WO2004061143A1 - オーステナイト系ステンレス鋼 - Google Patents
オーステナイト系ステンレス鋼 Download PDFInfo
- Publication number
- WO2004061143A1 WO2004061143A1 PCT/JP2003/015907 JP0315907W WO2004061143A1 WO 2004061143 A1 WO2004061143 A1 WO 2004061143A1 JP 0315907 W JP0315907 W JP 0315907W WO 2004061143 A1 WO2004061143 A1 WO 2004061143A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel
- stainless steel
- austenitic stainless
- heating
- Prior art date
Links
Classifications
-
- 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
- C22C38/001—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- 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
Definitions
- the present invention relates to an austenitic stainless steel, and more particularly, to a shape change by heating and cooling after cold working, which is suitable for structural members of automobiles.
- Austenitic stainless copper is used for various structural members because of its excellent workability, strength and corrosion resistance. And, in many cases, it is used after cold working.
- Japanese Patent Application Laid-Open No. 8-283915 discloses an austenitic stainless steel in which the formation of a work-induced martensite is suppressed by adjusting the chemical composition, and the work hardening is suppressed by controlling the crystal grain size to improve workability.
- the invention of steel has been disclosed. However, in the present invention, no consideration is given to the shape change due to the heating and cooling treatment after the cold working.
- austenitic stainless steel undergoes a shape change when it is annealed at a relatively low temperature after cold working.
- indices such as stacking fault energy and martensite transformation, are organized as indices of this shape change.
- Japanese Patent Application Laid-Open No. 2001-323341 discloses that a high strength is obtained by performing shape correction using a work-induced martensite by cold working and shrinkage due to a reverse transformation from a martensite phase to an austenite phase during low-temperature annealing.
- a stainless steel sheet with improved flatness is disclosed.
- a first object of the present invention is to provide a high-Si austenitic stainless steel that has a small change in shape due to heating and cooling after cold working.
- a second object of the present invention is to provide a high-Si austenitic stainless steel which has a small change in shape due to heating and cooling after cold working and has excellent weldability.
- the austenitic stainless steel of the present invention is particularly suitable as a structural member of an automobile.
- the gist of the present invention resides in the following austenitic stainless steels 1 and 2.
- Mass 0 /. C 0.03% or less, Si: 2 to 4%, Mn: 0.1 to 2%, P: 0.03% or less, S: 0.03% or less, Ni: 9 to 15%, Cr: 15 to 20%, N: 0.02 to 0.2%, Nb: 0.03% or less, one or two of Mo and Cu in total: 0.2 to 4%, the balance being Fe and impurities, and the following formulas (1), (2) and And austenitic stainless steel that satisfies equation (3).
- the present invention has been completed based on the following findings. .
- the martensite transformation in ( ⁇ ) is more likely to occur as the value of Md30 increases.
- the shrinkage in (B) is organized using stacking fault energy (SFE) as an index.
- SFE stacking fault energy
- the above Md30 is the temperature (° C) at which 50% by volume of martensite transformation occurs when 0.3% of true tensile strain is applied.
- Nb is usually added to fix C in steel in the grains to improve corrosion resistance.
- the stacking fault energy is significantly reduced and shrinkage is promoted.
- Equations (1) and (2) are equations found based on basic experiments and their complementary experiments.
- the composition in order to prevent high-temperature cracking during welding and to have good weldability, it is desirable that the composition be such that a ⁇ -ferrite is formed in the welded area and has a mild composition. That is, it is preferable that the composition be relatively high in Cr and low in M.
- the composition when the composition is such that ⁇ -frite easily forms in the weld, the shape change due to heating and cooling after cold working tends to increase. Therefore, in order to achieve both weldability and small shape change, it is necessary to balance chemical components.
- the present inventors have pursued a composition in which there is little change in shape due to heating and cooling treatment after cold working, and ⁇ -ferrite is easily formed in a welded portion.
- expression (3) it has been found that if the following expression (3) is satisfied in addition to the above expressions (1) and (2), both weldability and small shape change can be achieved. If Eqs. (1) and (2) are satisfied but Eq. (3) is not satisfied, the change in shape due to heating and cooling after cold working is small, but the weldability is significantly reduced.
- FIG. 1 is a diagram showing an examination test mode of shape change.
- FIG. 2 is a view showing a test piece after plastic deformation by the test.
