EP1544312A1 - Verfahren zur Herstellung von hitzebeständigem Chrom-reichem ferritisch-martensitischem Stahl - Google Patents

Verfahren zur Herstellung von hitzebeständigem Chrom-reichem ferritisch-martensitischem Stahl Download PDF

Info

Publication number
EP1544312A1
EP1544312A1 EP04078288A EP04078288A EP1544312A1 EP 1544312 A1 EP1544312 A1 EP 1544312A1 EP 04078288 A EP04078288 A EP 04078288A EP 04078288 A EP04078288 A EP 04078288A EP 1544312 A1 EP1544312 A1 EP 1544312A1
Authority
EP
European Patent Office
Prior art keywords
heat
martensitic steel
resistant high
high chromium
chromium ferritic
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.)
Granted
Application number
EP04078288A
Other languages
English (en)
French (fr)
Other versions
EP1544312B1 (de
Inventor
Woo Seog Ryu
Sung Ho Kim
Byoung Jun Song
Jun Hwa Hong
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Korea Atomic Energy Research Institute KAERI
Korea Hydro and Nuclear Power Co Ltd
Original Assignee
Korea Atomic Energy Research Institute KAERI
Korea Hydro and Nuclear Power Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Korea Atomic Energy Research Institute KAERI, Korea Hydro and Nuclear Power Co Ltd filed Critical Korea Atomic Energy Research Institute KAERI
Publication of EP1544312A1 publication Critical patent/EP1544312A1/de
Application granted granted Critical
Publication of EP1544312B1 publication Critical patent/EP1544312B1/de
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • 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
    • C21D1/28—Normalising
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • 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

