WO2012132679A1 - オーステナイト系ステンレス鋳鋼 - Google Patents
オーステナイト系ステンレス鋳鋼 Download PDFInfo
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- WO2012132679A1 WO2012132679A1 PCT/JP2012/054523 JP2012054523W WO2012132679A1 WO 2012132679 A1 WO2012132679 A1 WO 2012132679A1 JP 2012054523 W JP2012054523 W JP 2012054523W WO 2012132679 A1 WO2012132679 A1 WO 2012132679A1
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/20—Measures not previously mentioned for influencing the grain structure or texture; Selection of compositions therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D30/00—Cooling castings, not restricted to casting processes covered by a single main group
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
-
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- C21D2211/005—Ferrite
Definitions
- the present invention relates to austenitic stainless cast steel.
- austenitic cast stainless steel is particularly excellent in corrosion resistance, strength, weldability, etc., it is widely used in piping and valves of chemical plants and power plants.
- Austenitic stainless cast steel is formed, for example, from the metallurgical viewpoint of two phases of about 10 to 20% ⁇ phase and about 90 to 80% ⁇ phase (austenite phase).
- CF8C is known as a cast steel product of austenitic stainless steel.
- a CF8C austenitic stainless steel cast product has a maximum of 0.08 mass% C (carbon), a maximum of 2.0 mass% Si (silicon), a maximum of 1.5 mass% Mn (manganese), 18.0 to 21.0% by mass of Cr (chromium), 9.0 to 12.0% by mass of Ni (nickel), and a maximum of 1.0% by mass of Nb (niobium).
- CF8C contains about 12.0% ferrite phase.
- the ferrite phase can be calculated from a Schaeffler phase diagram based on the constituent elements by measuring the ferrite content in the austenitic stainless steel with a known ferrite scope, and is displayed in volume ratio (percent (%)).
- This ferrite phase is said to be effective in preventing weld cracking and reducing stress corrosion cracking.
- the ferrite phase may be transformed into a sigma phase ( ⁇ phase) that is a compound of iron and chromium and embrittled.
- Patent Document 1 discloses CF8C-Plus, which is an alloy obtained by modifying CF8C, and describes that the CF8C-Plus does not contain a ferrite phase.
- CF8C-Plus includes 0.05 to 0.15 mass% C, 0.2 to 1.0 mass% Si, 0.5 to 10.0 mass% Mn, 18.0 to 25.0% by mass of Cr, 10.0-15.0% by mass of Ni, 0.1-1.5% by mass of Nb, 0.05-0.5% by mass of N .
- an object of the present invention is to provide an austenitic stainless cast steel excellent in aging ductility and oxidation resistance.
- the volume fraction of the ferrite phase is 0.1 to 5.0%, C: 0.01 to 0.10% by mass, Si: 0.6 to 1.0% by mass, Mn: 2.0 to 2.8% by mass, N: 0.1 to 0.4% by mass, Cr: 18.0 to 24.0% by mass, Ni: 8.0 to 15.0% by mass, Nb: 0.2 to 0.7% by mass, An austenitic stainless cast steel with the balance being Fe and inevitable impurities.
- An austenitic stainless cast steel with the balance being Fe and inevitable impurities.
- [5] In any one of the above [1] to [4] obtained by cooling from a temperature range of 1150 to 1350 ° C. to a temperature range of 600 to 800 ° C. at a cooling temperature of 30 ° C./min or more. The austenitic stainless cast steel described.
- the austenitic cast stainless steel of the present invention is excellent in aging ductility, tensile strength, and oxidation resistance, for example, as shown in Examples described later.
- the aging ductility of the examples of the present invention was about 2.4 times that of the comparative examples.
- the oxidation resistance it was recognized that the example of the present invention was improved to about 9.5 times the comparative example.
- the volume fraction of the ferrite phase is 0.1 to 5.0%, and the contained components C, Si, Mn, Cr, Ni , Nb, N content is considered important. Each component will be described in detail.