- C stabilizes the austenite phase and suppresses the work-induced martensite transformation. On the other hand, it lowers stacking fault energy.
- C is an element that reduces the corrosion resistance when precipitated as Cr carbide in the weld.
- Nb has an effect of promoting shape change by heating and cooling after cold working, it is desirable that the Nb content is small. Therefore, the C content should be reduced, and its content was set to 0.03% or less. A preferred upper limit is 0.025%. The content of Nb will be described later.
- Si acts as a steel deoxidizer. It is also an effective element for improving the oxidation resistance of steel. To achieve these effects sufficiently, a content of 2% or more is required. On the other hand, if it exceeds 4%, the formability and the weldability decrease. Therefore, the Si content was set to 2 to 4%.
- the lower limit is preferably 2.5%, more preferably 3.0%.
- a good upper limit is 3.8%.
- Mn stabilizes the austenitic phase by heating and cooling after cold working. Shape change. Mn is also an effective element for improving hot workability. To achieve these effects sufficiently, a content of 0.1% or more is required. On the other hand, if it exceeds 2%, sulfides (MnS) are formed and become non-metallic inclusions in the steel, adversely affecting corrosion resistance and mechanical properties. Therefore, the Mn content was set to 0.1 to 2 ° / 0 .
- the lower limit is preferably 0.2%, and more preferably 0.4 ° / 0 . Further, the upper limit is preferably 1.5%, and more preferably 1.0%.
- P is an impurity. Since it lowers the corrosion resistance of stainless steel, it is better to be as small as possible, but there is no particular problem up to 0.03%, so it was set to 0.03% or less.
- S is also an impurity like P described above.
- S forms sulfides, which are nonmetallic inclusions, and adversely affects corrosion resistance and mechanical properties. In addition, it concentrates preferentially on the surface of the welded part and reduces the corrosion resistance of the welded part. Therefore, S should be as small as possible, but there is no particular problem up to 0.03%, so S is set to 0.03% or less. Preferred is 0.02 ° / 0 or less, more preferred is 0.01% or less.
- Ni stabilizes the austenite phase and suppresses the shape change due to heating and cooling after cold working. Also, is an important element for maintaining the corrosion resistance of stainless steel, and a content of 9% or more is required to ensure sufficient corrosion resistance. On the other hand, if M is contained excessively, it becomes difficult to generate ⁇ -ferrite in the welded portion, and hot cracking tends to occur during welding. Furthermore, as can be seen from the above formulas (1), (2) and (3), the upper limit of the ⁇ content needs to be determined in relation to the Cr content. The upper limit of the Ni content was 15%. Preferred as lower limit 10% is more preferable, and 10.5% is more preferable. The upper limit is preferably 13.0%, and more preferably 12.5%.
- the Cr content was set to 15 to 20 ° / 0 .
- the lower limit is preferably 15.5%, and more preferably 16%.
- the upper limit is preferably 18.0%, and more preferably 17.5%.
- N is an element that stabilizes the austenite phase, and has the effect of suppressing shape change due to heating and cooling after cold working. In addition, it has the effect of increasing the strength of the steel. To achieve these effects, a content of 0.02% or more is required. On the other hand, excessive N reduces the workability of steel, so the upper limit is set to 0.2%.
- the lower limit is preferably 0.025%, and more preferably 0.03%. Further, the upper limit is preferably 0.15%, and more preferably 0.1%.
- Nb is usually added positively because it has the effect of fixing C in steel within grains and improving corrosion resistance.
- b significantly changes shape due to heating and cooling after cold working in high Si steels such as the present invention.
- b suppresses the formation of ⁇ -ferrite during welding and lowers weldability. Therefore, it is desirable that b be as small as possible.
- the allowable upper limit as an impurity is set to 0.03 ° / 0 or less. Preferred is 0.02% or less, and more preferred is 0.01% or less.
- Mo and Cu are elements that stabilize the austenitic phase and are cold worked The effect of suppressing a change in shape during subsequent heating and cooling is great.
- Nb is usually added positively because it has the effect of fixing C in steel within grains and improving corrosion resistance.
- Nb significantly changes the shape of a high-Si steel such as the present invention due to heating and cooling after cold working.
- Nb suppresses the formation of ⁇ -ferrite during welding and reduces weldability. Therefore, it is desirable that Nb be as small as possible.
