has not been studied.
- Patent Document 4 discloses a technique for improving high-temperature strength and oxidation resistance by adjusting Mo and W amounts, but only the oxidation increase is evaluated, and the scale peeling amount is evaluated. Not.
- patent document 5 the inventors disclosed a technique for finely dispersing the Laves phase and the ⁇ -Cu phase by composite addition of Nb—Mo—Cu—Ti—B to obtain excellent high-temperature strength at 850 ° C. Yes.
- Patent Document 6 the Nb—Mo—Cu—Ti—B steel is used to reduce the precipitation and coarsening of the Laves phase by refining the carbonitride containing Nb as the main phase, and is excellent at 950 ° C.
- a technique for obtaining high heat resistance is disclosed.
- An object of the present invention is to provide a ferritic stainless steel having oxidation resistance higher than that of the prior art, particularly in an environment where the maximum temperature of exhaust gas is around 1000 ° C. Note that the following description is not intended to limit the present invention.
- the inventors melted Si-Mn-Nb-Mo-W-Cu-added steels having a large number of compositions, prototyped a plate material, cut out a test piece, and increased the amount of oxidation and the amount of scale peeling when used at 1000 ° C for a long time.
- Si—Mn—Nb—Mo—W—Cu-added steel having two or three kinds of compositions is excellent in long-term stability of an oxide film.
- the steel having the longest stability of the oxide film was selected from the above steels, and the relationship between the chemical increase and the amount of increase in oxidation and the amount of scale peeling at the time of long-term use at 1000 ° C. was clarified.
- FIG. 2 shows the relationship when the above results are applied to the M Cincinnati / Mn ratio (refers to (5 ⁇ Mo) / (3 ⁇ Mn) in the middle side of equation (1)). It was found that when the M / Mn ratio satisfies 20 or less, the scale peel-off amount is 1.0 mg / cm 2 or less, and excellent scale peelability can be obtained.
- the reason why the long-term stability of the oxide film is excellent when Mn is added is that the component composition of the steel of the present invention is excellent in the ability to form a Mn-containing oxide film.
- (Mn, Cr) 3 O 4 generated as an oxide film in the outermost layer is generated, and a thick scale is generated.
- generation and sublimation of MoO 3 which is easily sublimated are suppressed, defects on the scale are hardly formed, and scale peeling is difficult.
- the amount of added W is expressed by the formula (2): 2.28 ⁇ (5 ⁇ Mo + 2.5 W) / (4 ⁇ Mn) ⁇ 8.0 (2)
- the amount of increase in oxidation and the amount of scale peeling when using at 1000 ° C. for a long time are small, and the long-term stability of the oxide film is excellent. It was found to be 1/2.
- FIG. 3 shows the results of continuous oxidation tests in the atmosphere of steels selected as having excellent long-term stability of the oxide film. That is, 0.005 to 0.007% C-0.0010 to 0.012% N-17.4 to 17.8% Cr-0.13 to 0.15% Si-0.03 to 1.18% Mn—0.49 to 0.56% Nb—1.81 to 2.15% Mo—0.35 to 0.70% W—1.40 to 1.53% Cu—0.0004 to 0.0005B steel
- FIG. 3 shows the results of continuous oxidation tests in the atmosphere of steels selected as having excellent long-term stability of the oxide film. That is, 0.005 to 0.007% C-0.0010 to 0.012% N-17.4 to 17.8% Cr-0.13 to 0.15% Si-0.03 to 1.18% Mn—0.49
- the gist of the present invention is as follows. (1) In mass%, C: 0.001 to 0.020%, N: 0.001 to 0.020%, Si: 0.10 to 0.40%, Mn: 0.20 to 1.00%, Cr: 16.0-20.0%, Nb: 0.30 to 0.80%, Mo: 1.80 to 2.40%, W: 0.05 to 1.40%, Cu: 1.00 to 2.50%, B: 0.0003 to 0.0030%
- the above components are represented by the following formula (1): 3 ⁇ (5 ⁇ Mo) / (3 ⁇ Mn) ⁇ 20
- An Mn-containing ferritic stainless steel sheet characterized by containing and containing Fe and inevitable impurities.
- Mo and Mn in the formula (1) mean respective contents (mass%).
- the Mn-containing ferritic stainless steel sheet as described in (1) or (2) above, wherein the Mn-containing ferritic stainless steel sheet according to (1) or (2) above contains at least one component selected from the fourth group containing one or more of the above.
- high temperature characteristics exceeding SUS444 can be obtained, that is, ferritic stainless steel having oxidation resistance at 1000 ° C. exceeding SUS444 can be provided.
- exhaust system members such as automobiles, it becomes possible to cope with a high temperature of exhaust gas around 1000 ° C.
- the upper limit is 0.020%, preferably 0.015%, and more preferably 0.012%.
- the lower limit is 0.001%, preferably 0.002%, and more preferably 0.003%.
- the content was made 0.020% or less.
- the upper limit is preferably 0.015%, more preferably 0.012%.
- the lower limit is 0.001%, preferably 0.003%, and more preferably 0.005%.
- Si is a very important element for improving oxidation resistance. It is also an element useful as a deoxidizer. When the amount of Si added is less than 0.10%, abnormal oxidation tends to occur, and when it exceeds 0.40%, scale peeling tends to occur, so 0.10 to 0.40%.
- the upper limit is preferably 0.30%, and more preferably 0.25%.
- Si promotes precipitation of intermetallic compounds mainly composed of Fe and Nb, Mo, and W called the Laves phase at high temperatures, and reduces the amount of solid solution Nb, Mo, and W to reduce high-temperature strength. Assuming that the lower limit is set, the lower limit may be 0.10%, preferably 0.12%, and more preferably 0.15%.
- Mn is a very important element that forms (Mn, Cr) 3 O 4 on the surface layer during long-time use and contributes to scale adhesion and suppression of abnormal oxidation.
- the effect is manifested at 0.20% or more.
- excessive addition exceeding 1.00% lowers the processability at room temperature.
- the upper limit is preferably 0.87%, more preferably 0.60%.
- the lower limit is 0.20%, preferably 0.25%, and more preferably 0.30%.
- Cr is an essential element for securing oxidation resistance in the present invention.
- the lower limit was made 16.0%.
- the lower limit is preferably 16.5%, and more preferably 17.0%.
- the upper limit is 20.0%, preferably 19.5%, and more preferably 19.0%.
- Nb is an element necessary for improving high temperature strength by solid solution strengthening and precipitation strengthening by fine precipitation of the Laves phase.
- C and N are fixed as carbonitrides, contributing to the development of the recrystallization texture that affects the corrosion resistance and r value of the product plate.
