EP1544312B1 - Procédé de production d'acier ferritique-martensitique à haute teneur en chrome résistant à la chaleur - Google Patents

Procédé de production d'acier ferritique-martensitique à haute teneur en chrome résistant à la chaleur Download PDF

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Publication number
EP1544312B1
EP1544312B1 EP04078288A EP04078288A EP1544312B1 EP 1544312 B1 EP1544312 B1 EP 1544312B1 EP 04078288 A EP04078288 A EP 04078288A EP 04078288 A EP04078288 A EP 04078288A EP 1544312 B1 EP1544312 B1 EP 1544312B1
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EP
European Patent Office
Prior art keywords
heat
martensitic steel
resistant high
high chromium
chromium ferritic
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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.)
Expired - Lifetime
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EP04078288A
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German (de)
English (en)
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EP1544312A1 (fr
Inventor
Woo Seog Ryu
Sung Ho Kim
Byoung Jun Song
Jun Hwa Hong
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Korea Atomic Energy Research Institute KAERI
Korea Hydro and Nuclear Power Co Ltd
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Korea Atomic Energy Research Institute KAERI
Korea Hydro and Nuclear Power Co Ltd
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Publication of EP1544312A1 publication Critical patent/EP1544312A1/fr
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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
    • 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
    • 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.
  • TABLE 1 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.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)

Claims (4)

  1. Procédé de production d'acier à haute teneur en chrome thermorésistant qui comprend 0,08 à 0,2 % en poids de carbone, 0,1 % en poids ou moins de silicium, 0,2 à 0,8 % en poids de manganèse, 1,0 % en poids ou moins de nickel, 8,0 à 13,0 % en poids de chrome, 0,03 à 2,5 % en poids de molybdène, 3 % en poids ou moins de tungstène, 0,1 à 0,3 % en poids de vanadium, 0,1 à 0,25 % en poids de niobium, 0,01 % en poids ou moins de phosphore, 0,01 % en poids ou moins de soufre, 0,04 à 0,10 % en poids d'azote et le reste en tant que fer, le procédé comprenant les processus de fusion, formage à chaud et traitement thermique, où le processus de traitement thermique consiste en :
    une étape de normalisation à 1 030 à 1 100 °C (premier processus) ;
    la première étape de revenu à 620 à 720 °C (deuxième processus) ; et
    la seconde étape de revenu à 730 à 780 °C (troisième processus) .
  2. Procédé selon la revendication 1, comprenant en outre une étape de refroidissement par air après l'étape de normalisation conduite à 1 030 à 1 100 °C.
  3. Procédé selon la revendication 1, comprenant en outre une étape de refroidissement par air après la première étape de revenu conduite à 620 à 720 °C.
  4. Procédé selon la revendication 1, comprenant en outre une étape de refroidissement par air après la seconde étape de revenu conduite à 730 à 780 °C.
EP04078288A 2003-12-19 2004-12-03 Procédé de production d'acier ferritique-martensitique à haute teneur en chrome résistant à la chaleur Expired - Lifetime EP1544312B1 (fr)

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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

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EP1544312A1 EP1544312A1 (fr) 2005-06-22
EP1544312B1 true EP1544312B1 (fr) 2010-09-15

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EP (1) EP1544312B1 (fr)
JP (1) JP4077441B2 (fr)
KR (1) KR100580112B1 (fr)
AT (1) ATE481509T1 (fr)
DE (1) DE602004029131D1 (fr)

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KR101054642B1 (ko) 2008-11-06 2011-08-08 한국원자력연구원 고 강도 페라이트/마르텐사이트 강의 제조방법
KR101275105B1 (ko) * 2010-10-26 2013-06-17 한국수력원자력 주식회사 크리프 성능이 향상된 원자로 노심부품 소재용 고크롬 페라이트/마르텐사이트강 및 이의 제조방법
US9752203B2 (en) 2011-10-07 2017-09-05 Babasaheb Neelkanth Kalyani Process to improve fatigue strength of micro alloy steels, forged parts made from the process and an apparatus to execute the process
CN104080936B (zh) * 2011-11-28 2016-09-21 新日铁住金株式会社 不锈钢及其制造方法
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
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
TWI535857B (zh) * 2015-05-14 2016-06-01 wan-zhen Sun Carburized Vos Tempering Slider for Linear Slide and Its Manufacturing Method
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
WO2017074738A1 (fr) 2015-10-30 2017-05-04 Northwestern University Acier haute température pour turbine à vapeur et autres 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
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
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

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JP4077441B2 (ja) 2008-04-16
ATE481509T1 (de) 2010-10-15
KR20050063010A (ko) 2005-06-28
DE602004029131D1 (de) 2010-10-28
JP2005179772A (ja) 2005-07-07
EP1544312A1 (fr) 2005-06-22
KR100580112B1 (ko) 2006-05-12

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