Definitions

  • the present invention relates to a method for producing a heat-resistant high chromium ferritic/martensitic steel, which is applied to the pipes, tubes, and turbines of nuclear power plants, fossil power plants, and petrochemical plants.
  • a heat-resistant high chromium ferritic/martensitic steel is applied to tubes, pipes, turbines and so on of fossil power plants, nuclear power plants and the like.
  • the heat-resistant high chromium ferritic/martensitic steel is made of carbon, silicon, manganese, nickel, chromium, molybdenum, tungsten, vanadium, niobium, phosphorus, sulfur, nitrogen, and iron, and its composition and compositional ratio may be controlled according to its uses and required mechanical properties.
  • a hardening mechanism of the heat-resistant high chromium ferritic/martensitic steel may be classified into a precipitation hardening, which is realized by forming stable precipitates, and a solid solution hardening, which is achieved by dissolving alloying elements in a matrix to form a solid solution.
  • a precipitation hardening which is realized by forming stable precipitates
  • a solid solution hardening which is achieved by dissolving alloying elements in a matrix to form a solid solution.
  • vanadium and niobium as an element which can be applied to a precipitation hardening to precipitate stable carbonitride.
  • molybdenum has been frequently used as an element which can be applied to a solid solution hardening, but recently, tungsten has been used instead of molybdenum.
  • materials containing cobalt, copper, or boron have been developed.
  • efforts have been made to develop materials containing tantalum, rhenium, neodymium or those belonging to a rare-earth series.
  • an alloy with a creep rupture strength of 180 Mpa at 600°C for 10 5 hours is in an experimental stage of development.
  • a method of producing the heat-resistant high chromium ferritic/martensitic steel includes melting the material of the heat-resistant high chromium ferritic/martensitic steel to produce an ingot, hot working the ingot to produce an alloy with a predetermined shape, and heat treating the alloy.
  • Such a heat treatment which is a principal factor determining the mechanical properties of the material of the heat-resistant high chromium ferritic/martensitic steel, serves to stabilize the microstructure of the material, and is comprised of the normalizing and tempering processes (refer to FIG. 1).
  • the normalizing process precipitates existing in the hot-worked material are mostly decomposed at high temperatures to allow the microalloying elements to exist in a solid solution state in a matrix, and the material is air cooled, and the microalloying elements are then existing in a supersaturated solid solution state when an austenite is transformed into a martensite.
  • the normalizing process is conducted at 1050°C.
  • the tempering process serves to recover the dislocations while generating a great amount of precipitates from the microalloying elements existing in the supersaturated solid solution state through the normalizing process, thereby enabling the material to have desirable creep and impact properties. Stability of the precipitates is considered as one of the most important factors determining the high temperature creep rupture strength of the heat-resistant high chromium ferritic/martensitic steel.
  • a tempering temperature is determined at an A c1 temperature or less in consideration of the recovery of the dislocation and the generation of the precipitates.
  • the conventional tempering process is conducted at 700 - 780°C.
  • a method of heat treating a heat-resistant high chromium ferritic/martensitic steel containing cobalt in which a first tempering process is conducted at 500 - 620°C and a second tempering process is conducted at 690 - 740°C, but in this case, a low temperature tempering (first tempering) process is carried out so as to decompose any remaining austenite, which is not transformed to a martensite, after a normalizing process, and the second tempering process is conducted for the generation of precipitates and the recovery of the dislocations, which are a goal of a typical tempering process.
  • first tempering low temperature tempering
  • the heat-resistant high chromium ferritic/martensitic steel produced under conventional heat treatment conditions is disadvantageous in that the high temperature creep life is reduced because the microstructure is softened due to a martensite lath growth in its use at high temperatures, and thus, its application temperature is limited. Accordingly, there remains a need to develop a heat-resistant alloy assuring a desired creep strength even though it is used at a high temperature of 600°C or higher for a long time.
  • an object of the present invention is to provide a method of heat treating the heat-resistant high chromium ferritic/martensitic steel, which has a superior creep rupture strength as well as impact properties similar to the case of adopting a conventional heat treatment.
  • the above object can be accomplished by providing a method of producing the heat-resistant high chromium ferritic/martensitic steel, which includes melting, hot working, and heat treatment processes.
  • the heat treatment step includes a normalizing step at 1030 - 1100°C (first process), the first tempering step at 620 - 720°C (second process), and the second tempering step at 730 - 780°C (third process).
  • Components constituting the heat-resistant high chromium ferritic/martensitic steel used in the present invention are carbon, silicon, manganese, nickel, chromium, molybdenum, tungsten, vanadium, niobium, phosphorus, sulfur, nitrogen, and iron.
  • the heat-resistant high chromium ferritic/martensitic steel includes 0.08 - 0.2 wt% carbon, 0.1 wt% or less silicon, 0.2 - 0.8 wt% manganese, 1.0 wt% or less nickel, 8.0 - 13.0 wt% chromium, 0.03 - 2.5 wt% molybdenum, 3 wt% or less tungsten, 0.1 - 0.3 wt% vanadium, 0.1 - 0.25 wt% niobium, 0.01 wt% or less phosphorus, 0.01 wt% or less sulfur, 0.04 - 0.10 wt% nitrogen, iron as the balance, and inevitable impurities.
  • nitrogen plays an important role in forming the fine chromium carbonitride to maintain the creep strength, and thus, it is very important to properly maintain the content of nitrogen.
  • a heat treatment according to the present invention includes three steps (refer to FIG. 2).
  • a normalizing treatment is conducted within a temperature range of 1030 - 1100°C. Since precipitates formed in the course of producing a heat-resistant alloy are mostly decomposed due to the normalizing treatment, the microalloying elements exist in a solid solution state in a matrix.