- solid solution Nb increase and precipitation strengthening can be obtained by adding 0.30% or more of Nb.
- the lower limit is 0.30%, preferably 0.35%, and more preferably 0.40%.
- excessive Nb addition exceeding 0.80% promotes coarsening of the Laves phase, does not contribute to high temperature strength, and increases costs. From the above reasons, manufacturability and cost, the upper limit is 0.80%, preferably 0.75%, and more preferably 0.70%.
- Mo improves corrosion resistance, suppresses high-temperature oxidation, and is effective for precipitation strengthening by fine precipitation of the Laves phase and high-temperature strength improvement by solid solution strengthening.
- excessive addition promotes scale peeling during long-time use, promotes coarse precipitation of the Laves phase, reduces precipitation strengthening ability, and degrades workability.
- solid solution Mo increase and precipitation strengthening can be obtained by adding Mo of 1.80% or more.
- the lower limit is 1.80%, preferably 1.82%, and more preferably 1.86%.
- the upper limit should be 2.40%, preferably 2.35%, and more preferably 2.30%. In consideration of the fact that the Laves phase is coarsened and does not contribute to the high temperature strength and the cost is increased, the above 1.90 to 2.30% is desirable.
- W is an element that has the same effect as Mo and improves the high-temperature strength.
- the effect is achieved when 0.05% or more is added. can get.
- the lower limit is 0.05%, preferably 0.08%, and more preferably 0.10%.
- W is added excessively, it dissolves in the Laves phase, coarsening the precipitates and degrading manufacturability and workability.
- the upper limit is 1.40%, preferably 1.35%, and more preferably 1.30%.
- the W content is preferably 0.10 to 1.30% in consideration of the fact that, like Mo, an oxide having high sublimation properties is generated and the scale is easily peeled off.
- Cu is an element effective for improving high-temperature strength. This is a precipitation hardening effect caused by the precipitation of ⁇ -Cu, and is remarkably exhibited by addition of 1.00% or more.
- the lower limit is 1.00%, preferably 1.03%, and more preferably 1.05%.
- excessive addition causes a decrease in uniform elongation and an increase in normal temperature proof stress, which impairs press formability.
- the upper limit is preferably 2.50%, preferably 2.40%, more preferably 2.20%. Considering manufacturability and scale adhesion, 1.05 to 2.20% is preferable.
- B is an element that improves the secondary workability during the press working of the product, and the effect is exhibited by addition of 0.0003% or more.
- the lower limit is 0.0003%, preferably 0.00035%, more preferably 0.00040%.
- the upper limit may be 0.0030%, preferably 0.0025%, and more preferably 0.0029%.
- B is preferably 0.0004 to 0.0020%.
- the balance with Mn, which has the effect of suppressing MoO 3 should be in an appropriate range of 3 ⁇ (5 ⁇ Mo) / (3 ⁇ Mn) ⁇ 20 (1).
- the above M / Mn ratio is preferably 20 or less.
- the thickness reduction is reduced and the steel can be used.
- the upper and lower limits of the M Firm / Mn ratio are determined from the component ranges of Mo and Mn. However, in order to ensure the effect, the upper limit of the M Firm / Mn ratio is preferably 15 or less, more preferably 10 or less. Thereby, the scale peeling amount of the said test can be 1.0 g / cm ⁇ 2 > or less. From the viewpoint of ensuring high temperature strength and workability, the lower limit of the M / Mn ratio is preferably 3, preferably 4 and more preferably 5. In order to eliminate the scale peeling, the M Cincinnati / Mn ratio should be in the range of 3-10.
- the balance of each element is set to an appropriate range of 2.28 ⁇ (5 ⁇ Mo + 2.5W) / (4 ⁇ Mn) ⁇ 8.0 (2), It has been found that there can be almost no scale peeling (FIG. 3).
- the upper limit is preferably 7.5, and more preferably 7.0.
- the lower limit is determined from the component ranges of Mo, W, and Mn, but is preferably 2.5, and more preferably 3.0.
- the following elements may be added to further improve various properties such as high-temperature strength.
- Ni is an element that improves the corrosion resistance, but excessive addition causes an austenite phase to form at a high temperature range, causing abnormal oxidation and scale peeling on the surface.
- the upper limit should be 1.0%, preferably 0.8%, and more preferably 0.6%.
- the effect is stably expressed from Ni: 0.1%, but the lower limit is preferably 0.15%, more preferably 0.20%. Considering the manufacturing cost, the Ni content is preferably 0.2 to 0.6%.
- Al is an element that improves oxidation resistance in addition to being added as a deoxidizing element. It is also useful for improving the strength as a solid solution strengthening element. The action is stably manifested from 0.10%, but excessive addition leads to hardening, significantly lowering the uniform elongation and significantly lowering the toughness.
- the upper limit should be 1.0%, preferably 0.60%, and more preferably 0.30%.
- the lower limit is 0.01%, preferably 0.03%, and more preferably 0.10%.
- the upper limit is 0.50%, preferably 0.30%, and more preferably 0.20%.
- the lower limit is preferably 0.01%, preferably 0.03%, and more preferably 0.05%.
- Mg is an element that improves secondary workability. However, if over 0.0100% is added, workability is significantly degraded.
- the upper limit is 0.0100%, preferably 0.0050%, and more preferably 0.0010%.
- the lower limit is preferably 0.0001%, preferably 0.0003%, and more preferably 0.0004%.
- the upper limit is 0.50%, preferably 0.30%, and more preferably 0.20%.
- the lower limit is 0.05%, preferably 0.03%, and more preferably 0.01%.
- Co is an element that improves high-temperature strength. However, if it exceeds 1.50%, manufacturability and workability are remarkably deteriorated. For the above reasons, the upper limit is 1.50%, preferably 1.00%, and more preferably 0.50%. Furthermore, considering the cost, the lower limit may be 0.01%, preferably 0.03%, more preferably 0.05%.
- Zr is an element that improves oxidation resistance.
- the addition of more than 1.0% causes a coarse Laves phase to precipitate, resulting in significant deterioration in manufacturability and workability.
- the upper limit is 1.0%, preferably 0.80%, and more preferably 0.50%.
- the lower limit may be 0.01%, preferably 0.03%, and more preferably 0.05%.
- Hf is an element that improves oxidation resistance.
- the addition of more than 1.0% causes a coarse Laves phase to precipitate, resulting in significant deterioration in manufacturability and workability.
- the upper limit is 1.0%, preferably 0.80%, and more preferably 0.50%.
- the lower limit may be 0.01%, preferably 0.03%, and more preferably 0.05%.
- Ta like Zr and Hf, is an element that improves oxidation resistance.
