WO2013147027A1 - 耐熱オーステナイト系ステンレス鋼板 - Google Patents
耐熱オーステナイト系ステンレス鋼板 Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
Definitions
- the present invention relates to a heat-resistant austenitic stainless steel used for parts exposed to high temperatures, such as an automobile turbo housing, and a method for producing the same.
- stainless steel has been used because materials used for turbo housing for automobiles and the like are required to have extremely high high-temperature strength in a high-temperature environment reaching 800 ° C.
- An austenitic stainless steel typified by SUS310S is used as a stainless steel plate used in a high temperature environment.
- SUS310S the required performance for the materials used such as high temperature strength and oxidation resistance has become strict, and SUS310S cannot fully cope with it.
- turbo related materials are high temperature strength and creep properties.
- creep properties the magnitude of deformation after a certain time is more important than the life.
- processing is essential, a certain level of workability is also required.
- the creep strength is improved by adding P.
- P has a problem of reducing weldability and creep ductility.
- the invention disclosed in Patent Document 2 improves creep ductility and weldability by adding REM, particularly Nd, in addition to P.
- the addition of REM causes an increase in cost.
- Patent Documents 3 and 4 disclose austenitic stainless steel excellent in heat resistance.
- a steel having excellent heat resistance, particularly resistance to embrittlement cracking of a welded portion is disclosed by mutually adjusting each component element.
- the creep characteristics at this time are only evaluated at 650 ° C. or lower, and are not evaluated at 800 ° C.
- the object of the present invention is to improve high temperature strength and creep characteristics with an inexpensive component system.
- carbide is considered effective for improving the high temperature strength, particularly creep strength, of austenitic stainless steel.
- Carbides such as M 23 C 6 , TiC and NbC are used for improving the creep strength.
- the present inventors paid attention to not only carbides but also nitrides, and examined in detail the effects of these on high temperature strength and creep strength. As a result, it has been found that high temperature strength and creep strength can be improved by positively adding N and Nb, adding a small amount of V, further limiting the content of Al and Ti, and devising the manufacturing method. Although the mechanism has not been elucidated in detail, the following knowledge has been obtained.
- Nb-based carbonitrides during product use at high temperatures is important for improving creep properties. -It is better to reduce the precipitation of Al and Ti nitrides as much as possible. -When Nb is added excessively, a Laves phase (Fe 2 Nb) precipitates and the creep characteristics are not improved. -Addition of a small amount of V suppresses the coarsening of the Nb-based carbonitride and is effective in improving the creep characteristics. -If precipitates such as undissolved carbonitride remain in the product, these become nucleation sites for precipitation and prevent fine precipitation of Nb-based carbonitrides.
- the amount of residual precipitates in the product affects the creep characteristics, it is better to reduce this as much as possible.
- the amount of residual precipitates depends on the production process, and is particularly affected by the heating temperature and the final annealing temperature in hot rolling.
- the present inventors have completed an invention excellent in high-temperature strength and creep characteristics by determining the optimum range of the content of Nb, V, C, N, Al, and Ti and optimizing the manufacturing process. It was. That is, the gist of the present invention is as follows.
- the hot rolling heating temperature is 1200 ° C. to 1300 ° C.
- the final annealing temperature is 1100.
- C 0.03% or more and 0.06% or less C is an element effective for securing high-temperature strength and creep strength. If the addition amount is 0.03% or more, the effect cannot be exhibited. Moreover, even if it adds 0.1% or more, only the non-solid solution carbonitride in a solution-ized state will increase.
- N 0.1% or more and 0.3% or less N is an important element in the present invention. By adding N, fine carbonitrides are formed, and the high temperature strength and creep strength are improved. If it is less than 0.1%, the effect is small. Moreover, in order to add exceeding 0.3%, special equipment is required, so the upper limit is made 0.3%.
- Si 1% or less Si is not only useful as a deoxidizing element, but also an element effective for oxidation resistance. However, if added in excess, toughness and ductility are reduced, so the upper limit is made 1%.
