EP3284836B1 - Zirconium alloy having excellent corrosion resistance and creep resistance, and method for manufacturing same - Google Patents
Zirconium alloy having excellent corrosion resistance and creep resistance, and method for manufacturing same Download PDFInfo
- Publication number
- EP3284836B1 EP3284836B1 EP15889277.8A EP15889277A EP3284836B1 EP 3284836 B1 EP3284836 B1 EP 3284836B1 EP 15889277 A EP15889277 A EP 15889277A EP 3284836 B1 EP3284836 B1 EP 3284836B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- zirconium alloy
- rolled
- added
- corrosion resistance
- subjecting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C16/00—Alloys based on zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/186—High-melting or refractory metals or alloys based thereon of zirconium or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
Definitions
- the present invention relates to a zirconium alloy having excellent corrosion resistance and creep resistance and a method of manufacturing the same and, more particularly, to a zirconium alloy composition and annealing conditions, suitable for use in nuclear fuel cladding tubes and spacer grids for light and heavy water reactor nuclear power plants.
- Zirconium alloys having a low neutron absorption cross-section, superior corrosion resistance and mechanical properties, have been widely used for decades as materials for nuclear fuel cladding tubes, nuclear fuel assembly spaer grids, and internal structures in nuclear reactors.
- Zircaloy-2 (Sn: 1.20 to 1.70 wt%, Fe: 0.07 to 0.20 wt%, Cr: 0.05 to 1.15 wt%, Ni: 0.03 to 0.08 wt%, O: 900 to 1500 ppm, Zr: balance) and Zircaloy-4 (Sn: 1.20 to 1.70 wt%, Fe: 0.18 to 0.24 wt%, Cr: 0.07 to 1.13 wt%, O: 900 to 1500 ppm, Ni: ⁇ 0.007 wt%, Zr: balance) are widely used in nuclear industry.
- U.S. Patent No. 4,649,023 discloses a zirconium alloy composed essentially of 0.5 to 2.0 wt% of Nb and 0.9 to 1.5 wt% of Sn, and including 0.09 to 0.11 wt% of any one selected from among Fe, Cr, Mo, V, Cu, Ni and W, and 0.1 to 0.16 wt% of O, and the balance of Zr. Also, there is disclosed a method of manufacturing a product in which precipitates having a small size of 80 nm or less are uniformly distributed in a matrix using the above alloy.
- U.S. Patent No. 5,648,995 discloses a cladding tube using a zirconium alloy comprising 0.8 to 1.3 wt% of Nb, 50 to 250 ppm of Fe, 1600 ppm or less of O, and 120 ppm or less of Si.
- This alloy is annealed at 600 to 800°C, extruded, and subjected to cold rolling four to five times.
- intermediate annealing between the cold rolling processes is performed in the temperature range of 565 to 605°C for 2 to 4 hr, and final annealing is performed at 580°C, thereby manufacturing a nuclear fuel cladding tube.
- the alloy composition is configured such that the amounts of Fe and O are limited to 250 ppm or less and 1000 to 1600 ppm, respectively.
- U.S. Patent No. 6,325,966 discloses an alloy having superior corrosion resistance and mechanical properties, composed essentially of 0.15 to 0.25 wt% of Nb, 1.10 to 1.40 wt% of Sn, 0.35 to 0.45 wt% of Fe, and 0.15 to 0.25 wt% of Cr, and including 0.08 to 0.12 wt% of any one selected from among Mo, Cu, and Mn, 1000 to 1400 ppm of O, and the balance of Zr.
- an Zr-Nb alloy from which Sn is removed and to which P, Ta and the like are added, and which is controlled in terms of composition and annealing temperatures, may improve creep resistance while significantly increasing corrosion resistance, thus culminating in the present invention.
- US 2012/145287 A1 discloses a Zr alloy which exhibits excellent corrosion resistance by varying the kinds of metal oxides and controlling the size of precipitates of the composition, including: 1.05-1.45 wt % of Nb; one or more selected from the group consisting of 0.1-0.7 wt % of Fe and 0.05-0.6 wt % of Cr; and residual Zr.
- KR 2012/0126205 A discloses a Zr alloy with excellent mechanical property and corrosion resistance for a nuclear fuel cladding tube.