- the addition of more than 2.0% causes a coarse Laves phase to precipitate, resulting in significant deterioration in manufacturability and workability.
- the upper limit is 2.0%, preferably 1.50%, and more preferably 1.00%.
- the lower limit may be 0.01%, preferably 0.03%, and more preferably 0.05%.
- the ferritic stainless steel sheet of the present invention shows that (Mn, Cr) 3 O 4 is formed in the outermost layer of the oxide film when heat-treated at a temperature in the range of 900 to 1000 ° C. for 100 hours or more.
- (Mn, Cr) 3 O 4 is formed in the outermost layer of the oxide film when heat-treated at a temperature in the range of 900 to 1000 ° C. for 100 hours or more.
- the amount of scale peeling when a continuous oxidation test in air at 1000 ° C. for 200 (+ 10 / ⁇ 10) hours is 1.0 mg / cm 2 or less. That is, it can confirm that this is excellent in scale peelability.
- a general ferritic stainless steel manufacturing method can be applied to the steel plate manufacturing method according to the present invention.
- a slab is manufactured by melting ferritic stainless steel having a composition within the range of the present invention, heated to 1000 to 1200 ° C., and then hot-rolled (hot rolled) in the range of 1100 to 700 ° C.
- a 6 mm hot-rolled sheet is produced.
- pickling is performed after annealing at 800 to 1100 ° C., and the annealed pickled sheet is cold-rolled (cold rolled) to produce a cold-rolled sheet having a thickness of 1.5 to 2.5 mm.
- finish annealing at 1100 ° C. it is possible to produce a steel sheet by a process of pickling.
- the average cooling rate from the final annealing temperature is 600 ° C. to 5 ° C./sec or more.
- it is desirable to control the average cooling rate from the final annealing temperature to 600 ° C. to 5 ° C./sec or more.
- hot-rolled sheet hot-rolling conditions hot-rolled sheet thickness, the presence or absence of hot-rolled sheet annealing, cold-rolling conditions, hot-rolled sheet and cold-rolled sheet annealing temperature, atmosphere, and the like.
- cold rolling / annealing may be repeated a plurality of times, or temper rolling or tension leveler may be applied after cold rolling / annealing.
- the product plate thickness may be selected according to the required member thickness.
- Example creation method Steels having the component compositions shown in Tables 1 and 2 were melted and cast into 50 kg slabs, and the slabs were hot-rolled at 1100 to 700 ° C. to obtain hot rolled sheets having a thickness of 5 mm. Thereafter, the hot-rolled sheet was annealed at 900 to 1000 ° C., and then pickled, cold-rolled to a thickness of 2 mm, annealed and pickled, to obtain a product sheet. The annealing temperature of the cold-rolled sheet was controlled to 1000 to 1200 ° C., and the cooling rate from the annealing temperature to 600 ° C. was controlled to 5 ° C./sec or more. No. in Table 1 1 to 23 are examples of the present invention, No.
- ⁇ Oxidation resistance test method An oxidation test piece having a thickness of 20 mm ⁇ 20 mm was obtained from the product plate thus obtained, and subjected to a continuous oxidation test for 200 (+ 10 / ⁇ 10) hours at 1000 ° C. in the atmosphere. The presence or absence of peeling was evaluated (based on JIS Z 2281). When the increase in oxidation was 4.0 mg / cm 2 or less, B (conformity) was indicated as no abnormal oxidation, and C (nonconformity) was indicated as other abnormal oxidation. Moreover, B (conformity) if the scale peeling amount was 1.0 mg / cm 2 or less, A (excellent) if there was no scale peeling, and C (non-conforming) other than that with scale peeling.
- a JIS No. 13B test piece having a longitudinal direction parallel to the rolling direction was prepared in accordance with JIS Z 2201.
