CN108728621B - Method for refining martensite lath of high-chromium martensite steel - Google Patents

Method for refining martensite lath of high-chromium martensite steel Download PDF

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CN108728621B
CN108728621B CN201710247462.7A CN201710247462A CN108728621B CN 108728621 B CN108728621 B CN 108728621B CN 201710247462 A CN201710247462 A CN 201710247462A CN 108728621 B CN108728621 B CN 108728621B
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martensite
chromium
steel
lath
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CN108728621A (en
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刘晨曦
刘永长
余黎明
马宗青
李冲
李会军
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Tianjin University
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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • 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 Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention discloses a method for thinning a martensite lath of high-chromium martensite steel, which introduces a large amount of defects such as dislocation and the like by high-temperature pre-deformation through high-temperature treatment and pressure stress application, provides more nucleation positions for the martensite lath, and realizes the thinning of the lath by improving the lath nucleation rate.

Description

Method for refining martensite lath of high-chromium martensite steel
Technical Field
The invention belongs to the technical field of high-chromium martensitic steel production, and particularly relates to a method for refining a high-chromium martensitic steel martensite lath under a high-temperature pre-deformation condition.
Background
The development of power station power equipment technology towards the direction of high power and high parameters is closely related to the development of power station structural materials. Only if the structural material with qualified service performance is obtained, the operation parameters of the power station can be improved as much as possible, and the improvement of the power generation efficiency is realized. Research and development of structural materials for power stations have been carried out by researchers at home and abroad for a long time.
The high-chromium martensite steel is a commonly used metal structure material for nuclear power and thermal power stations, and has good high-temperature mechanical property, corrosion resistance and irradiation resistance. The normalized room temperature structure of high chromium martensitic steels is a lath martensite structure (see fig. 1), so the morphological characteristics of the martensite laths directly affect the service properties of the steel. A great deal of research shows that the mechanical property of the steel has a trend obviously related to the shape of martensite laths, and the strength and the toughness of the steel are obviously increased as the laths are finer. According to the tissue control principle, several methods are mainly expected to realize lath thinning at present: (1) according to the alloying principle, the components of the existing high-chromium martensite steel are continuously finely adjusted, the pinning of the martensite lath is realized by introducing the nano-scale second-phase precipitation, the movement of the lath interface is hindered, and the lath refinement is realized. (2) By changing the heat treatment process parameters of the high-chromium martensite steel, the most suitable normalizing, cooling and tempering parameters are formulated, and the structure refinement can be effectively realized. In addition, the introduction of novel processes such as rolling control and cooling control can also achieve the purpose of tissue regulation. (3) And (3) developing a new processing preparation technology, such as the introduction of an ODS (oxide-dispersion-strengthened steel) steel preparation technology. The method is mainly realized by combining alloy powder and fine and dispersed oxide particles into a block by means of hot isostatic pressing sintering and the like, and the structure refinement is realized by controlling a sintering process. The disadvantages are that: the production cost is very high; large-size parts are limited to be prepared; welding is difficult.
The invention content is as follows:
the invention aims to overcome the defects of the prior art and provide a method for refining a martensite lath of high-chromium martensite steel, which introduces a large amount of dislocation and other defects through high-temperature pre-deformation, thereby providing more nucleation positions for the martensite lath and realizing lath refinement through a mode of improving the lath nucleation rate.
The technical purpose of the invention is realized by the following technical scheme:
the high-chromium martensite steel comprises the following chemical components, by weight, 100 wt% of C, 0.05-0.08 wt%, less than or equal to 0.3 wt% of Si, less than or equal to 0.5 wt% of Mn, 9.5-10.5 wt% of Cr, 0.2-0.5 wt% of Mo, 1.5-1.8 wt% of W, 0.2-0.4 wt% of V, 0.05-0.08 wt% of Nb, less than or equal to 0.040 wt% of N, 1.2-1.6 wt% of Co and the balance of Fe.