- an object of the present invention is to provide a zirconium alloy composition and final annealing conditions, in which Sn, which negatively affects corrosion resistance, is removed and Nb, P, Ta and the like are added to maintain creep resistance, thus ensuring optimal annealing conditions while improving corrosion resistance and creep resistance.
- the present invention provides a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.01 to 0.2 wt% of P, 0.2 to 0.3 wt% of Fe, optionally 0.01 to 0.15 wt% of Ta, and the balance of Zr.
- P is added in an amount of 0.02 to 0.07 wt%.
- the zirconium alloy also comprises 0.01 to 0.15 wt% of Ta in order to improve corrosion resistance and creep resistance.
- Ta is added in an amount of 0.03 to 0.1 wt%.
- the present invention provides a method of manufacturing a zirconium alloy, comprising the steps of: (1) melting a mixture comprising 1.1 to 1.2 wt% of Nb, 0.01 to 0.2 wt% of P, 0.2 to 0.3 wt% of Fe, optionally 0.01 to 0.15 wt% of Ta, and the balance of Zr, thus preparing an ingot; (2) subjecting the ingot prepared in step (1) to solution heat treatment at 1,000 to 1,050°C ( ⁇ -phase range) for 30 to 40 min and then to ⁇ -quenching using water; (3) preheating the ingot treated in step (2) at 630 to 650°C for 20 to 30 min and subjecting the ingot to hot rolling at a reduction ratio of 60 to 65%; (4) subjecting the material hot -rolled in step (3), to primary intermediate vacuum annealing at 570 to 590°C for 3 to 4 hr and then to primarily cold-rolled at a reduction ratio of 30 to 40%; (5) subjecting the material primarily cold-rolled in step
- step (1) P is added in an amount of 0.02 to 0.07 wt%, and in step (7), the final vacuum annealing temperature is 460 to 600°C, thereby optimizing corrosion resistance and creep resistance.
- the mixture also comprises 0.01 to 0.15 wt% of Ta, thereby further increasing corrosion resistance.
- Ta is added in an amount of 0.03 to 0.1 wt%, and in step (7), the final vacuum annealing temperature is 460 to 530°C, thereby maximizing corrosion resistance and creep resistance.
- P is compacted in order to prevent precipitation thereof before melting the mixture in step (1).
- the zirconium alloy is configured such that Sn is completely removed and the kinds and amounts of added elements and final annealing conditions are controlled, thus exhibiting corrosion resistance superior to that of Zircaloy-4 and high creep resistance. Therefore, this zirconium alloy can be effectively utilized in nuclear fuel cladding tubes and the like inside reactor cores for light and heavy water reactor nuclear power plants.
- the present invention addresses a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.02 to 0.05 wt% of P, 0.2 to 0.3 wt% of Fe, optionally 0.01 to 0.15 wt% of Ta, and the balance of Zr.
- the present invention addresses a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.02 wt% of P, 0.2 to 0.3 wt% of Fe, and the balance of Zr.
- the present invention addresses a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.05 wt% of P, 0.2 to 0.3 wt% of Fe, and the balance of Zr.
- the present invention addresses a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.05 wt% of P, 0.03 to 0.04 wt% of Ta, 0.2 to 0.3 wt% of Fe, and the balance of Zr.
- the present invention addresses a zirconium alloy, comprising: 1.1 to 1.2 wt% of Nb, 0.05 wt% of P, 0.09 to 0.1 wt% of Ta, 0.2 to 0.3 wt% of Fe, and the balance of Zr.
- the present invention also addresses the method of manufacturing the zirconium alloy as outlined in claim 5.
- step (1) 1.2 wt% of Nb, 0.02 to 0.05 wt% of P, 0.03 to 0.1 wt% of Ta, 0.2 wt% of Fe, and the balance of Zr were subjected to VAR (Vacuum Arc Remelting), thus forming an ingot.
- VAR Vauum Arc Remelting
- the Zr that was used is zirconium sponge (Reactor Grade ASTM B349), and the added elements Nb, P, Ta, and Fe, have a high purity of 99.99% or more.