- a tensile test was performed using these test pieces, and the elongation at break was measured (in accordance with JIS Z 2241).
- the elongation at break at room temperature is 30% or more, it can be processed into a general exhaust part. Therefore, if it has a break elongation of 30% or more, B (conformity), if it is less than 30% C (non-conforming).
- No. 20 is a No. 20 that satisfies only formula (1).
- the inventive examples have good ductility at break in mechanical properties at room temperature and have workability equal to or higher than that of the comparative examples.
- the ferritic stainless steel of the present invention is excellent in heat resistance, it can be used as an exhaust gas path member of a power plant in addition to a processed product of an automobile exhaust system member. Furthermore, since Mo which is effective for improving corrosion resistance is added, it can be used for applications where corrosion resistance is required.
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Abstract
Description
なお、以下のいかなる記載も本発明を限定する趣旨ではない。
3≦(5×Mo)/(3×Mn)≦20・・・(1)
を満たすように制御すると、1000℃長時間使用時の酸化増量およびスケール剥離量は少なく、酸化膜の長期安定性に優れることを見出した。また、Tiを含有した場合、スケール剥離性が劣化することが判明した。
すなわち、前記酸化膜の長期安定性に優れた鋼であるSi-Mn-Nb-Mo-W-Cu添加鋼として、0.005~0.008%C-0.009~0.013%N-16.9~17.5%Cr-0.13~0.19%Si-0.03~1.18%Mn-0.49~0.55%Nb-2.14~2.94%Mo-0.67~0.80%W-1.40~1.55%Cu-0.0003~0.0006B鋼を用いた。図1に、1000℃で200時間の大気中連続酸化試験を行った場合のスケール剥離量の検討結果を示す。Mnの添加量が0.20%以上となった鋼種では、スケール剥離量が減少し、0.30%以上になるとスケール剥離量がほぼ0になっていることがわかる。また、図2に上記の結果をMо/Mn比((1)式の中辺の(5×Mo)/(3×Mn)をいう。)にあてはめた場合の関係を示す。Mо/Mn比が20以下を満たす場合に、スケール剥離量が1.0mg/cm2以下であり、優れたスケール剥離性を得られることが判明した。Mnを添加すると酸化膜の長期安定性に優れる理由は、本発明鋼の成分組成においてはMn含有酸化膜の形成能に優れることに起因すると考えられる。長時間高温にさらされることにより、酸化膜として最外層に生成される(Mn,Cr)3O4が生成し、厚みのあるスケールを生成する。その結果、昇華しやすいMoO3の生成および昇華が抑制され、スケールに欠陥ができにくくなり、スケール剥離しにくくなるものと推察される。このMn含有酸化膜の存在を確認するには、熱処理後の断面をEPMAで元素マッピングを行い、Mnが最外層で濃化しているかで判断することが可能である。
2.28≦(5×Mo+2.5W)/(4×Mn)≦8.0・・・(2)
を満たすように制御すると、より1000℃長時間使用時の酸化増量およびスケール剥離量は少なく、酸化膜の長期安定性に優れる、すなわちWの耐スケール剥離性に及ぼす影響は、Moの添加量の1/2であることを見出した。
(1)質量%にて、
C:0.001~0.020%、
N:0.001~0.020%、
Si:0.10~0.40%、
Mn:0.20~1.00%、
Cr:16.0~20.0%、
Nb:0.30~0.80%、
Mo:1.80~2.40%、
W:0.05~1.40%、
Cu:1.00~2.50%、
B:0.0003~0.0030%
を含有し、さらに上記成分が下記(1)式:
3≦(5×Mo)/(3×Mn)≦20・・・(1)
を満たして含有し、残部がFeおよび不可避的不純物からなることを特徴とするMn含有フェライト系ステンレス鋼板。ここで(1)式のMo、Mnはそれぞれの含有量(質量%)を意味する。
(2)さらに下記(2)式:
2.28≦(5×Mo+2.5×W)/(4×Mn)≦8.0・・・(2)
を満たして含有することを特徴とする(1)記載のMn含有フェライト系ステンレス鋼板。ここで(2)式のMo、Mn、Wはそれぞれの含有量(質量%)を意味する。
(3)質量%にて、
Ni:0.10~1.0%
Al:0.01~1.0%、
V:0.01~0.50%
の1種または2種以上を含有する第1群、
Mg:0.00010~0.0100%
を含有する第2群、
Sn:0.01~0.50%、
Co:0.01~1.50%
の1種または2種を含有する第3群、および
Zr:0.01~1.0%、
Hf:0.01~1.0%、
Ta:0.01~2.0%
の1種または2種以上を含有する第4群のうち、少なくとも1つの群から選ばれた 成分を含有することを特徴とする上記(1)又は(2)記載のMn含有フェライト 系ステンレス鋼板。
(4)900~1000℃×100~200時間の条件で熱処理を施した時に、酸化膜の最外層に(Mn,Cr)3O4が生成することを特徴とする(1)~(3)に記載のMn含有酸化膜形成能およびスケール剥離性を有するフェライト系ステンレス鋼板。
(5)(1)~(3)に記載のフェライト系ステンレス鋼板に、1000℃で200時間の大気中連続酸化試験を行った場合のスケール剥離量が、1.0mg/cm2以下であることを特徴とする(1)~(4)に記載のMn含有フェライト系ステンレス鋼板。
但し、過度の低減は精錬コストの増加に繋がるため、下限は0.001%、好適には0.002%、さらに好適には0.003%とするとよい。
しかし、2.40%超の過度なMо添加は、スケールの剥離を促進して耐酸化性には寄与せず、かつコスト増をもたらす。前記理由から、上限を2.40%、好適には2.35%、より好適には2.30%とするとよい。Laves相の粗大化を促進して高温強度には寄与せず、かつコスト増になることを考慮すると、前記1.90~2.30%が望ましい。
一方、過度な添加は、均一伸びの低下や常温耐力の上昇をもたらし、プレス成型性に支障が生じる。また、Cuを2.50%以上添加すると、高温域でオーステナイト相が形成され表面に異常酸化が生じる。前記理由から、上限を2.50%、好適には2.40%、より好適には2.20%とするとよい。製造性やスケール密着性をも考慮すると、前記1.05~2.20%が望ましい。
なお、高温強度および加工性を確保する観点から、Mо/Mn比の下限を3、好適には4、より好適には5とするとよい。スケール剥離がほぼないようにするには、Mо/Mn比を3~10の範囲にすればよい。
表1、表2に示す成分組成の鋼を溶製して50kgのスラブに鋳造し、スラブを1100~700℃で熱間圧延して板厚5mmの熱延板とした。その後、熱延板を900~1000℃で焼鈍した後に酸洗を施し、板厚2mmまで冷間圧延し、焼鈍・酸洗を施して製品板とした。冷延板の焼鈍温度は、1000~1200℃、焼鈍温度から600℃までの冷却速度は5℃/sec以上に制御した。表1のNo.1~23は本発明例、表2のNo.24~49は比較例である。表2において、本発明範囲から外れる数値にアンダーラインを付している。表1、2において、「-」は積極的に添加せず不可避的不純物レベルであることを意味する。また(2)式の中辺が好ましい範囲外である数値を太字で示している。