  • microalloying elements existing in the solid solution state in the matrix during the normalizing treatment, are present in a supersaturated solid solution state when the austenite is transformed into martensite due to the air cooling process.
  • two-step tempering treatments are conducted, which serves to recover the dislocations while generating a great amount of precipitates, thereby improving the creep and impact properties of the heat-resistant alloy.
  • the tempering treatment is divided into the first tempering treatment corresponding to the second process and the second tempering treatment corresponding to the third process.
  • the second process that is, the first tempering treatment is conducted at 620 - 720°C. Since the first tempering treatment is conducted at 620 - 720°C, which is a temperature range lower than a conventional tempering temperature, relatively fine and stable chromium carbonitride can be generated.
  • a stable precipitate is insufficiently generated or the first tempering time is very long, and when the first tempering temperature is higher than the above-mentioned temperature range, a coarse precipitate is generated or chromium carbonitride is resolved to reduce the dispersion effect of the chromium carbonitride.
  • the fine precipitate generated within the above temperature range serves to efficiently suppress a movement of the dislocation and the growth of a martensite lath when a creep deformation occurs, thereby improving the creep rupture strength.
  • the second tempering treatment is conducted at a temperature range of 730 - 780°C.
  • the second tempering treatment is conducted at a temperature lower than the above-mentioned temperature range, since the dislocation is insufficiently recovered, the impact ductility is poor, and when the second tempering treatment is conducted at a temperature higher than the above-mentioned temperature range, a martensite structure forms sub-grains to significantly reduce the strength because of an excess tempering process.
  • the second tempering treatment is conducted within the above temperature range to assure the desired strength and ductility.
  • An alloy with a composition as described in Table 1 was prepared as a test sample to be used in examples.
  • the alloy was shaped as a 30 kg ingot in a vacuum induction melting furnace. The ingot was hot worked at 1100°C to gain a thickness of 15 mm.
  • the alloy was normalized at 1050°C for 1 hour, and then air-cooled.
  • a tempering treatment was conducted through two steps.
  • the normalized alloy was subjected to the first tempering treatment at 700°C for 2 hours, air-cooled, subjected to the second tempering treatment at 750°C for 1 hour, and air-cooled to produce a heat-resistant high chromium ferritic/martensitic steel.
  • Chemical composition Chemical component (wt%) C Si Mn Ni Cr Mo V Nb P S N Fe 0.15 0.061 0.47 0.45 10.01 1.29 0.200 0.210 0.001 0.001 0.079 Balance
  • COMPARATIVE EXAMPLE 1 Production of a heat-resistant high chromium ferritic/martensitic steel according to a conventional heat treatment
  • example 1 The procedure of example 1 was repeated with the exception of a tempering treatment being conducted through one step, unlike the case of example 1 in which the tempering treatment was conducted through two steps, that is, the first and second tempering treatments, thereby producing an alloy with the same composition as that of example 1.
  • the tempering treatment conditions were 750°C and 2 hours.
  • the tension test was carried out using an Instron 4505.
  • a tension test piece was shaped into a plate with a length of 100 mm, a gauge length of 28.5 mm, and a width of 6.25 mm.
  • the high temperature tension test was conducted at 600 ⁇ 3°C, and all the tension tests were repeated three times to obtain an average of the measured values.
  • the impact test was executed using an impact testing machine, manufactured by SATEC Ltd., at room temperature. At this time, the impact test piece had a length of 55 mm, a width of 10 mm, and a height of 10 mm, and also had a V-notch formed at the center thereof. The impact test was repeated three times to obtain an average of the measured values.
  • the heat-resistant alloy of example 1 according to the present invention had a relatively increased yield and tensile strengths at both the room temperature and a high temperature (600°C) in comparison with those of comparative example 1. Furthermore, the elongation was the same at a high temperature but slightly lower at room temperature.
  • the heat-resistant alloy produced according to the present invention has superior tensile properties at both the room and high temperatures, which are believed to be achieved by the two-step tempering treatments according to the present invention.
  • a creep test piece was shaped into a rod with a length of 90 mm, a gauge length of 30 mm, and a diameter of 6 mm.
  • the creep rupture strength was measured using a creep testing machine, manufactured by Power Engineering Corp., according to a constant load test.
  • the test temperature was adjusted to 600 ⁇ 3°C, and the displacement according to the deformation was measured using a linear variable differential transformer (LVDT).
  • LVDT linear variable differential transformer
  • the present invention is advantageous in that a tempering treatment is conducted under predetermined conditions through two steps to desirably distribute the chromium carbonitride with a size of tens of nanometers to greatly stabilize the structure of the martensite lath, thereby producing a heat-resistant high chromium ferritic/martensitic steel with a superior creep rupture strength as well as superior impact properties.
  • the heat-resistant high chromium ferritic/martensitic steel is usefully applied to nuclear fuel claddings, heat transfer tubes, and pipes of nuclear power plants, and pipes, tubes, turbines and the like for the boilers of fossil power plants, which must have a superior creep rupture strength and impact properties at a high temperature of about 600°C.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)
EP04078288A 2003-12-19 2004-12-03 Verfahren zur Herstellung von hitzebeständigem Chrom-reichem ferritisch-martensitischem Stahl Not-in-force EP1544312B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR2003094059 2003-12-19
KR1020030094059A KR100580112B1 (ko) 2003-12-19 2003-12-19 고 크롬 페라이트/마르텐사이트 내열합금의 제조방법