- the volume ratio of the ferrite phase By setting the volume ratio of the ferrite phase to 0.1 to 5.0%, the amount of sigma phase deposited can be reduced even when exposed to high temperatures for a long period of time. By reducing the precipitation amount of the sigma phase, the austenitic stainless cast steel becomes difficult to become brittle, and an austenitic stainless cast steel excellent in aging ductility is obtained.
- C has the effect of lowering the melting point and improving the fluidity of the molten metal, that is, the castability. Further, C is preferably as low as possible from the viewpoint of corrosion resistance, and when added in a large amount, the corrosion resistance of the base material is lowered. Based on these, in the present invention, in order to improve the high temperature ductility, the amount of C added is set to 0.01 to 0.10% by mass.
- Si is an element effective for deoxidizing molten metal and improving fluidity, oxidation resistance, and weldability.
- the austenite structure becomes unstable, which causes deterioration of castability, and promotes hindrance to workability and weldability and weld cracking. Therefore, in the present invention, the amount of Si added is set to 0.6 to 1.0 mass%.
- Mn is effective as a deoxidizer for molten metal, and improves the flowability during casting to improve productivity. Furthermore, it is effective in reducing weld cracking. Since excessive addition impairs oxidation resistance, the amount of Mn added in the present invention is set to 2.0 to 2.8% by mass. If Mn is in this range, as shown in the examples described later, austenitic stainless cast steel having excellent oxidation resistance can be obtained.
- N is an element that improves high-temperature strength and heat fatigue resistance, is a strong austenite generating element, and stabilizes the austenite base. It is also an effective element for grain refinement. This refinement of crystal grains makes it possible to ensure the ductility of materials that are important as structures, and to improve the disadvantage of poor machinability that is characteristic of austenitic cast stainless steel. In particular, in a member that is subjected to a drilling process for connecting parts, the drilling processability is improved. When a large amount of N is added, embrittlement is promoted, while an effective amount of Cr is reduced and oxidation resistance is deteriorated. Therefore, in the present invention, the addition amount of N is set to 0.1 to 0.4 mass%.
- Cr is an element that improves oxidation resistance and stabilizes the ferrite structure, but in order to ensure the effect, it is made 18.0% by mass or more.
- the addition of a large amount causes a decrease in the aging ductility of the steel due to excessive precipitation of Cr carbide in the course of high temperature use, so the upper limit is 24.0% by mass.
- Ni forms a stable austenite base, stabilizes the austenite phase, and increases the high temperature strength and oxidation resistance of the steel.
- the addition amount of Ni is set to 8.0 to 15.0 mass%.
- Nb combines with C to form fine carbides and improves high temperature strength. Moreover, oxidation resistance is improved by suppressing the production
- the austenitic stainless cast steel of the present invention can be produced by cooling from a temperature range of 1150 to 1350 ° C. to a temperature range of 600 to 800 ° C. at a cooling temperature of 30 ° C./min or more.
- the produced austenitic stainless cast steel is used, for example, as a material for piping and valves of chemical plants and power plants.
- the austenitic stainless cast steel of the present invention is configured so that the volume fraction of the ferrite phase is 0.1 to 5.0%, preferably 0.5 to 3.0%.
- the austenitic stainless cast steel of the present invention contains C, Si, Mn, Cr, Ni, Nb, N and the like as components.
- C is 0.01 to 0.10% by mass, preferably 0.02 to 0.04% by mass
- Si is 0.6 to 1.0% by mass, preferably 0.7 to 0.9% by mass
- Mn is 2.0 to 2.8% by mass, preferably 2.2 to 2.4% by mass
- N 0.1 to 0.4% by mass, preferably 0.15 to 0.25% by mass
- Cr 18.0 to 24.0% by mass, preferably 19.5 to 21.5% by mass
- Ni 8.0 to 15.0% by mass, preferably 10.5 to 12.5% by mass
- Nb 0.2 to 0.7% by mass, preferably 0.2 to 0.4% by mass.
- Table 1 shows the range of the composition (mass%) of the above components in the austenitic stainless cast steel of the present invention and, for reference, CF8C and CF8C-Plus.