このようにして得られた製品板から20mm×20mm、板厚のままの酸化試験片を作製し、大気中1000℃で200(+10/-10)時間の連続酸化試験を行い、異常酸化とスケール剥離の発生有無を評価した(JIS Z 2281に準拠)。酸化増量が4.0mg/cm2以下であれば、異常酸化なしとしてB(適合)、それ以外を異常酸化ありとしてC(不適合)とした。また、スケール剥離量が1.0mg/cm2以下であればB(適合)、スケール剥離がなければA(優良)、それ以外をスケール剥離ありとしてC(不適合)とした。
耐酸化性試験方法で連続酸化試験を行った試験片の断面を、樹脂で埋め込んだ後に鏡面研磨した試験片を、EPMAで元素マッピングを行い、Mnが最外層で濃化しているか確認した。2000倍でスケール最表層部をFe,Cr,Mn,Si,Oの元素マッピングを行い、最外層にMnが8質量%以上濃化していれば、Mn含有酸化膜有としてB(適合)、それ以外をなしとしてC(不適合)とした。
製品板から圧延方向を長手方向とする長さ100mmの高温引張試験片を作製し、1000℃引張試験を行い、0.2%耐力を測定した(JIS G 0567に準拠)。ここで、1000℃の0.2%耐力が11MPa以上の場合はB(適合)、11MPa未満の場合はC(不適合)とした。
JIS Z 2201に準拠して圧延方向と平行方向を長手方向とするJIS13B号試験片を作製した。これらの試験片を用いて引張試験を行い、破断伸びを測定した(JIS Z 2241に準拠)。ここで、常温での破断伸びは30%以上あれば、一般的な排気部品への加工が可能なため、30%以上の破断伸びを有した場合はB(適合)、30%未満の場合はC(不適合)とした。
表1、表2から明らかなように、本発明で規定する成分組成を有する鋼は、比較例に比べて1000℃における酸化増量やスケール剥離量が少なく、高温耐力も優れていることがわかる。また、式(2)を満たす本発明例のNo.1,5,6,8,9,12,17,18,19は、スケール剥離量評価結果がすべてA(優良)であり、式(1)のみを満たす他の本発明例(スケール剥離量評価結果がB(適合))と比較して、スケール剥離量がほぼないことがわかる。Mn、Mo、W以外の成分が同等である本発明例のNo.20とNo.21を比較すると、式(1)および(2)を満たすNo.20のほうが、式(1)のみを満たすNo.21よりも耐スケール剥離量が優れていることがわかる。さらに本発明例は、常温での機械的性質において破断延性が良好となり、比較例と同等以上の加工性を有することがわかる。
Claims (5)
- 質量%にて、
C:0.001~0.020%、
N:0.001~0.020%、
Si:0.10~0.40%、
Mn:0.20~1.00%、
Cr:16.0~20.0%、
Nb:0.30~0.80%、
Mo:1.80~2.40%、
W:0.05~1.40%、
Cu:1.00~2.50%、
B:0.0003~0.0030%
を含有し、さらに下記(1)式
を満たして含有し、残部がFeおよび不可避的不純物からなることを特徴とするMn含有フェライト系ステンレス鋼板。
3≦(5×Mo)/(3×Mn)≦20・・・(1)
ここで(1)式のMo、Mnはそれぞれの含有量(質量%)を意味する。 - さらに下記(2)式を満たして含有することを特徴とする請求項1に記載のMn含有フェライト系ステンレス鋼板。
2.28≦(5×Mo+2.5×W)/(4×Mn)≦8.0・・・(2)
ここで(2)式のMo、Mn、Wはそれぞれの含有量(質量%)を意味する。 - 質量%にて、
Ni:0.10~1.0%
Al:0.01~1.0%、
V:0.01~0.50%
の1種以上を含有する第1群、Mg:0.00010~0.0100%を含有する第2群、
Sn:0.01~0.50%、
Co:0.01~1.50%
の1種以上を含有する第3群、および
Zr:0.01~1.0%、
Hf:0.01~1.0%、
Ta:0.01~2.0%
の1種以上を含有する第4群の少なくとも1群から選ばれた成分を含有することを特徴とする請求項1または2記載のMn含有フェライト系ステンレス鋼板。 - 900~1000℃×100時間以上の条件で熱処理を施したときに、酸化膜の最外層に(Mn,Cr)3O4が生成することを特徴とする請求項1乃至3のいずれか1項に記載のMn含有フェライト系ステンレス鋼板。
- 請求項1乃至3のいずれかに記載のフェライト系ステンレス鋼板に、1000℃で200時間の大気中連続酸化試験を行った場合のスケール剥離量が、1.0mg/cm2以下であることを特徴とする請求項1乃至4のいずれか1項に記載のMn含有フェライト系ステンレス鋼板。
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KR101659185B1 (ko) * | 2014-12-26 | 2016-09-23 | 주식회사 포스코 | 페라이트계 스테인리스강 |
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KR20220127296A (ko) * | 2020-03-02 | 2022-09-19 | 제이에프이 스틸 가부시키가이샤 | 고체 산화물형 연료 전지용 페라이트계 스테인리스강 |
Citations (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0533104A (ja) * | 1991-07-26 | 1993-02-09 | Nisshin Steel Co Ltd | 耐熱性, 低温靭性および溶接性に優れたフエライト系耐熱用ステンレス鋼 |
JP2696584B2 (ja) | 1990-03-24 | 1998-01-14 | 日新製鋼株式会社 | 低温靭性,溶接性および耐熱性に優れたフエライト系耐熱用ステンレス鋼 |
JP2009001834A (ja) | 2007-06-19 | 2009-01-08 | Jfe Steel Kk | 高温強度、耐熱性および加工性に優れるフェライト系ステンレス鋼 |
JP2009120894A (ja) * | 2007-11-13 | 2009-06-04 | Nisshin Steel Co Ltd | 自動車排ガス経路部材用フェライト系ステンレス鋼材 |
JP2009197307A (ja) * | 2008-02-25 | 2009-09-03 | Jfe Steel Corp | 高温強度、耐水蒸気酸化性および加工性に優れるフェライト系ステンレス鋼 |
JP2009215648A (ja) | 2008-02-13 | 2009-09-24 | Nippon Steel & Sumikin Stainless Steel Corp | 高温強度に優れたフェライト系ステンレス鋼板およびその製造方法 |
JP2009235555A (ja) | 2008-03-28 | 2009-10-15 | Nippon Steel & Sumikin Stainless Steel Corp | 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板 |
JP2010156039A (ja) | 2008-12-04 | 2010-07-15 | Jfe Steel Corp | 耐熱性に優れるフェライト系ステンレス鋼 |
JP2011068948A (ja) * | 2009-09-25 | 2011-04-07 | Nisshin Steel Co Ltd | スターリングエンジンの熱交換器 |
WO2011111871A1 (ja) * | 2010-03-11 | 2011-09-15 | 新日鐵住金ステンレス株式会社 | 耐酸化性に優れたフェライト系ステンレス鋼板並びに耐熱性に優れたフェライト系ステンレス鋼板及びその製造方法 |
JP2011190468A (ja) | 2010-03-11 | 2011-09-29 | Nippon Steel & Sumikin Stainless Steel Corp | 耐熱性に優れたフェライト系ステンレス鋼板およびその製造方法 |
Family Cites Families (89)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS59159974A (ja) | 1983-03-02 | 1984-09-10 | Sumitomo Metal Ind Ltd | フエライト系クロムステンレス鋼 |
JPS63182818A (ja) | 1987-01-26 | 1988-07-28 | Hitachi Ltd | 乾燥装置 |
JPH04218823A (ja) | 1990-09-27 | 1992-08-10 | Toshiba Corp | スリープモード機能を備えたパーソナルコンピュータ |