- Mn 3% or less Mn is useful as a deoxidizing element like Si. Further, S inevitably contained in the steel is fixed as a sulfide to improve hot workability. However, if added excessively, the mechanical properties deteriorate, so the upper limit is made 3%.
- P 0.04% or less P improves the creep strength of the steel of the present invention, but decreases creep ductility and weldability. Therefore, the upper limit is made 0.04%.
- S 0.03% or less S is contained as an inevitable impurity in the steel, and remarkably deteriorates hot workability. Therefore, 0.03% is made the upper limit.
- Ni is an essential element as an austenitic stainless steel, and is an important element for ensuring corrosion resistance. The appropriate amount is 5-12%.
- Cr 15-20% Cr is an essential element as an austenitic stainless steel, and is an important element for ensuring corrosion resistance and oxidation resistance. However, if the Cr content is high, the mechanical properties deteriorate. Therefore, it is set to 15% or more and 20% or less.
- Al 0.01% or more and 0.06% or less Al is useful because it is useful as a deoxidizing element and can be deoxidized at low cost. This effect is manifested when 0.01% or more is added. However, since Al forms AlN and degrades the creep characteristics, the addition is suppressed in the present invention, and 0.06% or less is good. A more preferable range is 0.03% to 0.06%.
- Nb 0.05% or more and 0.3% or less
- Nb is an essential element. It is considered that Nb-based carbonitride is finely precipitated and added to suppress the growth rate by adding simultaneously with N, and this effect improves the creep characteristics. This effect can be obtained by adding 0.05% or more. However, addition exceeding 0.3% is not preferable because it not only coarsens the carbonitride, but also forms Fe 2 Nb called a Laves phase, which lowers the creep characteristics.
- V 0.05% or more and 0.15% or less V is an element necessary for the present invention. It is an element that improves high temperature strength and creep strength. Furthermore, in the present invention, Nb—V-based carbonitrides are formed together with Nb, and as a result, they are more finely precipitated and the creep characteristics are further improved. This effect can be obtained by adding 0.05% or more. However, if it exceeds 0.30% and it is added excessively, the creep characteristics deteriorate due to the formation of VN, which is not preferable.
- Ti 0.03% or less
- Ti is an element to be restricted.
- Ti is not preferable because it is easily combined with C, N, particularly N, forms coarse carbonitride, suppresses formation of fine Nb-based carbonitride, and as a result, deteriorates creep characteristics. This effect is almost negligible when Ti is 0.03% or less, so this is the upper limit.
- Nb, V, C, and N It is desirable that (Nb + V) / (C + N) is 2 or less by mass%. This is because when N exceeds 2, Nb and V become excessive, a Laves phase or the like is formed, and the creep characteristics are deteriorated. Further, the lower limit is not particularly defined, but if it is too low, C and N are excessive, and there is a possibility that the corrosion resistance and the like may be lowered due to Cr-based carbide precipitation or the like.
- Cu 1% or less Cu is an element that greatly improves creep strength because it precipitates finely during use at high temperatures, and in the present invention, 1% is added to the upper limit. If it exceeds 1%, the hot workability and creep ductility, and further, the room temperature ductility is lowered, which is not preferable. In the case of adding 0.1% or more, the effect is remarkably exhibited.
- Mo 3% or less Mo is an element that improves high-temperature strength and creep characteristics, and can be added as necessary. However, excessive addition is not preferable because it impairs the tissue stability, and the addition amount is desirably 3% or less.
- W 3% or less W, like Mo, is an element that improves high-temperature strength and creep strength, and can be added as necessary. However, since excessive addition impairs the tissue stability, it is not preferable, and the addition is desirably 3% or less.
- Co 1% or less Co, like Mo and W, is an element that improves high-temperature strength and creep strength, and can be added as necessary. However, excessive addition is undesirable because it impairs the tissue stability and is also expensive, so the addition is desirably 1% or less.
- B 0.01% or less B is also an element that enhances high-temperature strength and creep characteristics. However, excessive addition lowers the room temperature ductility, so the addition is made 0.01% or less. Desirably, it is 0.0003% or more and 0.0050% or less.