- the allowable upper limit as an impurity is set to 0.03 ° / 0 or less. Preferred is 0.02 ° / 0 or less, and more preferred is 0.01% or less.
- each of the remaining steel sheets was subjected to an annealing treatment at 1100 ° C for 15 minutes, and then cold rolling and annealing at 1100 ° C for 15 minutes were repeated to form a 0.3mm-thick cold-rolled steel sheet.
- each steel sheet was subjected to final annealing at 1100 ° C for 15 minutes to finish it as a cold-rolled annealed steel sheet, and a test specimen 30 mm wide and 100 mm long was collected from each obtained cold-rolled annealed steel sheet, After wet polishing with No. 600 emery paper, it was subjected to the shape change test shown in Fig.1.
- the Transvalestrain test shows the current under the load strain of 3.72%. Perform TIG welding at 100A, voltage 14V, welding speed 15cm / min.Measure the maximum crack length after welding.If the maximum crack length is less than 0.5mm, the weldability is good, if it is 0.5mm or more Was evaluated as having poor weldability. The “ ⁇ ” mark shown in Table 1 is good, and the “X” mark is bad.
- the steels of Nos. 1 to 7 of the present invention have a small change in shape during heating and cooling after cold working.
- Steels No. 1 to No. 5 also have excellent weldability.
- the steels of Nos. 8 to 13 of the comparative examples have large shape changes or poor weldability.
- the cause is that either component is out of the range specified in the present invention, or the content of each component is in the range specified in the present invention, but the formulas (1) and (2) ⁇ ⁇ ⁇ One or more of equation (3) is not satisfied.
- the steel of No. 14 had too high a content of Mo and Cu and had poor hot workability, and could not be used for the evaluation test. table 1
- the austenitic stainless steel of the present invention is particularly suitable as a structural member of an automobile, because the shape change due to heating and cooling after cold working is small.
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CA002509638A CA2509638C (en) | 2002-12-12 | 2003-12-11 | Austenitic stainless steel |
AU2003289043A AU2003289043A1 (en) | 2002-12-12 | 2003-12-11 | Austenitic stainless steel |
US11/143,610 US7101446B2 (en) | 2002-12-12 | 2005-06-03 | Austenitic stainless steel |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002360728A JP4221569B2 (ja) | 2002-12-12 | 2002-12-12 | オーステナイト系ステンレス鋼 |
JP2002-360728 | 2002-12-12 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US11/143,610 Continuation-In-Part US7101446B2 (en) | 2002-12-12 | 2005-06-03 | Austenitic stainless steel |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2004061143A1 true WO2004061143A1 (ja) | 2004-07-22 |
Family
ID=32708094
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2003/015907 WO2004061143A1 (ja) | 2002-12-12 | 2003-12-11 | オーステナイト系ステンレス鋼 |
Country Status (5)
Country | Link |
---|---|
US (1) | US7101446B2 (ja) |
JP (1) | JP4221569B2 (ja) |
AU (1) | AU2003289043A1 (ja) |
CA (1) | CA2509638C (ja) |
WO (1) | WO2004061143A1 (ja) |
Families Citing this family (26)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8637127B2 (en) | 2005-06-27 | 2014-01-28 | Kennametal Inc. | Composite article with coolant channels and tool fabrication method |
US7687156B2 (en) | 2005-08-18 | 2010-03-30 | Tdy Industries, Inc. | Composite cutting inserts and methods of making the same |