JPH05320764A (ja) | 1992-03-18 | 1993-12-03 | Sumitomo Metal Ind Ltd | 高クロムフェライト系ステンレス鋼の製造方法 |
JPH088913B2 (ja) | 1992-08-26 | 1996-01-31 | 惠 橋本 | 心電図測定用着身具における電極取付構造 |
JP2896077B2 (ja) | 1993-04-27 | 1999-05-31 | 日新製鋼株式会社 | 耐高温酸化性およびスケール密着性に優れたフエライト系ステンレス鋼 |
JPH0741854A (ja) | 1993-07-27 | 1995-02-10 | Nippon Steel Corp | 靱性に優れたフェライト単相ステンレス熱延鋼板の製造方法 |
DE69516336T2 (de) | 1994-01-26 | 2000-08-24 | Kawasaki Steel Co | Verfahren zur herstellung eines stahlbleches mit hoher korrosionsbeständigkeit |
EP0683241B1 (en) | 1994-05-21 | 2000-08-16 | Yong Soo Park | Duplex stainless steel with high corrosion resistance |
JPH0860303A (ja) | 1994-08-11 | 1996-03-05 | Nisshin Steel Co Ltd | 抗菌性を有するフェライト系ステンレス鋼及び製造方法 |
JPH0874073A (ja) | 1994-09-06 | 1996-03-19 | Hitachi Cable Ltd | 塩化第二鉄エッチャントの液管理方法 |
JPH08189235A (ja) | 1995-01-11 | 1996-07-23 | Yunimatsuku:Kk | 水圧開放式キーボックス |
JPH08199237A (ja) | 1995-01-25 | 1996-08-06 | Nisshin Steel Co Ltd | 低温靭性に優れたフェライト系ステンレス熱延鋼帯の製造方法 |
JP3067577B2 (ja) | 1995-03-20 | 2000-07-17 | 住友金属工業株式会社 | 耐酸化性と高温強度に優れたフェライト系ステンレス鋼 |
JPH09279312A (ja) | 1996-04-18 | 1997-10-28 | Nippon Steel Corp | 高温特性、耐食性及び加工性に優れたフェライト系ステンレス鋼 |
JP3242007B2 (ja) | 1996-09-13 | 2001-12-25 | 日本冶金工業株式会社 | 耐酸化スケール剥離性に優れた自動車排気系部材用フェライト系ステンレス鋼 |
JP3705391B2 (ja) | 1997-02-27 | 2005-10-12 | 日新製鋼株式会社 | 熱延板の低温靱性に優れたNb含有フェライト系ステンレス鋼 |
JP3071427B2 (ja) | 1998-10-09 | 2000-07-31 | 花王株式会社 | 酵素粒子 |
JP3926492B2 (ja) | 1998-12-09 | 2007-06-06 | 新日鐵住金ステンレス株式会社 | 断続加熱時の高温強度に優れ、断続加熱時にも剥離し難い酸化スケールを有するフェライト系ステンレス鋼板 |
JP2001026826A (ja) | 1999-07-12 | 2001-01-30 | Sumitomo Metal Ind Ltd | ステンレス熱延鋼帯の製造方法 |
TW480288B (en) | 1999-12-03 | 2002-03-21 | Kawasaki Steel Co | Ferritic stainless steel plate and method |
JP2001181798A (ja) | 1999-12-20 | 2001-07-03 | Kawasaki Steel Corp | 曲げ加工性に優れたフェライト系ステンレス熱延鋼板およびその製造方法ならびに冷延鋼板の製造方法 |
JP2001223269A (ja) | 2000-02-10 | 2001-08-17 | Nec Corp | 半導体装置およびその製造方法 |
JP3804408B2 (ja) | 2000-07-13 | 2006-08-02 | Jfeスチール株式会社 | 成形性に優れたCr含有耐熱耐食鋼板の製造方法 |
KR100467719B1 (ko) | 2000-12-08 | 2005-01-24 | 주식회사 포스코 | 리징 저항성 및 스피닝 가공성이 우수한 페라이트계스테인리스강 및 그 제조 방법 |
JP4545335B2 (ja) | 2001-03-21 | 2010-09-15 | 日新製鋼株式会社 | 耐リジング性に優れたFe−Cr系鋼板およびその製造法 |
JP3696552B2 (ja) | 2001-04-12 | 2005-09-21 | 日新製鋼株式会社 | 加工性,冷間鍛造性に優れた軟質ステンレス鋼板 |
CN1225566C (zh) | 2001-07-05 | 2005-11-02 | 日新制钢株式会社 | 用作排放汽车废气的管道构件的铁素体不锈钢 |
JP3935713B2 (ja) * | 2001-11-21 | 2007-06-27 | 株式会社サンエー化研 | 再閉封可能な易開封包装体および再閉封可能な易開封包装体に形成した開口の開閉方法 |
JP4340448B2 (ja) | 2002-03-28 | 2009-10-07 | 日新製鋼株式会社 | 燃料電池セパレータ用フェライト系ステンレス鋼及びその製造方法 |
KR100733016B1 (ko) | 2002-06-17 | 2007-06-27 | 제이에프이 스틸 가부시키가이샤 | Тi첨가 페라이트계 스테인레스 강판 및 그 제조방법 |
FR2845397B1 (fr) | 2002-10-02 | 2005-07-29 | Allevard Rejna Autosuspensions | Installation de trempe par induction, notamment pour la fabrication d'elements de suspension |
KR100629988B1 (ko) | 2002-12-12 | 2006-09-29 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | 가공성이 우수한 Cr 함유 내열 강판 및 그 제조 방법 |
JP4309140B2 (ja) | 2003-01-15 | 2009-08-05 | 新日鐵住金ステンレス株式会社 | 自動車排気系機器用フェライト系ステンレス鋼 |
US7294212B2 (en) | 2003-05-14 | 2007-11-13 | Jfe Steel Corporation | High-strength stainless steel material in the form of a wheel rim and method for manufacturing the same |
JP4519505B2 (ja) | 2004-04-07 | 2010-08-04 | 新日鐵住金ステンレス株式会社 | 成形性に優れるフェライト系ステンレス鋼板およびその製造方法 |
JP2006037176A (ja) | 2004-07-28 | 2006-02-09 | Nisshin Steel Co Ltd | エキゾーストマニホールド用フェライト系ステンレス鋼 |
JP4468137B2 (ja) | 2004-10-20 | 2010-05-26 | 日新製鋼株式会社 | 熱疲労特性に優れたフェライト系ステンレス鋼材および自動車排ガス経路部材 |
EP2351866B1 (en) | 2004-10-27 | 2014-11-26 | Global Tough Alloys Pty Ltd | Improved wear resistant alloy |
JP2006171377A (ja) | 2004-12-16 | 2006-06-29 | Canon Inc | 現像剤受け入れ装置及び現像剤補給容器及び画像形成装置 |
JP4721917B2 (ja) | 2005-01-24 | 2011-07-13 | 新日鐵住金ステンレス株式会社 | 成形時の面内異方性が小さく耐リジング性及び耐肌荒れ性に優れた低炭素低窒素フェライト系ステンレス鋼薄板及びその製造方法 |