- the present invention defines the amount of carbonitride deposited. This is based on the result of investigating the cause of the creep characteristics that may vary depending on the manufacturing conditions even with the same alloy amount. Observing the microstructure of the steel with inferior creep properties before and after the creep test, some coarse precipitates already existed before the creep test, and during the test the coarse precipitates became nuclei and new precipitates formed. Turned out to be. That is, the precipitate in the product inhibits fine precipitation at high temperature, which is considered to be the cause of the deterioration of the creep characteristics. Therefore, it is important to reduce the amount of precipitation in the product. The inventors conducted various tests and found that when the amount of precipitation in the product was 1% or less, the creep characteristics were not affected. Therefore, the upper limit of the amount of precipitates is set to 1%. There is no particular lower limit.
- the method for producing a steel sheet of the present invention comprises the steps of steelmaking, hot rolling, pickling, cold rolling, annealing and pickling.
- steelmaking a method in which the steel containing the above essential components and components added as necessary is subjected to furnace melting followed by secondary refining.
- the molten steel is made into a slab according to a known casting method (continuous casting).
- the slab is heated to a predetermined temperature and hot-rolled to a predetermined plate thickness by continuous rolling.
- the hot-rolled sheet After that, after annealing the hot-rolled sheet, it is cold-rolled and further subjected to final annealing and pickling to obtain a product. Cold rolling and annealing may be repeated a plurality of times. Moreover, it is good also as a product by performing bright annealing instead of final annealing and pickling.
- the annealing conditions for the bright annealing are preferably the same as those for the final annealing.
- the precipitation amount of carbonitride is important in the present invention, and it is preferable to reduce the precipitation amount in the product.
- carbonitride is generated at a relatively high temperature, it is difficult to completely dissolve the carbonitride, and a large load is generated on the production facility.
- the present inventors have studied in detail the precipitation amount of carbonitride, the creep characteristics, and the production method, and found the optimum production conditions.
- the important processes in the present invention are hot rolling and final annealing.
- the amount of carbonitride of the product is 1% or less, and excellent creep characteristics are obtained.
- the heating temperature of hot rolling is set to 1200 ° C. or more and 1300 ° C. or less.
- the temperature is lower than 1200 ° C., a large amount of undissolved carbonitride remains, and thus the creep strength decreases. Further, even if the temperature exceeds 1300 ° C., the creep characteristics are not improved, and adverse effects such as shortening the life of the heating furnace increase.
- the final annealing temperature is set to 1100 ° C. or more and 1200 ° C. or less.
- the temperature is less than 1100 ° C., a large amount of undissolved carbonitride remaining until the end of the hot rolling process remains, which is not preferable.
- the temperature exceeds 1200 ° C., the risk of plate breakage increases, so the upper limit is set to 1200 ° C.
- the manufacturing method in other steps is not particularly defined, but the hot rolling conditions, the hot rolled sheet thickness, etc. may be appropriately selected. Further, temper rolling or correction by a tension leveler may be applied after cold rolling and annealing. Further, the product plate thickness may be selected according to the required member thickness.
- the heating temperature at this time is 1250 degreeC. Thereafter, the hot-rolled coil was annealed at an annealing temperature of 1100 ° C., then pickled, further cold-rolled to a thickness of 2 mm, and subjected to annealing and pickling to obtain a product plate.
- the final annealing temperature is 1150 ° C. and the annealing time is 120 seconds.
- a normal temperature tensile test JIS 13B
- a high temperature tensile test piece were collected.
- the total elongation value obtained by conducting a room temperature tensile test (based on JIS Z 2241) was used as an index of workability.
- a tensile test was performed at 800 ° C., and 0.2% proof stress and tensile strength were measured (based on JIS G 0567).
- a creep strain test was performed using the same test piece. The test temperature was 800 ° C., the test time was 300 hours, various loads were applied, the amount of strain was determined, and the load stress that gave 1% strain was determined from these.
- the amount of extraction residue was determined from the product plate and used as the amount of precipitate.