- the austenitic stainless cast steel of the present invention by setting the volume fraction of the ferrite phase to 0.1 to 5.0%, the amount of sigma phase deposited can be reduced even when exposed to high temperatures for a long period of time. . Therefore, the austenitic stainless cast steel of the present invention is not easily embrittled and is excellent in aging ductility.
- the Mn content is set higher than that of CF8C, and the C content is set lower. Thereby, strength and oxidation resistance at high temperatures can be improved.
- the austenitic stainless cast steel of the present invention contains W, B, Al, Mo, Co, Ti, Zr, Cu, rare earth elements (La, Ce, Y, Pd, Nd, etc.) and the like in addition to the above-described composition.
- the balance is Fe and inevitable impurities.
- the above-mentioned metal component is melted in a melting furnace and cooled from a temperature range of 1150 to 1350 ° C. to a temperature range of 600 to 800 ° C. at a cooling temperature of 30 ° C./min or more, whereby the austenite system of the present invention.
- Stainless cast steel can be produced. By producing the austenitic stainless cast steel of the present invention under these conditions, the solution has excellent strength characteristics even when cast, so that the solution heat treatment can be omitted.
- the produced austenitic stainless cast steel is used, for example, in piping and valves of chemical plants and power plants.
- Example 1 Examples of the present invention will be described.
- the compositions (mass%) of the main components of the austenitic stainless cast steels of the present invention (Examples 1-1 to 1-6) and CF8C (Comparative Examples 1-1 to 1-5) are shown in Tables 2 and 3, respectively.
- aging ductility 700 ° C.-620 hours
- tensile strength 900 ° C.
- 0.2% proof stress 900 ° C.
- oxidation resistance 1000 ° C.
- high temperature low cycle fatigue The test (double oscillation triangle wave, strain rate 0.1% / second, 700 ° C., total strain 0.5%) was performed.
- casting was performed by a normal in-place casting method.
- Examples 1 and 2 were performed by as-cast (as cast), and other Examples and Comparative Examples were performed by SHT (Solution Solution Heat Treatment).
- Table 4 shows the results of examining the aging ductility, tensile strength, 0.2% proof stress, and oxidation resistance.
- the aging ductility was 20.4% or more in the example, whereas it was 17.2% or less in the comparative example.
- the tensile strength was 113 to 134 Mpa in the examples, and 93 to 127 Mpa in the comparative examples.
- the 0.2% proof stress was 87 to 91 Mpa in the examples and 70 to 84 Mpa in the comparative examples.
- the oxidation resistance was 0.489 mm / year or less in the example and 1.278 mm / year or more in the comparative example.
- the examples were superior in terms of aging ductility, tensile strength, and oxidation resistance.
- the average value of the example was 24.8%
- the average value of the comparative example was 10.4%
- the example was about 2.4 times that of the comparative example.
- oxidation resistance the average value of the example is 0.290 mm / year and the average value of the comparative example is 2.770 mm / year, and the example is improved to about 9.5 times the comparative example.
- Example 2 In Example 1, the volume fraction of the ferrite phase of the austenitic stainless cast steel of the present invention was 0.2% (Examples 1-1 to 1-6). Also in the case of 1 to 3%, aging ductility, tensile strength, 0.2% proof stress, and oxidation resistance were examined (Examples 2-1 to 2-4). These were performed under the same conditions as in Example 1. The components of Examples 2-1 to 2-4 are shown in Table 5, and the results are shown in Table 6.
- Example 1 the average value of aging ductility in Examples 2-1 to 2-4 was 24.6%, and the average value of oxidation resistance was 0.159 mm / year. These values were the same as in Example 1. It was recognized that it was superior to the comparative example. Even if the upper limit of the volume fraction of the ferrite phase of the austenitic stainless cast steel of the present invention is 5%, it is considered that the same result can be obtained.
- Example 3 The oxidation resistance (mm / year) of austenitic stainless cast steel having a Mn content of about 1.0 to 4.5% by mass was examined.
- the austenitic stainless cast steel of the present invention was examined for an embodiment in which the Mn content was 2.26 mass% (Example 3-1) and 2.33 mass% (Example 3-2).