- this process was repeated about three times, and the alloy was melted under the condition that the chamber for VAR was maintained at a vacuum level of 10 -5 torr or less, thus forming an ingot. Unlike the other alloy elements, P was melted after being compacted, in order to prevent precipitation and segregation.
- cooling was carried out inert gas environment such as argon.
- step (2) for ⁇ -solution heat treatment and ⁇ -quenching solution heat treatment was performed for 30 min at 1,000 to 1,050°C, corresponding to the ⁇ -phase range, and then, water cooling at a rate of about 300°C/sec or more was performed. This process was performed to homogenize the alloy composition in the formed ingot and to uniformly distribute the size of SPP (Secondary Phase Particles) in the matrix.
- SPP Single Phase Particles
- the ingot was clad with a 1 mm thick stainless steel plate and was then spot welded.
- step (3) the ⁇ -quenched sample was subjected to hot rolling.
- the sample was preheated at 630 to 650°C for about 20 to 30 min, and was then rolled at a reduction rate of about 60 to 65%. If the processing temperature falls out of the above range, it is difficult to obtain the rolled material suitable for use in subsequent step (4). Also, if the reduction rate of hot rolling is less than 60%, the texture of the zirconium material becomes non-uniform, which lead to undesirably deterioration in hydrogen embrittlement resistance. On the other hand, if the reduction rate is higher than 80%, subsequent processability may become problematic.
- the material hot-rolled was treated as follows: the clad stainless steel plate was removed, an oxide film and impurities were removed using a pickling solution comprising water, nitric acid and hydrofluoric acid at a volume ratio of 50:40:10, and the remaining oxide film was completely removed using a wire brush in order to facilitate subsequent processing.
- the intermediate vacuum annealing is carried out at a temperature elevated to a fully recrystallization annealing temperature. If the temperature falls out of the above range, corrosion resistance may deteriorate.
- the rolled material was subjected to primary cold rolling at a reduction ratio of about 40 to 50% at an interval of about 0.3 mm for each pass.
- the rolled material was subjected to secondary intermediate vacuum annealing at 570 to 580°C for about 2 to 3 hr.
- the rolled material was subjected to secondary cold rolling at a reduction ratio of about 50 to 60% at an interval of about 0.3 mm for each pass.
- the rolled material was subjected to tertiary intermediate vacuum annealing at 570 to 580°C for 2 to 3 hr.
- the rolled material was subjected to tertiary cold rolling at a reduction ratio of about 30 to 40% at an interval of about 0.3 mm for each pass.
- the rolled material was finally annealed in a high vacuum of 10 -5 torr or less.
- Zircaloy-4 As a commercially available zirconium alloy for use in nuclear power plants, Zircaloy-4 was used.
- Each of the zirconium alloys of Examples 1 to 12 was manufactured into a sheets through the above manufacturing process, which was then fabricated a corrosion test sample having a size of 20 mm x 20 mm x 1.0 mm, followed by stepwise mechanical polishing using #400 to #1200 SiC abrasive paper.
- the sample was pickled using a solution comprising water, nitric acid and hydrofluoric acid at a volume ratio of 50:40:10, sonicated with acetone, and then completely dried in an oven for 24 hr or longer.
- the surface area and the initial weight of the alloy were measured before the alloy was loaded into an autoclave.
- the loaded sample was subjected to corrosion testing for 260 days using a static autoclave at 360°C in an 18.6 MPa pure water atmosphere.
- the corrosion testing results were evaluated depending on 1) when P was added in amounts of 0.02 wt% and 0.05 wt% in the absence of Ta, and 2) when Ta was added in amounts of 0.03 wt% and 0.1 wt% in the presence of 0.05 wt% of P. As such, both 1) and 2) were tested at all of three final annealing temperatures of 460°C, 520°C and 580°C.
- Example 4 When the amount of Ta was 0.1 wt%, corrosion resistance was significantly increased in Example 4 at a final annealing temperature of 460°C and Example 8 at a final annealing temperature of 520°C. When the amount of Ta was 0.03 wt%, corrosion resistance was insignificantly increased.
- corrosion resistance was increased when Ta was added in an amount of 0.01 wt% to 0.15 wt%, and was remarkably increased when Ta was added in an amount of 0.03 wt% to 0.1 wt%.