EP2327856B1 (en) | 2006-04-27 | 2016-06-08 | Kennametal Inc. | Modular fixed cutter earth-boring bits, modular fixed cutter earth-boring bit bodies, and related methods |
EP2078101A2 (en) | 2006-10-25 | 2009-07-15 | TDY Industries, Inc. | Articles having improved resistance to thermal cracking |
US8512882B2 (en) | 2007-02-19 | 2013-08-20 | TDY Industries, LLC | Carbide cutting insert |
US7846551B2 (en) | 2007-03-16 | 2010-12-07 | Tdy Industries, Inc. | Composite articles |
JP5395805B2 (ja) | 2007-11-29 | 2014-01-22 | エイティーアイ・プロパティーズ・インコーポレーテッド | オーステナイト系のリーンステンレス鋼 |
US8877121B2 (en) | 2007-12-20 | 2014-11-04 | Ati Properties, Inc. | Corrosion resistant lean austenitic stainless steel |
US8337749B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel |
ES2394980T3 (es) | 2007-12-20 | 2013-02-07 | Ati Properties, Inc. | Acero inoxidable austenítico bajo en níquel conteniendo elementos estabilizantes |
US8790439B2 (en) | 2008-06-02 | 2014-07-29 | Kennametal Inc. | Composite sintered powder metal articles |
CA2725318A1 (en) | 2008-06-02 | 2009-12-10 | Tdy Industries, Inc. | Cemented carbide-metallic alloy composites |
US8025112B2 (en) | 2008-08-22 | 2011-09-27 | Tdy Industries, Inc. | Earth-boring bits and other parts including cemented carbide |
US8322465B2 (en) | 2008-08-22 | 2012-12-04 | TDY Industries, LLC | Earth-boring bit parts including hybrid cemented carbides and methods of making the same |
US8272816B2 (en) | 2009-05-12 | 2012-09-25 | TDY Industries, LLC | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
US8308096B2 (en) | 2009-07-14 | 2012-11-13 | TDY Industries, LLC | Reinforced roll and method of making same |
US8440314B2 (en) | 2009-08-25 | 2013-05-14 | TDY Industries, LLC | Coated cutting tools having a platinum group metal concentration gradient and related processes |
US9643236B2 (en) | 2009-11-11 | 2017-05-09 | Landis Solutions Llc | Thread rolling die and method of making same |
CN103826766B (zh) * | 2011-07-29 | 2015-11-25 | 新日铁住金株式会社 | 奥氏体系不锈钢的制造方法 |
US8800848B2 (en) | 2011-08-31 | 2014-08-12 | Kennametal Inc. | Methods of forming wear resistant layers on metallic surfaces |
US9016406B2 (en) | 2011-09-22 | 2015-04-28 | Kennametal Inc. | Cutting inserts for earth-boring bits |
FI124993B (fi) * | 2012-09-27 | 2015-04-15 | Outokumpu Oy | Austeniittinen ruostumaton teräs |
SG11201701799RA (en) * | 2014-09-17 | 2017-04-27 | Nippon Steel & Sumitomo Metal Corp | Austenitic stainless steel sheet |
US20160144461A1 (en) * | 2014-11-21 | 2016-05-26 | Huntington Alloys Corporation | Ni-Cr-Mo-Ta-Nb Welding Filler Metals, Welding Filler Metal Consumables, Weld Deposits, Methods of Making Weld Deposits, and Weldments Thereof |
KR102120700B1 (ko) | 2018-09-13 | 2020-06-09 | 주식회사 포스코 | 확관가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 |
AU2021259899B2 (en) * | 2020-04-20 | 2023-06-29 | Nippon Steel Stainless Steel Corporation | Austenitic stainless steel and spring |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11350085A (ja) * | 1998-06-11 | 1999-12-21 | Nippon Steel Corp | 耐食鋼 |
JP2001164341A (ja) * | 1999-12-10 | 2001-06-19 | Nippon Steel Corp | 加工部耐食性に優れた鋼 |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH08283915A (ja) | 1995-04-12 | 1996-10-29 | Nkk Corp | 加工性に優れたオーステナイトステンレス鋼 |
KR20010002733A (ko) * | 1999-06-17 | 2001-01-15 | 이구택 | 광택성이 향상되는 오스테나이트 스테인레스 냉연강판의광휘소둔방법 |
JP4479053B2 (ja) | 2000-05-15 | 2010-06-09 | 住友金属工業株式会社 | 高強度かつ平坦性に優れたステンレス鋼板とその製造方法 |