- the austenitic stainless cast steel of the comparative example has a Mn content of 1.04% by mass (Comparative Example 3-1), 1.17% by mass (Comparative Example 3-2), and 1.81% by mass (Comparative Example 3- 3)
- An embodiment of 4.37% by mass (Comparative Example 3-4) and 4.48% by mass (Comparative Example 3-5) was examined.
- the respective components are shown in Table 7.
- the results are shown in Table 8 and FIG.
- FIG. 1 shows that in the austenitic stainless cast steel of the present invention, if the Mn content is 2.0 to 2.8% by mass, the oxidation resistance can be suppressed to 1 mm / year or less.
- the present invention can be used for the production of austenitic stainless cast steel.
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Abstract
Description
[1] フェライト相の体積率が0.1~5.0%であるオーステナイト系ステンレス鋳鋼。
[2] C:0.01~0.10質量%、Si:0.6~1.0質量%、Mn:2.0~2.8質量%、N:0.1~0.4質量%を含有する上記[1]に記載のオーステナイト系ステンレス鋳鋼。
[3] Cr:18.0~24.0質量%、Ni:8.0~15.0質量%、Nb:0.2~0.7質量%を含有する上記[1]または[2]に記載のオーステナイト系ステンレス鋳鋼。
[4] フェライト相の体積率が0.1~5.0%であり、
C:0.01~0.10質量%、Si:0.6~1.0質量%、Mn:2.0~2.8質量%、N:0.1~0.4質量%、Cr:18.0~24.0質量%、Ni:8.0~15.0質量%、Nb:0.2~0.7質量%、を含有し、
残部がFeおよび不可避不純物であるオーステナイト系ステンレス鋳鋼。
[5] 1150~1350℃の温度範囲から、30℃/分以上の冷却温度で、600~800℃の温度範囲まで冷却して得られた上記[1]~[4]の何れか一項に記載のオーステナイト系ステンレス鋳鋼。
[6] 上記[1]~[5]の何れか一項に記載のオーステナイト系ステンレス鋳鋼を用いて形成されたバルブ。
製造されたオーステナイト系ステンレス鋳鋼は、例えば、化学プラントや発電プラントの配管やバルブなどの材料として使用される。
本発明のオーステナイト系ステンレス鋳鋼は、フェライト相の体積率が0.1~5.0%、好ましくは0.5~3.0%となるように構成される。本発明のオーステナイト系ステンレス鋳鋼は、成分として、C、Si、Mn、Cr、Ni、Nb、Nなどを含有する。
Cは0.01~0.10質量%、好ましくは0.02~0.04質量%、
Siは0.6~1.0質量%、好ましくは0.7~0.9質量%、
Mnは2.0~2.8質量%、好ましくは2.2~2.4質量%、
N:0.1~0.4質量%、好ましくは0.15~0.25質量%、
Cr:18.0~24.0質量%、好ましくは19.5~21.5質量%、
Ni:8.0~15.0質量%、好ましくは10.5~12.5質量%、
Nb:0.2~0.7質量%、好ましくは0.2~0.4質量%、の含有量とする。
本発明のオーステナイト系ステンレス鋳鋼、および、参考としてCF8CおよびCF8C-Plusにおける上記成分の組成(質量%)の範囲を表1に示す。
また、本発明のオーステナイト系ステンレス鋳鋼では、Mnの含有量をCF8Cより高めており、Cの含有量を低めに設定している。これにより、高温での強度・耐酸化性を向上させることができる。
本発明の実施例について説明する。
本発明のオーステナイト系ステンレス鋳鋼(実施例1-1~1-6)、CF8C(比較例1-1~1-5の主成分の組成(質量%)をそれぞれ表2,3に示す。
引張強度については、実施例では113~134Mpaであり、比較例では93~127Mpaであった。
0.2%耐力については、実施例では87~91Mpaであり、比較例では70~84Mpaであった。
耐酸化性については、実施例では0.489mm/年 以下であり、比較例では1.278mm/年 以上であった。
上述した結果は、本発明のオーステナイト系ステンレス鋳鋼のフェライト相の体積率が0.2%である場合であるが、フェライト相の体積率の下限を0.1%とした場合であっても同様の結果が得られるものと考えられる。
実施例1では、本発明のオーステナイト系ステンレス鋳鋼のフェライト相の体積率は0.2%であった(実施例1-1~1-6)が、これに限らず、フェライトト相の体積率を1~3%とした場合についても時効延性、引張強度、0.2%耐力、耐酸化性を調べた(実施例2-1~2-4)。これらは実施例1と同様の条件で行なった。実施例2-1~2-4の各成分を表5に示し、結果を表6に示した。