Publications (2)

Publication Number Publication Date
EP1544312A1 true EP1544312A1 (de) 2005-06-22
EP1544312B1 EP1544312B1 (de) 2010-09-15

Family

ID=34511257

Family Applications (1)

Application Number Title Priority Date Filing Date
EP04078288A Not-in-force EP1544312B1 (de) 2003-12-19 2004-12-03 Verfahren zur Herstellung von hitzebeständigem Chrom-reichem ferritisch-martensitischem Stahl

Country Status (5)

Country Link
EP (1) EP1544312B1 (de)
JP (1) JP4077441B2 (de)
KR (1) KR100580112B1 (de)
AT (1) ATE481509T1 (de)
DE (1) DE602004029131D1 (de)

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8444782B2 (en) * 2008-11-06 2013-05-21 Korea Atomic Energy Research Institute Manufacturing method of high strength ferritic/martensitic steels
CN103409606A (zh) * 2013-06-25 2013-11-27 山东莱芜金雷风电科技股份有限公司 风电主轴锻后热处理方法
EP2764127B1 (de) 2011-10-07 2015-08-12 Babasaheb Neelkanth Kalyani Verfahren zur verbesserung der ermüdungsbeständigkeit von mikrolegierten stählen, schmiedeteile aus dem verfahren und vorrichtung zur ausführung des verfahrens
CN105671255A (zh) * 2016-02-01 2016-06-15 浙江德福精密驱动制造有限公司 一种锻件正火工艺
CN106148881A (zh) * 2015-05-14 2016-11-23 孙豌蓁 用于线性滑轨的渗碳沃斯回火滑块及其制造方法
CN109594019A (zh) * 2018-12-27 2019-04-09 天津理工大学 一种9Cr马氏体耐热铸钢及消除该铸钢中δ-铁素体的方法
US10316379B2 (en) 2015-10-30 2019-06-11 Northwestern University High temperature steel for steam turbine and other applications
CN112626316A (zh) * 2019-09-24 2021-04-09 宝武特种冶金有限公司 一种提高新型马氏体耐热钢g115冲击韧性的热处理方法及应用
CN115354227A (zh) * 2022-08-22 2022-11-18 中国核动力研究设计院 一种反应堆燃料包壳材料用铁素体马氏体钢及其热处理工艺

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101275105B1 (ko) * 2010-10-26 2013-06-17 한국수력원자력 주식회사 크리프 성능이 향상된 원자로 노심부품 소재용 고크롬 페라이트/마르텐사이트강 및 이의 제조방법
WO2013080699A1 (ja) * 2011-11-28 2013-06-06 新日鐵住金株式会社 ステンレス鋼及びその製造方法
RU2580256C1 (ru) * 2014-11-20 2016-04-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Омский государственный университет им. Ф.М. Достоевского" Способ повышения коррозионной стойкости труб из малоуглеродистых сталей
CN105063321B (zh) * 2015-09-26 2017-12-05 叶桂玲 一种高强度脚手架连接件的制备方法
RU2725463C1 (ru) * 2019-08-01 2020-07-02 Федеральное государственное бюджетное образовательное учреждение высшего образования "Московский государственный технологический университет "СТАНКИН" (ФГБОУ ВО "МГТУ "СТАНКИН") Способ термической обработки жаропрочного сплава Х65НВФТ на основе хрома для повышения обрабатываемости резанием