- the X-ray diffraction test of the residue was also conducted and it was confirmed that the residue was mainly carbonitride.
- a heat resistant stainless steel plate having excellent creep characteristics can be provided.
- the contribution is significant.
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Abstract
Description
・Al、Ti系の窒化物の析出は可能な限り低減した方が良い。
・Nbが過剰に添加されると、Laves相(Fe2Nb)が析出し、クリープ特性は向上しない。
・Vを微量添加すると、Nb系炭窒化物の粗大化が抑制され、クリープ特性向上に有効である。
・製品に未固溶炭窒化物等の析出物が残存していると、これらが析出の核生成サイトとなり、Nb系炭窒化物の微細析出を妨げる。
・製品中の残存析出物量がクリープ特性に影響を与えるので、これをできるだけ低減する方が良い。
・残存析出物量は製造プロセスに依存し、特に熱間圧延の加熱温度と最終焼鈍温度の影響が大きい。
即ち本発明の要旨は、以下のとおりである。
(1)質量%で、
C:0.03%以上0.06%以下
N:0.1%以上0.3%以下
Si:1%以下
Mn:3%以下
P:0.04%以下
S:0.03%以下
Ni:5~12%
Cr:15~20%
Al:0.01%以上0.1%以下
Nb:0.05%以上0.3%以下
V:0.05%以上0.30%以下
Ti:0.03%以下
かつ、(Nb+V)/(C+N)が2以下であり、
さらに、残部Fe及び不可避的不純物からなり、鋼中の炭窒化物を主体とする析出物の量が1%以下であることを特徴とする耐熱オーステナイト系ステンレス鋼板。
Cu:1%以下、Mo:3%以下、W:3%以下、Co:1%以下、B:0.01%以下
の1種または2種以上を含有することを特徴とする(1)記載の耐熱オーステナイト系ステンレス鋼板。
C:0.03%以上0.06%以下
Cは高温強度やクリープ強度を確保するために有効な元素である。その添加量は、0.03%以上だとその効果は発揮できない。また、0.1%以上添加しても溶体化状態における未固溶炭窒化物が増えるだけである。
Nは本発明で重要な元素である。Nの添加による微細な炭窒化物が形成され、高温強度およびクリープ強度が向上する。0.1%未満だとその効果が小さい。また、0.3%を超えて添加するには、特別な設備が必要であるため、その上限を0.3%とする。
Siは脱酸元素として有用であるばかりでなく、耐酸化性にも有効な元素である。しかし、過剰に添加すると靭性や延性の低下が生じるため、その上限を1%とする。
Mnは、Siと同じく脱酸元素として有用である。また、鋼中に不可避的に含有されるSを硫化物として固着し熱間加工性を改善する。しかし、過剰に添加すると機械的特性が劣化するため、その上限を3%とする。
Pは、本発明鋼のクリープ強度を向上させるが、クリープ延性や溶接性を低下させる。そのため、上限を0.04%とする。
Sは鋼中に不可避的不純物として含有され、熱間加工性を著しく低下させる。そのため、0.03%を上限とする。
Niはオーステナイト系ステンレス鋼として、必須元素であり、また、耐食性を確保する重要な元素である。その適量は、5~12%である。
Crはオーステナイト系ステンレス鋼として、必須元素であり、耐食性、耐酸化性を確保する重要な元素である。しかし、Cr含有量が高いと機械的特性が劣化する。そのため、15%以上20%以下とする。
Alは脱酸元素として有用であり、低コストで脱酸できるため、添加している。この効果は0.01%以上の添加で発現する。しかし、AlはAlNを形成してクリープ特性を低下させるため、本発明ではその添加を抑制し、0.06%以下が良い。より好ましい範囲は、0.03%以上0.06%以下が好ましい範囲である。