KR100480354B1 (ko) * | 2000-12-13 | 2005-04-06 | 주식회사 포스코 | 내산화성이 향상되는 오스테나이트계 스테인레스 광휘소둔냉연강판의 제조방법 |
JP2002194506A (ja) * | 2000-12-25 | 2002-07-10 | Sumitomo Metal Ind Ltd | ステンレス鋼板およびその製造方法 |
-
2002
- 2002-12-12 JP JP2002360728A patent/JP4221569B2/ja not_active Expired - Fee Related
-
2003
- 2003-12-11 CA CA002509638A patent/CA2509638C/en not_active Expired - Fee Related
- 2003-12-11 AU AU2003289043A patent/AU2003289043A1/en not_active Abandoned
- 2003-12-11 WO PCT/JP2003/015907 patent/WO2004061143A1/ja active Application Filing
-
2005
- 2005-06-03 US US11/143,610 patent/US7101446B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11350085A (ja) * | 1998-06-11 | 1999-12-21 | Nippon Steel Corp | 耐食鋼 |
JP2001164341A (ja) * | 1999-12-10 | 2001-06-19 | Nippon Steel Corp | 加工部耐食性に優れた鋼 |
Also Published As
Publication number | Publication date |
---|---|
US7101446B2 (en) | 2006-09-05 |
JP4221569B2 (ja) | 2009-02-12 |
US20050232805A1 (en) | 2005-10-20 |
CA2509638A1 (en) | 2004-07-22 |
CA2509638C (en) | 2008-04-22 |
JP2004190103A (ja) | 2004-07-08 |
AU2003289043A1 (en) | 2004-07-29 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2004061143A1 (ja) | オーステナイト系ステンレス鋼 | |
TWI399443B (zh) | Heat-resistant fat iron-based stainless steel | |
JP6223351B2 (ja) | フェライト系ステンレス鋼、それを用いた排気系部材及びフェライト系ステンレス鋼の製造方法 | |
KR101614236B1 (ko) | 페라이트계 스테인리스 강판 | |
KR101463525B1 (ko) | 인성이 우수한 고내식성 페라이트계 스테인레스 냉연 강판 및 그 제조 방법 | |
KR19990007429A (ko) | 매우 낮은 니켈 함량 및 높은 인장 연신율을 갖는 오오스테노페라이트 스테인레스 강 | |
KR101463526B1 (ko) | 인성이 우수한 고내식성 페라이트계 스테인레스 열연 강판 | |
TW200946694A (en) | Ferritic stainless steel with excellent heat resistance and toughness | |
JP2009235555A (ja) | 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板 | |
KR101581886B1 (ko) | 내열성과 가공성이 우수한 페라이트계 스테인리스강 | |
WO2012036313A1 (ja) | 耐酸化性に優れた耐熱フェライト系ステンレス鋼板 | |
JP4185425B2 (ja) | 成形性と高温強度・耐高温酸化性・低温靱性とを同時改善したフェライト系鋼板 | |
JP5677819B2 (ja) | 耐酸化性に優れたフェライト系ステンレス鋼板 | |
EP3126537B1 (en) | Dual-phase stainless steel | |
JP4327030B2 (ja) | 張出し性と耐発銹性に優れた低Niオ−ステナイト系ステンレス鋼 | |
JP6025362B2 (ja) | 耐熱性に優れたフェライト系ステンレス鋼板 | |
KR20130034025A (ko) | 용접부 내식성이 우수한 구조용 스테인레스 강판 및 그의 제조 방법 | |
JP4457492B2 (ja) | 加工性と溶接性に優れたステンレス鋼 | |
US7429302B2 (en) | Stainless steel sheet for welded structural components and method for making the same | |
JP2002030346A (ja) | 成形性に優れたCr含有耐熱耐食鋼板の製造方法 | |
JP3858647B2 (ja) | 低温継手靱性と耐ssc性に優れた高張力鋼とその製造方法 | |
JP3744403B2 (ja) | 軟質なCr含有鋼 | |
JP2002105601A (ja) | 高強度複相ステンレス鋼及びその製造方法 | |
JPH08239737A (ja) | 熱間加工性および耐σ脆化性に優れた耐熱用オーステナイト系ステンレス鋼 | |
JP6262893B1 (ja) | フェライト系ステンレス鋼および溶接構造物 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AK | Designated states |
Kind code of ref document: A1 Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BW BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE EG ES FI GB GD GE GH GM HR HU ID IL IN IS KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NI NO NZ OM PG PH PL PT RO RU SC SD SE SG SK SL SY TJ TM TN TR TT TZ UA UG US UZ VC VN YU ZA ZM ZW |
|
AL | Designated countries for regional patents |
Kind code of ref document: A1 Designated state(s): BW GH GM KE LS MW MZ SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LU MC NL PT RO SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: 11143610 Country of ref document: US |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2509638 Country of ref document: CA |
|
122 | Ep: pct application non-entry in european phase |