Mnの含有量が約1.0~4.5質量%であるオーステナイト系ステンレス鋳鋼において、耐酸化性(mm/年)を調べた。本発明のオーステナイト系ステンレス鋳鋼は、Mnの含有量が2.26質量%(実施例3-1)、2.33質量%(実施例3-2)の態様について調べた。比較例のオーステナイト系ステンレス鋳鋼は、Mnの含有量が1.04質量%(比較例3-1)、1.17質量%(比較例3-2)、1.81質量%(比較例3-3)、4.37質量%(比較例3-4)、4.48質量%(比較例3-5)の態様について調べた。これら実施例および比較例において、それぞれの成分を表7に示した。結果を表8および図1に示した。
Claims (6)
- フェライト相の体積率が0.1~5.0%であるオーステナイト系ステンレス鋳鋼。
- C:0.01~0.10質量%、Si:0.6~1.0質量%、Mn:2.0~2.8質量%、N:0.1~0.4質量%を含有する請求項1に記載のオーステナイト系ステンレス鋳鋼。
- Cr:18.0~24.0質量%、Ni:8.0~15.0質量%、Nb:0.2~0.7質量%を含有する請求項1または2に記載のオーステナイト系ステンレス鋳鋼。
- フェライト相の体積率が0.1~5.0%であり、
C:0.01~0.10質量%、Si:0.6~1.0質量%、Mn:2.0~2.8質量%、N:0.1~0.4質量%、Cr:18.0~24.0質量%、Ni:8.0~15.0質量%、Nb:0.2~0.7質量%、を含有し、
残部がFeおよび不可避不純物であるオーステナイト系ステンレス鋳鋼。 - 1150~1350℃の温度範囲から、30℃/分以上の冷却温度で、600~800℃の温度範囲まで冷却して得られた請求項1~4の何れか一項に記載のオーステナイト系ステンレス鋳鋼。
- 請求項1~5の何れか一項に記載のオーステナイト系ステンレス鋳鋼を用いて形成されたバルブ。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
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CN201280013824.1A CN103429778B (zh) | 2011-03-31 | 2012-02-24 | 奥氏体不锈钢铸钢 |
EP12765111.5A EP2692887B1 (en) | 2011-03-31 | 2012-02-24 | Cast austenitic stainless steel |
CA2830586A CA2830586A1 (en) | 2011-03-31 | 2012-02-24 | Austenitic stainless cast steel |
JP2013507281A JP5863770B2 (ja) | 2011-03-31 | 2012-02-24 | オーステナイト系ステンレス鋳鋼 |
KR1020137028616A KR20140044318A (ko) | 2011-03-31 | 2012-02-24 | 오스테나이트계 스테인레스 주강 |
US14/007,578 US20140056751A1 (en) | 2011-03-31 | 2012-02-24 | Cast austenitic stainless steel |
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JP2011-079965 | 2011-03-31 | ||
JP2011079965 | 2011-03-31 |
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WO2012132679A1 true WO2012132679A1 (ja) | 2012-10-04 |
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US (1) | US20140056751A1 (ja) |
EP (1) | EP2692887B1 (ja) |
JP (1) | JP5863770B2 (ja) |
KR (1) | KR20140044318A (ja) |
CN (1) | CN103429778B (ja) |
CA (1) | CA2830586A1 (ja) |
WO (1) | WO2012132679A1 (ja) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10627168B2 (en) | 2016-03-28 | 2020-04-21 | Lg Electronics Inc. | Stainless steel and pipe made thereof |
JP6793866B1 (ja) * | 2020-06-17 | 2020-12-02 | 株式会社クボタ | ガス弁及びプロパンガスの流量制御方法 |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
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KR102030162B1 (ko) | 2016-12-23 | 2019-11-08 | 주식회사 포스코 | 가공성 및 표면특성이 우수한 오스테나이트계 스테인리스강 및 이의 제조방법 |
WO2018117683A1 (ko) * | 2016-12-23 | 2018-06-28 | 주식회사 포스코 | 가공성 및 표면특성이 우수한 오스테나이트계 스테인리스강 및 이의 제조방법 |