In terms of weight percent (wt%) 100, preferably, C is 0.07 wt%, Si is 0.2 wt%, Mn is 0.4 wt%, Cr is 9.8 wt%, Mo is 0.3 wt%, W is 1.7 wt%, V is 0.3 wt%, Nb is 0.0,7 wt%, N is 0.037 wt%, Co is 1.3 wt%, and Fe is the remainder.
A method for thinning martensite laths of high-chromium martensite steel comprises heating a sample to 1100 + -50 deg.C, and keeping the temperature for 8-15 min, preferably 10-12 min; then cooling to a temperature higher than the martensite phase transformation starting temperature Ms, and applying a compressive stress of 100-200 MPa to the sample, wherein the loading time is 80-120 seconds; then unloaded and cooled to room temperature 20-25 ℃.
In the technical scheme, when the temperature is kept at 1100 +/-50 ℃ and then cooled, the temperature is cooled to 500-700 ℃.
When heating is carried out, the temperature is raised at a rate of 2 to 5 ℃ per minute from room temperature of 20 to 25 ℃.
When cooling, the temperature is reduced at the speed of 2-5 ℃ per minute.
In the above technical solution, a compressive stress of 150 to 180MPa is preferably applied for a loading time of 100 to 120 s.
Compared with the samples treated by the conventional process, fig. 2 is a transmission electron microscope photograph of the samples with different loading temperatures and loading stresses, and fig. 3 is the statistical average width of the martensite laths of the different samples. Therefore, the width of the strip of the sample subjected to high-temperature pre-deformation treatment is obviously reduced, and the strip is more obviously thinned along with the reduction of the loading temperature and the increase of the loading stress. Taking a sample with the loading stress of 200MPa and the loading temperature of 500 ℃ as an example, the width of the martensite lath is reduced by 81 percent relative to the sample without pre-deformation treatment, and the lath thinning effect is obvious.
Drawings
FIG. 1 is a transmission electron micrograph of a sample treated by a conventional normalizing process (heat preservation at 1100 ℃ for 10 minutes and air cooling).
FIG. 2 is a transmission electron micrograph of samples at different loading temperatures and loading stresses: (a) 100MPa at 700 deg.C, (b) 200MPa at 700 deg.C, (c) 100MPa at 600 deg.C, (d) 200Pa at 600 deg.C, (e) 100MPa at 500 deg.C, and (f) 200MPa at 500 deg.C.
Figure 3 is the average width of the martensite laths on different samples using the method of the present invention.
Detailed Description
The technical scheme of the invention is further explained by combining specific examples. The martensite laths were measured by transmission electron microscopy using JEM-100CXII, and the width of the martensite laths was obtained by a number of transmission electron microscopy measurements (Li, Q. (2003). Modpling the microstructure-mechanical property correlation for a12 Cr-2W-V-Mo-Ni power plant materials Science and Engineering: A,361(1),385- & 391).
Table 1 chemical composition of high chromium martensitic steel used in the examples of the invention
Components Content (wt.%)
C 0.07
Si 0.2
Mn 0.4
Cr 9.8
Mo 0.3
W 1.7
V 0.3
Nb 0.07
N 0.037
Co 1.3
Fe Balance of
Example 1:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 700 ℃ at the speed of 3 ℃/s, applying 100MPa of compressive stress on the sample, loading for 85 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.28 μm.
Example 2:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 700 ℃ at the speed of 3 ℃/s, applying a pressure stress of 200MPa to the sample, loading for 118 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.25 μm.
Example 3:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 600 ℃ at the speed of 3 ℃/s, applying 100MPa of compressive stress on the sample, loading for 80 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.24 μm.
Example 4:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 600 ℃ at the speed of 3 ℃/s, applying a pressure stress of 200MPa to the sample, loading for 116 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.22 μm.
Example 5:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 500 ℃ at the speed of 3 ℃/s, applying 100MPa of compressive stress on the sample, loading for 82 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.19 μm.
Example 6:
taking steel materials with components shown in the table 1, heating a sample to 1100 ℃ at the speed of 3 ℃/s, preserving heat for 10 minutes, then cooling to 500 ℃ at the speed of 3 ℃/s, applying a pressure stress of 200MPa to the sample, loading for 120 seconds, then unloading, and cooling to room temperature at the speed of 3 ℃/s.
The average width of the martensite laths of the samples treated by the process is reduced from 0.29 μm to 0.16 μm.
The martensite lath can be refined by adjusting the process parameters according to the content of the invention. The invention has been described in an illustrative manner, and it is to be understood that any simple variations, modifications or other equivalent changes which may occur to those skilled in the art without departing from the spirit and the scope of the invention may be resorted to without departing from the scope of the invention.