JP4498950B2 (ja) | 2005-02-25 | 2010-07-07 | 新日鐵住金ステンレス株式会社 | 加工性に優れた排気部品用フェライト系ステンレス鋼板およびその製造方法 |
JP4088316B2 (ja) | 2006-03-24 | 2008-05-21 | 株式会社神戸製鋼所 | 複合成形性に優れた高強度熱延鋼板 |
CN101045054A (zh) | 2006-03-29 | 2007-10-03 | 上海医药工业研究院 | 尼莫地平纳米混悬剂冻干组合物、其制备方法及应用 |
JP4727601B2 (ja) | 2007-02-06 | 2011-07-20 | 新日鐵住金ステンレス株式会社 | 耐すきま腐食性に優れたフェライト系ステンレス鋼 |
CA2662965A1 (en) * | 2006-09-19 | 2008-03-27 | Wyeth | Use of lxr agonists for the treatment of osteoarthritis |
JP5000281B2 (ja) | 2006-12-05 | 2012-08-15 | 新日鐵住金ステンレス株式会社 | 加工性に優れた高強度ステンレス鋼板およびその製造方法 |
JP2008144189A (ja) | 2006-12-06 | 2008-06-26 | Railway Technical Res Inst | カーボン系すり板 |
JP4948998B2 (ja) | 2006-12-07 | 2012-06-06 | 日新製鋼株式会社 | 自動車排ガス流路部材用フェライト系ステンレス鋼および溶接鋼管 |
JP4306734B2 (ja) | 2007-01-31 | 2009-08-05 | カシオ計算機株式会社 | 平面円偏波アンテナ及び電子機器 |
JP5010301B2 (ja) | 2007-02-02 | 2012-08-29 | 日新製鋼株式会社 | 排ガス経路部材用フェライト系ステンレス鋼および排ガス経路部材 |
US8059236B2 (en) | 2007-02-15 | 2011-11-15 | Au Optronics Corporation | Method for producing reflective layers in LCD display |
JP5297630B2 (ja) | 2007-02-26 | 2013-09-25 | 新日鐵住金ステンレス株式会社 | 耐熱性に優れたフェライト系ステンレス鋼板 |
JP5092498B2 (ja) | 2007-03-30 | 2012-12-05 | Jfeスチール株式会社 | 低降伏比高強度高靱性鋼板及びその製造方法 |
JP2008297531A (ja) | 2007-05-02 | 2008-12-11 | Yoshishige Katori | バイオ燃料製造方法及びその装置 |
JP4949124B2 (ja) | 2007-05-22 | 2012-06-06 | 新日鐵住金ステンレス株式会社 | 形状凍結性に優れた高強度複相ステンレス鋼板及びその製造方法 |
JP2009035756A (ja) | 2007-07-31 | 2009-02-19 | Nisshin Steel Co Ltd | 高温強度に優れた二輪車排ガス経路部材用Al系めっき鋼板および部材 |
ES2651023T3 (es) | 2007-08-20 | 2018-01-23 | Jfe Steel Corporation | Chapa de acero inoxidable ferrítico excelente en cuanto a capacidad de troquelado y procedimiento para la producción de la misma |
JP5396752B2 (ja) | 2007-10-02 | 2014-01-22 | Jfeスチール株式会社 | 靭性に優れたフェライト系ステンレス鋼およびその製造方法 |
JP5178156B2 (ja) * | 2007-11-13 | 2013-04-10 | 日新製鋼株式会社 | 自動車排ガス経路部材用フェライト系ステンレス鋼材 |
KR101689519B1 (ko) | 2007-12-26 | 2016-12-26 | 가부시키가이샤 한도오따이 에네루기 켄큐쇼 | 증착용 기판, 증착용 기판의 제조방법, 및 발광장치의 제조방법 |
JP5390175B2 (ja) | 2007-12-28 | 2014-01-15 | 新日鐵住金ステンレス株式会社 | ろう付け性に優れたフェライト系ステンレス鋼 |
JP5401039B2 (ja) | 2008-01-11 | 2014-01-29 | 日新製鋼株式会社 | フェライト系ステンレス鋼及びその製造方法 |
JP5264199B2 (ja) | 2008-01-28 | 2013-08-14 | 日新製鋼株式会社 | フェライト系ステンレス鋼を用いたegrクーラー |
JP5141296B2 (ja) * | 2008-02-25 | 2013-02-13 | Jfeスチール株式会社 | 高温強度と靭性に優れるフェライト系ステンレス鋼 |
CN101538683A (zh) | 2008-03-19 | 2009-09-23 | 宝山钢铁股份有限公司 | 具有优良成型性的铁素体不锈钢及其制造方法 |
WO2010010916A1 (ja) | 2008-07-23 | 2010-01-28 | 新日鐵住金ステンレス株式会社 | 尿素水タンク用フェライト系ステンレス鋼 |
JP5283136B2 (ja) | 2008-09-05 | 2013-09-04 | 国立大学法人東北大学 | 窒素添加Co−Cr−Mo合金の結晶粒微細化方法および窒素添加Co−Cr−Mo合金 |
JP2010100877A (ja) | 2008-10-22 | 2010-05-06 | Jfe Steel Corp | 靭性に優れるフェライト系ステンレス熱延鋼板の製造方法 |
JP4986975B2 (ja) | 2008-10-24 | 2012-07-25 | 新日鐵住金ステンレス株式会社 | 加工性、耐酸化性に優れたAl含有耐熱フェライト系ステンレス鋼板及びその製造方法 |
JP5462583B2 (ja) | 2008-10-24 | 2014-04-02 | 新日鐵住金ステンレス株式会社 | Egrクーラ用フェライト系ステンレス鋼板 |
JP5438302B2 (ja) | 2008-10-30 | 2014-03-12 | 株式会社神戸製鋼所 | 加工性に優れた高降伏比高強度の溶融亜鉛めっき鋼板または合金化溶融亜鉛めっき鋼板とその製造方法 |
JP5546911B2 (ja) | 2009-03-24 | 2014-07-09 | 新日鐵住金ステンレス株式会社 | 耐熱性と加工性に優れたフェライト系ステンレス鋼板 |
JP4702493B1 (ja) | 2009-08-31 | 2011-06-15 | Jfeスチール株式会社 | 耐熱性に優れるフェライト系ステンレス鋼 |
JP4831256B2 (ja) | 2010-01-28 | 2011-12-07 | Jfeスチール株式会社 | 靭性に優れた高耐食性フェライト系ステンレス熱延鋼板 |
CN102741445B (zh) | 2010-02-02 | 2014-12-17 | 杰富意钢铁株式会社 | 韧性优异的高耐腐蚀性铁素体系不锈钢冷轧钢板及其制造方法 |
CN102711448B (zh) | 2010-02-15 | 2014-11-26 | 利拉伐控股有限公司 | 一种动物处理装置 |
JP5600968B2 (ja) | 2010-03-03 | 2014-10-08 | カシオ計算機株式会社 | 自動演奏装置および自動演奏プログラム |
JP5677819B2 (ja) | 2010-11-29 | 2015-02-25 | 新日鐵住金ステンレス株式会社 | 耐酸化性に優れたフェライト系ステンレス鋼板 |
JP2011190524A (ja) | 2010-03-17 | 2011-09-29 | Nisshin Steel Co Ltd | 耐酸化性、二次加工脆性および溶接部の靭性に優れたフェライト系ステンレス鋼 |
ES2581315T3 (es) | 2010-03-29 | 2016-09-05 | Nippon Steel & Sumikin Stainless Steel Corporation | Lámina de acero inoxidable ferrítico excelente en brillo superficial y resistencia a la corrosión, y método para producir la misma |