CN109454220A (zh) * | 2018-11-24 | 2019-03-12 | 共享铸钢有限公司 | 一种奥氏体不锈钢材料铸钢件的生产方法 |
CN110093561B (zh) * | 2019-05-13 | 2021-06-18 | 襄阳市立强机械有限公司 | 一种铸态无磁奥氏体不锈钢及其制备方法 |
CN113699453B (zh) * | 2021-08-30 | 2023-03-10 | 上海海塔机械制造有限公司 | 一种耐热型高氮钢及其生产方法 |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5487627A (en) * | 1977-12-23 | 1979-07-12 | Kubota Ltd | Stainless steel for extreme low temperature excellent in weld ability |
JPS5547370A (en) * | 1978-09-30 | 1980-04-03 | Kubota Ltd | Stainless cast steel for cryogenic temperature use |
JPS6353244A (ja) * | 1986-08-25 | 1988-03-07 | Aichi Steel Works Ltd | 強度、耐食性に優れ、かつ異方性が小さいステンレス鋼およびその製造方法 |
JPS63169362A (ja) * | 1986-12-29 | 1988-07-13 | Aichi Steel Works Ltd | 非磁性工具鋼 |
JPH05311337A (ja) * | 1992-05-08 | 1993-11-22 | Nippon Yakin Kogyo Co Ltd | 高延性オーステナイト−フェライト2相耐熱鋼およびその製造方法 |
JPH06336653A (ja) * | 1993-05-27 | 1994-12-06 | Agency Of Ind Science & Technol | 原子力発電所海水ポンプ用ステンレス鋳鋼及びステンレス鋳鋼品の製造方法 |
JPH0931601A (ja) * | 1995-07-25 | 1997-02-04 | Hitachi Ltd | 耐海水腐食性オーステナイト系ステンレス鋳鋼及び海水用ポンプ |
JP2009545675A (ja) | 2006-07-31 | 2009-12-24 | キャタピラー インコーポレイテッド | 高温強度が改善された耐熱および耐食性オーステナイト系ステンレス鋼鋳鋼合金 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5218418A (en) * | 1975-08-02 | 1977-02-12 | Jgc Corp | Stainless cast steel for low temperature use |
JPS60121098A (ja) * | 1983-12-05 | 1985-06-28 | Kawasaki Steel Corp | オ−ステナイト系ステンレス鋼肉盛溶接における水素はくり割れ防止方法 |
JPH0297648A (ja) * | 1988-09-30 | 1990-04-10 | Aichi Steel Works Ltd | クリープ破断強度の優れたオーステナイト系ステンレス鋼およびその製造方法 |
JPH0297647A (ja) * | 1988-09-30 | 1990-04-10 | Aichi Steel Works Ltd | ねじり強度の優れたバルブステム用鋼およびその製造方法 |
JP2574917B2 (ja) * | 1990-03-14 | 1997-01-22 | 株式会社日立製作所 | 耐応力腐食割れ性に優れたオーステナイト鋼及びその用途 |
JP3954954B2 (ja) * | 2002-10-25 | 2007-08-08 | 新日本製鐵株式会社 | オーステナイト系ステンレス鋼及び薄帯鋳片の製造法 |
CA2528743C (en) * | 2003-06-10 | 2010-11-23 | Sumitomo Metal Industries, Ltd. | Austenitic stainless steel for hydrogen gas and a method for its manufacture |
DK1637785T3 (da) * | 2004-09-15 | 2010-08-16 | Sumitomo Metal Ind | Stålrør med fremragende eksfolieringsmodstandsdygtighed mod afskalning på den indvendige overflade |
EP2245202B1 (en) * | 2007-12-20 | 2011-08-31 | ATI Properties, Inc. | Austenitic stainless steel low in nickel containing stabilizing elements |
CN101845605B (zh) * | 2009-03-24 | 2013-01-02 | 宝山钢铁股份有限公司 | 一种中低温强度优异的奥氏体不锈钢板及其制造方法 |
-
2012