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1189347A (en) * 1966-06-28 1970-04-22 Nippon Kokan Kk High-Temperature Alloy Steel
EP0219089A2 (de) * 1985-10-14 1987-04-22 Sumitomo Metal Industries, Ltd. Hochfester hitzebeständiger ferritischer Stahl mit hohem Chromgehalt und Verfahren zu seiner Herstellung
JPH07118812A (ja) * 1993-10-26 1995-05-09 Hitachi Ltd 耐熱鋳鋼タービンケーシング及びその製造法
JPH08225833A (ja) * 1995-02-16 1996-09-03 Nippon Steel Corp 高温クリープ強度の優れたマルテンサイト系耐熱鋼の製造方法
WO2002081766A1 (fr) * 2001-04-04 2002-10-17 V & M France Acier et tube en acier pour usage a haute temperature

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1189347A (en) * 1966-06-28 1970-04-22 Nippon Kokan Kk High-Temperature Alloy Steel
EP0219089A2 (de) * 1985-10-14 1987-04-22 Sumitomo Metal Industries, Ltd. Hochfester hitzebeständiger ferritischer Stahl mit hohem Chromgehalt und Verfahren zu seiner Herstellung
JPH07118812A (ja) * 1993-10-26 1995-05-09 Hitachi Ltd 耐熱鋳鋼タービンケーシング及びその製造法
JPH08225833A (ja) * 1995-02-16 1996-09-03 Nippon Steel Corp 高温クリープ強度の優れたマルテンサイト系耐熱鋼の製造方法
WO2002081766A1 (fr) * 2001-04-04 2002-10-17 V & M France Acier et tube en acier pour usage a haute temperature

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 08 29 September 1995 (1995-09-29) *
PATENT ABSTRACTS OF JAPAN vol. 1997, no. 01 31 January 1997 (1997-01-31) *

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8444782B2 (en) * 2008-11-06 2013-05-21 Korea Atomic Energy Research Institute Manufacturing method of high strength ferritic/martensitic steels
EP2764127B1 (de) 2011-10-07 2015-08-12 Babasaheb Neelkanth Kalyani Verfahren zur verbesserung der ermüdungsbeständigkeit von mikrolegierten stählen, schmiedeteile aus dem verfahren und vorrichtung zur ausführung des verfahrens
CN103409606A (zh) * 2013-06-25 2013-11-27 山东莱芜金雷风电科技股份有限公司 风电主轴锻后热处理方法
CN106148881A (zh) * 2015-05-14 2016-11-23 孙豌蓁 用于线性滑轨的渗碳沃斯回火滑块及其制造方法
CN106148881B (zh) * 2015-05-14 2018-07-27 孙豌蓁 用于线性滑轨的渗碳沃斯回火滑块及其制造方法
US10316379B2 (en) 2015-10-30 2019-06-11 Northwestern University High temperature steel for steam turbine and other applications
CN105671255A (zh) * 2016-02-01 2016-06-15 浙江德福精密驱动制造有限公司 一种锻件正火工艺
CN109594019A (zh) * 2018-12-27 2019-04-09 天津理工大学 一种9Cr马氏体耐热铸钢及消除该铸钢中δ-铁素体的方法
CN112626316A (zh) * 2019-09-24 2021-04-09 宝武特种冶金有限公司 一种提高新型马氏体耐热钢g115冲击韧性的热处理方法及应用
CN115354227A (zh) * 2022-08-22 2022-11-18 中国核动力研究设计院 一种反应堆燃料包壳材料用铁素体马氏体钢及其热处理工艺