JP2011246813A (ja) | 2010-04-30 | 2011-12-08 | Jfe Steel Corp | フェライト系ステンレス鋼板およびその製造方法 |
CN101845803B (zh) | 2010-05-28 | 2011-08-03 | 武汉理工大学 | 多杆式管涌卡 |
JP5793283B2 (ja) | 2010-08-06 | 2015-10-14 | 新日鐵住金ステンレス株式会社 | ブラックスポットの生成の少ないフェライト系ステンレス鋼 |
JP5737951B2 (ja) | 2011-01-05 | 2015-06-17 | 日新製鋼株式会社 | Ti含有フェライト系ステンレス鋼熱延コイルおよび製造法 |
JP5737952B2 (ja) | 2011-01-05 | 2015-06-17 | 日新製鋼株式会社 | Nb含有フェライト系ステンレス鋼熱延コイルおよび製造法 |
WO2012108473A1 (ja) | 2011-02-08 | 2012-08-16 | 国立大学法人高知大学 | カルサイト単結晶の製造方法 |
JP5659061B2 (ja) | 2011-03-29 | 2015-01-28 | 新日鐵住金ステンレス株式会社 | 耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法 |
JP6071608B2 (ja) | 2012-03-09 | 2017-02-01 | 新日鐵住金ステンレス株式会社 | 耐酸化性に優れたフェライト系ステンレス鋼板 |
-
2013
- 2013-02-08 JP JP2013023416A patent/JP6071608B2/ja active Active
- 2013-03-08 WO PCT/JP2013/056531 patent/WO2013133429A1/ja active Application Filing
- 2013-03-08 CN CN201380012714.8A patent/CN104160054B/zh active Active
- 2013-03-08 PL PL13757964T patent/PL2824208T3/pl unknown
- 2013-03-08 KR KR1020147024652A patent/KR101614236B1/ko active IP Right Grant
- 2013-03-08 ES ES13757964T patent/ES2818560T3/es active Active
- 2013-03-08 US US14/384,121 patent/US9885099B2/en active Active
- 2013-03-08 EP EP13757964.5A patent/EP2824208B1/en active Active
-
2017
- 2017-10-06 US US15/726,722 patent/US20180044767A1/en not_active Abandoned
Patent Citations (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2696584B2 (ja) | 1990-03-24 | 1998-01-14 | 日新製鋼株式会社 | 低温靭性,溶接性および耐熱性に優れたフエライト系耐熱用ステンレス鋼 |
JPH0533104A (ja) * | 1991-07-26 | 1993-02-09 | Nisshin Steel Co Ltd | 耐熱性, 低温靭性および溶接性に優れたフエライト系耐熱用ステンレス鋼 |
JP2009001834A (ja) | 2007-06-19 | 2009-01-08 | Jfe Steel Kk | 高温強度、耐熱性および加工性に優れるフェライト系ステンレス鋼 |
JP2009120894A (ja) * | 2007-11-13 | 2009-06-04 | Nisshin Steel Co Ltd | 自動車排ガス経路部材用フェライト系ステンレス鋼材 |
JP2009215648A (ja) | 2008-02-13 | 2009-09-24 | Nippon Steel & Sumikin Stainless Steel Corp | 高温強度に優れたフェライト系ステンレス鋼板およびその製造方法 |
JP2009197307A (ja) * | 2008-02-25 | 2009-09-03 | Jfe Steel Corp | 高温強度、耐水蒸気酸化性および加工性に優れるフェライト系ステンレス鋼 |
JP2009235555A (ja) | 2008-03-28 | 2009-10-15 | Nippon Steel & Sumikin Stainless Steel Corp | 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板 |
JP2010156039A (ja) | 2008-12-04 | 2010-07-15 | Jfe Steel Corp | 耐熱性に優れるフェライト系ステンレス鋼 |
JP2011068948A (ja) * | 2009-09-25 | 2011-04-07 | Nisshin Steel Co Ltd | スターリングエンジンの熱交換器 |
WO2011111871A1 (ja) * | 2010-03-11 | 2011-09-15 | 新日鐵住金ステンレス株式会社 | 耐酸化性に優れたフェライト系ステンレス鋼板並びに耐熱性に優れたフェライト系ステンレス鋼板及びその製造方法 |
JP2011190468A (ja) | 2010-03-11 | 2011-09-29 | Nippon Steel & Sumikin Stainless Steel Corp | 耐熱性に優れたフェライト系ステンレス鋼板およびその製造方法 |
Non-Patent Citations (1)
Title |
---|
YASUSHI KATO ET AL.: "Development of a Ferritic Stainless Steel with Excellent Heat Resistance", TRANSACTIONS OF THE SOCIETY OF AUTOMOTIVE ENGINEERS OF JAPAN, vol. 39, no. 2, 25 March 2008 (2008-03-25), pages 329 - 333, XP008174502 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
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WO2018180643A1 (ja) * | 2017-03-29 | 2018-10-04 | 新日鐵住金ステンレス株式会社 | 高温耐摩耗性に優れたフェライト系ステンレス鋼、フェライト系ステンレス鋼板の製造方法、排気部品、高温摺動部品、およびターボチャージャー部品 |
JPWO2018180643A1 (ja) * | 2017-03-29 | 2020-03-26 | 日鉄ステンレス株式会社 | 高温耐摩耗性に優れたフェライト系ステンレス鋼、フェライト系ステンレス鋼板の製造方法、排気部品、高温摺動部品、およびターボチャージャー部品 |
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PL2824208T3 (pl) | 2021-02-08 |
US20150044085A1 (en) | 2015-02-12 |
US9885099B2 (en) | 2018-02-06 |
CN104160054B (zh) | 2018-04-27 |
EP2824208A4 (en) | 2016-04-20 |
EP2824208A1 (en) | 2015-01-14 |
KR101614236B1 (ko) | 2016-04-20 |
EP2824208B1 (en) | 2020-08-26 |
CN104160054A (zh) | 2014-11-19 |
US20180044767A1 (en) | 2018-02-15 |
JP2013213279A (ja) | 2013-10-17 |
JP6071608B2 (ja) | 2017-02-01 |
KR20140127851A (ko) | 2014-11-04 |
ES2818560T3 (es) | 2021-04-13 |
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