- 2012-02-24 CA CA2830586A patent/CA2830586A1/en not_active Abandoned
- 2012-02-24 KR KR1020137028616A patent/KR20140044318A/ko not_active Application Discontinuation
- 2012-02-24 US US14/007,578 patent/US20140056751A1/en not_active Abandoned
- 2012-02-24 EP EP12765111.5A patent/EP2692887B1/en not_active Not-in-force
- 2012-02-24 CN CN201280013824.1A patent/CN103429778B/zh not_active Expired - Fee Related
- 2012-02-24 JP JP2013507281A patent/JP5863770B2/ja active Active
- 2012-02-24 WO PCT/JP2012/054523 patent/WO2012132679A1/ja active Application Filing
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5487627A (en) * | 1977-12-23 | 1979-07-12 | Kubota Ltd | Stainless steel for extreme low temperature excellent in weld ability |
JPS5547370A (en) * | 1978-09-30 | 1980-04-03 | Kubota Ltd | Stainless cast steel for cryogenic temperature use |
JPS6353244A (ja) * | 1986-08-25 | 1988-03-07 | Aichi Steel Works Ltd | 強度、耐食性に優れ、かつ異方性が小さいステンレス鋼およびその製造方法 |
JPS63169362A (ja) * | 1986-12-29 | 1988-07-13 | Aichi Steel Works Ltd | 非磁性工具鋼 |
JPH05311337A (ja) * | 1992-05-08 | 1993-11-22 | Nippon Yakin Kogyo Co Ltd | 高延性オーステナイト−フェライト2相耐熱鋼およびその製造方法 |
JPH06336653A (ja) * | 1993-05-27 | 1994-12-06 | Agency Of Ind Science & Technol | 原子力発電所海水ポンプ用ステンレス鋳鋼及びステンレス鋳鋼品の製造方法 |
JPH0931601A (ja) * | 1995-07-25 | 1997-02-04 | Hitachi Ltd | 耐海水腐食性オーステナイト系ステンレス鋳鋼及び海水用ポンプ |
JP2009545675A (ja) | 2006-07-31 | 2009-12-24 | キャタピラー インコーポレイテッド | 高温強度が改善された耐熱および耐食性オーステナイト系ステンレス鋼鋳鋼合金 |
Non-Patent Citations (1)
Title |
---|
See also references of EP2692887A4 |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10627168B2 (en) | 2016-03-28 | 2020-04-21 | Lg Electronics Inc. | Stainless steel and pipe made thereof |
JP6793866B1 (ja) * | 2020-06-17 | 2020-12-02 | 株式会社クボタ | ガス弁及びプロパンガスの流量制御方法 |
WO2021256002A1 (ja) * | 2020-06-17 | 2021-12-23 | 株式会社クボタ | ガス弁及びプロパンガスの流量制御方法 |
US11686395B2 (en) | 2020-06-17 | 2023-06-27 | Kubota Corporation | Gas valve and flow rate control method for propane gas |
Also Published As
Publication number | Publication date |
---|---|
CN103429778B (zh) | 2016-01-06 |
CN103429778A (zh) | 2013-12-04 |
EP2692887A1 (en) | 2014-02-05 |
CA2830586A1 (en) | 2012-10-04 |
EP2692887B1 (en) | 2017-07-19 |
EP2692887A4 (en) | 2015-01-21 |
JPWO2012132679A1 (ja) | 2014-07-24 |
KR20140044318A (ko) | 2014-04-14 |
US20140056751A1 (en) | 2014-02-27 |
JP5863770B2 (ja) | 2016-02-17 |
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