Also Published As

Publication number Publication date
ATE481509T1 (de) 2010-10-15
KR100580112B1 (ko) 2006-05-12
KR20050063010A (ko) 2005-06-28
DE602004029131D1 (de) 2010-10-28
JP2005179772A (ja) 2005-07-07
EP1544312B1 (de) 2010-09-15
JP4077441B2 (ja) 2008-04-16

Similar Documents

Publication Publication Date Title
US4957701A (en) High-strength high-Cr ferritic heat-resistant steel
JP6562476B2 (ja) フェライト系耐熱鋼とその製造方法
EP1544312B1 (de) Verfahren zur Herstellung von hitzebeständigem Chrom-reichem ferritisch-martensitischem Stahl
US7820098B2 (en) High Cr ferritic heat resistance steel
US9631249B2 (en) Stainless steel and method for manufacturing same
JP4221518B2 (ja) フェライト系耐熱鋼
EP0770696B1 (de) Hochfester, hochzaher warmebestandiger stahl und verfahren zu seiner herstellung
US20030185700A1 (en) Heat-resisting steel and method of manufacturing the same
JP5265325B2 (ja) クリープ強度に優れる耐熱鋼およびその製造方法
JP2000204434A (ja) 高温強度に優れたフェライト系耐熱鋼およびその製造方法
EP1382701A1 (de) Ferritischer wärmebeständiger stahl und herstellungsverfahren dafür
JP2003286543A (ja) 長時間クリープ特性に優れた高強度低Ｃｒフェライト系ボイラ用鋼管およびその製造方法
US6696016B1 (en) High-chromium containing ferrite based heat resistant steel
JPH1192881A (ja) ラスマルテンサイト組織のフェライト系耐熱鋼と その製造方法
JP3368413B2 (ja) 高Ｃｒフェライト系耐熱鋼の製造方法
KR20230032300A (ko) 저온 충격특성이 우수한 저방사 강재 및 그 제조 방법
JP2003253402A (ja) 高クロムフェライト耐熱鋼
JP3843314B2 (ja) 高Ｃｒフェライト系耐熱鋼
JP5835079B2 (ja) フェライト系耐熱鋼の製造方法
JP2004018993A (ja) 高温環境下での強度変化の小さい低合金非調質耐熱鋼およびその製造方法
JP2017210656A (ja) 浸炭用鋼の製造方法
JPH05320753A (ja) 高温強度の優れた炭素鋼の製造方法
JP4223161B2 (ja) 超高強度準安定オーステナイト系ステンレス鋼材および製造法
JP2024084300A (ja) 肌焼鋼の製造方法
KR960007427B1 (ko) 고강도 오스테나이트계 석출경화형 스텐레스 냉연강판 제조방법

Legal Events

Date Code Title Description
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

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU MC NL PL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL BA HR LV MK YU

17P Request for examination filed

Effective date: 20050831

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU MC NL PL PT RO SE SI SK TR

17Q First examination report despatched

Effective date: 20091209

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU MC NL PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 602004029131

Country of ref document: DE

Date of ref document: 20101028

Kind code of ref document: P

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20100915

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20100915

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: 20100915

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: 20100915

LTIE Lt: invalidation of european patent or patent extension

Effective date: 20100915

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: 20100915

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: 20100915

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: 20100915

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20101216

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: 20100915

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: 20100915

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: 20110117

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: 20110115

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: 20100915

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: 20100915

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: 20100915

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: 20100915

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: 20100915

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20100915

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: 20101226

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: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101231

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

26N No opposition filed

Effective date: 20110616

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20101215

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20100915

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602004029131

Country of ref document: DE

Effective date: 20110616

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101231

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101231

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101203

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602004029131

Country of ref document: DE

Effective date: 20110701

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110701

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101215

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: 20100915

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20101203

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

Effective date: 20110316

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

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: 20100915

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: 20101215

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20151026

Year of fee payment: 12

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20170831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170102