- Each of the zirconium alloys of Examples 1 to 4 was manufactured into a sheets through the above manufacturing process, which was then formed into a creep test sample.
- a Zircaloy-4 sheet sample of Comparative Example 2 was manufactured through the same process by simulating the commercially available cladding tube of Comparative Example 1.
- the final annealing temperature of Comparative Example 2 was set to 460°C, as in Examples 1 to 4 and Comparative Example 1, and creep testing was carried out.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020150052711A KR101604105B1 (ko) | 2015-04-14 | 2015-04-14 | 우수한 내식성 및 크리프 저항성을 갖는 지르코늄 합금과 그 제조방법 |
PCT/KR2015/004641 WO2016167397A1 (ko) | 2015-04-14 | 2015-05-08 | 우수한 내식성 및 크리프 저항성을 갖는 지르코늄 합금과 그 제조방법 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP3284836A1 EP3284836A1 (en) | 2018-02-21 |
EP3284836A4 EP3284836A4 (en) | 2018-09-26 |
EP3284836B1 true EP3284836B1 (en) | 2020-07-01 |
Family
ID=55649936
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP15889277.8A Active EP3284836B1 (en) | 2015-04-14 | 2015-05-08 | Zirconium alloy having excellent corrosion resistance and creep resistance, and method for manufacturing same |
Country Status (6)
Country | Link |
---|---|
US (1) | US20160304991A1 (ko) |
EP (1) | EP3284836B1 (ko) |
JP (1) | JP6588104B2 (ko) |
KR (1) | KR101604105B1 (ko) |
CN (1) | CN107438675B (ko) |
WO (1) | WO2016167397A1 (ko) |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN108251698A (zh) * | 2018-01-15 | 2018-07-06 | 燕山大学 | 一种耐腐蚀锆合金及其制备方法和应用 |
AR110991A1 (es) | 2018-02-21 | 2019-05-22 | Comision Nac De Energia Atomica Cnea | Aleaciones de circonio con resistencia a la corrosión y temperatura de servicio mejoradas para usar en el revestimiento del combustible y las partes estructurales del núcleo de un reactor nuclear |
US20220184706A1 (en) * | 2019-04-30 | 2022-06-16 | Westinghouse Electric Company Llc | Improved corrosion resistance of additively-manufactured zirconium alloys |
WO2021133194A1 (ru) * | 2019-12-26 | 2021-07-01 | Акционерное Общество "Твэл" | Способ изготовления трубных изделий из циркониевого сплава |
CN115011822B (zh) * | 2022-06-13 | 2023-07-18 | 国核宝钛锆业股份公司 | 一种外方内圆锆合金型材的制备方法 |
CN115652237B (zh) * | 2022-08-16 | 2023-11-24 | 重庆大学 | 含三次孪晶的锆合金及其制备方法 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4814136A (en) | 1987-10-28 | 1989-03-21 | Westinghouse Electric Corp. | Process for the control of liner impurities and light water reactor cladding |
JPH04224648A (ja) * | 1990-12-25 | 1992-08-13 | Kobe Steel Ltd | 高耐蝕性・高強度ジルコニウム合金 |
JPH08253828A (ja) * | 1995-03-14 | 1996-10-01 | Sumitomo Metal Ind Ltd | 高耐食性ジルコニウム合金 |
JPH11194189A (ja) * | 1997-10-13 | 1999-07-21 | Mitsubishi Materials Corp | 耐食性およびクリープ特性にすぐれた原子炉燃料被覆管用Zr合金管の製造方法 |
EP1760724A3 (de) * | 1999-03-29 | 2009-03-18 | AREVA NP GmbH | Brennelement für einen Druckwasser-Reaktor und Verfahren zur Herstellung seiner Hüllrohre |
KR100441562B1 (ko) * | 2001-05-07 | 2004-07-23 | 한국수력원자력 주식회사 | 우수한 내식성과 기계적 특성을 갖는 지르코늄 합금핵연료 피복관 및 그 제조 방법 |
KR100461017B1 (ko) * | 2001-11-02 | 2004-12-09 | 한국수력원자력 주식회사 | 우수한 내식성을 갖는 니오븀 함유 지르코늄 합금핵연료피복관의 제조방법 |
KR100733701B1 (ko) * | 2005-02-07 | 2007-06-28 | 한국원자력연구원 | 크립저항성이 우수한 지르코늄 합금 조성물 |
KR100831578B1 (ko) * | 2006-12-05 | 2008-05-21 | 한국원자력연구원 | 원자력용 우수한 내식성을 갖는 지르코늄 합금 조성물 및이의 제조방법 |