本発明において、Nbは必須元素である。Nと同時に添加することにより、Nb系の炭窒化物を微細に析出させるとともに、その成長速度を抑制する働きがあると考えており、この効果によりクリープ特性が向上する。この効果は0.05%以上添加することによって得られる。しかし、0.3%を超えての添加は、炭窒化物を粗大化させてしまうだけでなく、Laves相と呼ばれるFe2Nbが形成されるため、クリープ特性を低下させるので、好ましくない。
Vは本発明に必要な元素である。高温強度、クリープ強度を向上させる元素である。さらに、本発明においては、NbとともにNb-V系の炭窒化物を形成し、その結果、より微細に析出し、クリープ特性をより向上させる。この効果は、0.05%以上添加することによって得られる。しかし、0.30%を超え、過剰に添加すると、VNの形成によりクリープ特性は低下するため、好ましくない。
本発明においてTiは制限すべき元素である。TiはC、N特にNと結びつきやすく、粗大な炭窒化物を形成し、微細なNb系炭窒化物の形成を抑制し、その結果、クリープ特性を低下させるため好ましくない。Tiが0.03%以下であるとこの弊害がほぼ無視できるので、これを上限とする。
質量%で、(Nb+V)/(C+N)が2以下となることが望ましい。2を超えるとNb、Vが過剰となり、Laves相等が形成され、クリープ特性を低下させるためである。また、下限は特に定めないが、低すぎると、C、Nが過剰であり、Cr系炭化物析出等で耐食性等を低下させる可能性があるため、0.2以上が好ましい。
Cuは高温下での使用中に微細に析出するためクリープ強度を大きく向上させる元素であり、本発明では1%を上限に添加する。1%を超えると、熱間加工性およびクリープ延性、さらには、常温延性も低下するため好ましくない。添加する場合は0.1%以上の添加でその効果が顕著に発現する。
Moは、高温強度、クリープ特性を向上させる元素であり、必要に応じて添加できる。しかし、過剰に添加すると組織安定性を損なうため好ましくなく、その添加量は3%以下が望ましい。
WもMoと同様に、高温強度、クリープ強度を向上させる元素であり、必要に応じて添加できる。しかし、過剰に添加すると組織安定性を損なうため好ましくなく、その添加は3%以下が望ましい。
CoもMo、Wと同様に、高温強度、クリープ強度を向上させる元素であり、必要に応じて添加できる。しかし、過剰に添加すると組織安定性を損なうため好ましくなく、高価でもあるため、その添加は1%以下が望ましい。
Bも高温強度、クリープ特性を高める元素である。しかし、過剰の添加は常温延性を低下させるため、その添加は0.01%以下とする。望ましくは、0.0003%以上0.0050%以下である。
更に、製品板厚についても、要求部材厚に応じて選択すれば良い。
表1から明らかなように、本発明鋼は優れた高温強度およびクリープ特性を示す。また、比較鋼は、高温強度、クリープ特性が劣位であるか、他に問題があり、好ましくないことが明らかである。
Claims (3)
- 質量%で、
C:0.03%以上0.06%以下
N:0.1%以上0.3%以下
Si:1%以下
Mn:3%以下
P:0.04%以下
S:0.03%以下
Ni:5~12%
Cr:15~20%
Al:0.01%以上0.1%以下
Nb:0.05%以上0.3%以下
V:0.05%以上0.30%以下
Ti:0.03%以下
かつ、(Nb+V)/(C+N)が2以下であり、
さらに、残部Fe及び不可避的不純物からなり、鋼中の炭窒化物を主体とする析出物の量が1%以下であることを特徴とする耐熱オーステナイト系ステンレス鋼板。
- さらに、
Cu:1%以下、Mo:3%以下、W:3%以下、Co:1%以下、B:0.01%以下
の1種または2種以上を含有することを特徴とする請求項1記載の耐熱オーステナイト系ステンレス鋼板。
- 製鋼-熱間圧延-酸洗-冷間圧延-焼鈍・酸洗の各工程からなる鋼板の製造工程において、熱間圧延の加熱温度が1200℃以上1300℃以下、最終焼鈍温度が1100℃以上1200℃以下であることを特徴とする請求項1又は2記載の耐熱オーステナイト系ステンレス鋼板の製造方法。
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