Claims (5)

1. A method for thinning martensite laths of high-chromium martensite steel is characterized in that a sample is heated to 1100 +/-50 ℃, is subjected to heat preservation for 8-15 minutes, is cooled to 500-700 ℃, and is subjected to 100-200 MPa of compressive stress, and the loading time is 80-120 seconds; unloading and cooling to room temperature of 20-25 ℃; the high-chromium martensite steel comprises the following chemical components, by weight, 100 wt% of C, 0.05-0.08 wt%, less than or equal to 0.3 wt% of Si, less than or equal to 0.5 wt% of Mn, 9.5-10.5 wt% of Cr, 0.2-0.5 wt% of Mo, 1.5-1.8 wt% of W, 0.2-0.4 wt% of V, 0.05-0.08 wt% of Nb, less than or equal to 0.040 wt% of N, 1.2-1.6 wt% of Co and the balance of Fe; when heating, raising the temperature at the speed of 3 ℃ per second from the room temperature of 20-25 ℃; in the cooling, the temperature was decreased at a rate of 3 degrees celsius per second.
2. The method as claimed in claim 1, wherein the high chromium martensitic steel has chemical composition of 100 wt% (wt%), C0.07 wt%, Si 0.2 wt%, Mn 0.4 wt%, Cr 9.8 wt%, Mo 0.3 wt%, W1.7 wt%, V0.3 wt%, Nb 0.07 wt%, N0.037 wt%, Co 1.3 wt%, and Fe the rest.
3. The method as claimed in claim 1 or 2, wherein the martensite lath is cooled to 600-700 ℃ after the temperature is maintained at 1100 ± 50 ℃.
4. The method for refining martensite laths of high-chromium martensite steel according to claim 1 or 2, wherein the sample is heated to 1100 ± 50 ℃ and kept for 10-12 minutes.
5. A method of refining martensitic laths of a high chromium martensitic steel as claimed in claim 1 or 2 wherein a compressive stress of 150-180 MPa is applied for a loading time of 100-120 s.
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101509058A (en) * 2009-03-18 2009-08-19 天津大学 High-chromium ferrite heat-resistant steel fine-deformation martensite lath microstructure refinement method
CN101608254A (en) * 2009-07-21 2009-12-23 天津大学 The little distortion lath of high chromium content ferrite high temperature steel austenitizing martensitic stucture control method
CN103014514A (en) * 2012-11-27 2013-04-03 天津大学 Novel high-chromium ferritic heat-resistant steel and martensite lath refining method
CN105838862A (en) * 2016-05-26 2016-08-10 中国科学院金属研究所 Method for refining grains of maraging stainless steel by cyclic phase transformation

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102256921B1 (en) * 2013-10-02 2021-05-27 더 나노스틸 컴퍼니, 인코포레이티드 Recrystallization, refinement, and strengthening mechanisms for production of advanced high strength metal alloys

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101509058A (en) * 2009-03-18 2009-08-19 天津大学 High-chromium ferrite heat-resistant steel fine-deformation martensite lath microstructure refinement method
CN101608254A (en) * 2009-07-21 2009-12-23 天津大学 The little distortion lath of high chromium content ferrite high temperature steel austenitizing martensitic stucture control method
CN103014514A (en) * 2012-11-27 2013-04-03 天津大学 Novel high-chromium ferritic heat-resistant steel and martensite lath refining method
CN105838862A (en) * 2016-05-26 2016-08-10 中国科学院金属研究所 Method for refining grains of maraging stainless steel by cyclic phase transformation

Non-Patent Citations (5)

* Cited by examiner, † Cited by third party
Title
"10Cr-W型铁素体耐热钢的成分设计及热处理工艺探讨";刘家泳等;《物理测试》;20141231;第32卷(第6期);第17-20页 *
"形变热处理对T91钢组织和性能的影响";宁保群等;《材料研究学报》;20080430;第22卷(第2期);第191-196页 *
"高Cr铁素体耐热钢连续冷却相变行为";高秋志等;《材料热处理学报》;20110930;第32卷(第9期);第67-71页 *
刘家泳等."10Cr-W型铁素体耐热钢的成分设计及热处理工艺探讨".《物理测试》.2014,第32卷(第6期),第17-20页. *
宁保群等."形变热处理对T91钢组织和性能的影响".《材料研究学报》.2008,第22卷(第2期),第191-196页. *

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