KR100754477B1 (ko) * | 2007-03-26 | 2007-09-03 | 한국원자력연구원 | 크립저항성이 우수한 지르코늄 합금 조성물 |
KR100999387B1 (ko) * | 2008-02-29 | 2010-12-09 | 한국원자력연구원 | 다양한 산소화합물 및 석출상의 제어를 통한 우수한내식성을 갖는 지르코늄 합금 조성물 및 이의 제조방법 |
KR101341135B1 (ko) * | 2011-05-11 | 2013-12-13 | 충남대학교산학협력단 | 우수한 기계적 특성과 내식성을 갖는 핵연료 피복관용 지르코늄 합금 |
CN103409661B (zh) * | 2013-07-31 | 2015-09-23 | 中科华核电技术研究院有限公司 | 用于反应堆核燃料组件的锆铌合金 |
CN103589910B (zh) * | 2013-09-05 | 2016-05-25 | 上海大学 | 核电站燃料包壳用含硫的锆铌铁合金 |
-
2015
- 2015-04-14 KR KR1020150052711A patent/KR101604105B1/ko active IP Right Grant
- 2015-05-08 CN CN201580078752.2A patent/CN107438675B/zh active Active
- 2015-05-08 EP EP15889277.8A patent/EP3284836B1/en active Active
- 2015-05-08 WO PCT/KR2015/004641 patent/WO2016167397A1/ko unknown
- 2015-05-08 JP JP2017553426A patent/JP6588104B2/ja active Active
-
2016
- 2016-04-13 US US15/097,354 patent/US20160304991A1/en not_active Abandoned
Also Published As
Publication number | Publication date |
---|---|
EP3284836A4 (en) | 2018-09-26 |
US20160304991A1 (en) | 2016-10-20 |
WO2016167397A1 (ko) | 2016-10-20 |
CN107438675B (zh) | 2020-04-07 |
JP2018514650A (ja) | 2018-06-07 |
EP3284836A1 (en) | 2018-02-21 |
KR101604105B1 (ko) | 2016-03-16 |
CN107438675A (zh) | 2017-12-05 |
JP6588104B2 (ja) | 2019-10-09 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3284836B1 (en) | Zirconium alloy having excellent corrosion resistance and creep resistance, and method for manufacturing same | |
US6261516B1 (en) | Niobium-containing zirconium alloy for nuclear fuel claddings | |
US11195628B2 (en) | Method of manufacturing a corrosion-resistant zirconium alloy for a nuclear fuel cladding tube | |
EP1930454B1 (en) | Zirconium alloy composition having excellent corrosion resistance for nuclear applications and method of preparing the same | |
KR100441562B1 (ko) | 우수한 내식성과 기계적 특성을 갖는 지르코늄 합금핵연료 피복관 및 그 제조 방법 | |
KR20130098618A (ko) | 사고조건 하의 원자로 내에서 우수한 내산화성을 나타내는 핵연료 피복관용 지르코늄 합금 조성물, 이를 이용하여 제조한 지르코늄 합금 핵연료 피복관 및 이의 제조방법 | |
KR101378066B1 (ko) | 합금원소의 첨가량을 낮추어 부식저항성을 향상시킨 핵연료 피복관용 지르코늄 합금 조성물 및 이를 이용한 지르코늄 합금 핵연료 피복관의 제조방법 | |
US20100108204A1 (en) | Zirconium alloy composition for nuclear fuel cladding tube forming protective oxide film, zirconium alloy nuclear fuel cladding tube manufactured using the composition, and method of manufacturing the zirconium alloy nuclear fuel cladding tube | |
EP3241920B1 (en) | Method for manufacturing nuclear fuel zirconium part by using multi-stage hot-rolling | |
KR101557391B1 (ko) | 우수한 저수소흡수성 및 수소취화 저항성을 갖는 지르코늄합금의 제조방법 및 우수한 저수소흡수성 및 수소취화 저항성을 갖는 지르코늄합금 조성물 | |
CN114150184A (zh) | 一种低应力腐蚀敏感性的高强耐蚀Zr702L合金 | |
KR101265261B1 (ko) | 우수한 내식성 및 고강도를 가지는 지르코늄합금의 제조방법 | |
JP6228231B2 (ja) | ジルコニウム合金の処理方法、該方法で得られたジルコニウム合金、および該合金からなる原子炉の部品 | |
KR20080065749A (ko) | 냉각수 및 수증기 부식 저항성이 우수한 지르코늄 합금조성물 | |
KR20130098621A (ko) | 가혹한 원자로 가동조건에서 내산화성이 우수한 핵연료피복관용 지르코늄 합금 조성물 및 이를 이용한 지르코늄 합금 핵연료 피복관의 제조방법 | |
KR20130098622A (ko) | 고온 가압수 및 수증기 부식환경에서 우수한 내식성을 보유한 핵연료피복관용 지르코늄 합금 조성물 및 이를 이용한 지르코늄 합금 핵연료 피복관의 제조방법 | |
KR100296952B1 (ko) | 핵연료 피복관용 지르코늄 합금조성물 및 제조방법 | |
KR20140120290A (ko) | 사고조건 하의 원자로 내에서 우수한 내산화성을 나타내는 핵연료 피복관용 지르코늄 합금 조성물, 이를 이용하여 제조한 지르코늄 합금 핵연료 피복관 및 이의 제조방법 | |
KR20090079866A (ko) | 냉각수 및 수증기 부식 저항성이 우수한 지르코늄 합금 조성물 | |
KR20080097380A (ko) | 냉각수 및 수증기 부식 저항성이 우수한 지르코늄 합금 조성물 | |
KR101088111B1 (ko) | 부식저항성과 크립저항성이 우수한 지르코늄 합금 조성물 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20171114 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
DAV | Request for validation of the european patent (deleted) | ||
DAX | Request for extension of the european patent (deleted) | ||
A4 | Supplementary search report drawn up and despatched |
Effective date: 20180823 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: B21B 3/00 20060101ALI20180817BHEP Ipc: C22F 1/18 20060101ALI20180817BHEP Ipc: C22C 16/00 20060101AFI20180817BHEP |
|
RIN1 | Information on inventor provided before grant (corrected) |
Inventor name: KIM, JAE IK Inventor name: LEE, CHUNG YONG Inventor name: KIM, YOON HO Inventor name: KO, DAE GYUN Inventor name: LEE, SEUNG JAE Inventor name: CHOI, MIN YOUNG Inventor name: NA, YEON SOO Inventor name: JUNG, TAE SIK Inventor name: MOK, YONG KYOON |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
17Q | First examination report despatched |
Effective date: 20181019 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22F 1/18 20060101ALI20191212BHEP Ipc: C22C 16/00 20060101AFI20191212BHEP Ipc: B21B 3/00 20060101ALI20191212BHEP Ipc: C22C 1/02 20060101ALI20191212BHEP |
|
INTG | Intention to grant announced |
Effective date: 20200110 |
|
RIN1 | Information on inventor provided before grant (corrected) |
Inventor name: KIM, JAE IK Inventor name: CHOI, MIN YOUNG Inventor name: LEE, SEUNG JAE Inventor name: MOK, YONG KYOON Inventor name: KIM, YOON HO Inventor name: LEE, CHUNG YONG Inventor name: JUNG, TAE SIK Inventor name: KO, DAE GYUN Inventor name: NA, YEON SOO |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP Ref country code: AT Ref legal event code: REF Ref document number: 1286240 Country of ref document: AT Kind code of ref document: T Effective date: 20200715 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602015055259 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201001 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20200701 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 1286240 Country of ref document: AT Kind code of ref document: T Effective date: 20200701 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201001 Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201002 Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201102 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: SE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201101 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602015055259 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
26N | No opposition filed |
Effective date: 20210406 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 602015055259 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20210508 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210531 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210508 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210531 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20210531 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210508 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210508 Ref country code: DE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20211201 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210531 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20150508 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200701 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20230510 Year of fee payment: 9 |