CN107843591A - Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods - Google Patents

Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods Download PDF

Info

Publication number
CN107843591A
CN107843591A CN201610833351.XA CN201610833351A CN107843591A CN 107843591 A CN107843591 A CN 107843591A CN 201610833351 A CN201610833351 A CN 201610833351A CN 107843591 A CN107843591 A CN 107843591A
Authority
CN
China
Prior art keywords
aging
sample
rank
tissue
brinell hardness
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.)
Pending
Application number
CN201610833351.XA
Other languages
Chinese (zh)
Inventor
严伟
杨旭
单以银
肖福仁
杨柯
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.)
Institute of Metal Research of CAS
Original Assignee
Institute of Metal Research of CAS
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 Institute of Metal Research of CAS filed Critical Institute of Metal Research of CAS
Priority to CN201610833351.XA priority Critical patent/CN107843591A/en
Publication of CN107843591A publication Critical patent/CN107843591A/en
Pending legal-status Critical Current

Links

Classifications

    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N21/00—Investigating or analysing materials by the use of optical means, i.e. using sub-millimetre waves, infrared, visible or ultraviolet light
    • G01N21/84—Systems specially adapted for particular applications
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N3/00—Investigating strength properties of solid materials by application of mechanical stress
    • G01N3/40—Investigating hardness or rebound hardness
    • G—PHYSICS
    • G01—MEASURING; TESTING
    • G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
    • G01N2203/00—Investigating strength properties of solid materials by application of mechanical stress
    • G01N2203/0098—Tests specified by its name, e.g. Charpy, Brinnel, Mullen

Landscapes

  • Physics & Mathematics (AREA)
  • Health & Medical Sciences (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Chemical & Material Sciences (AREA)
  • Analytical Chemistry (AREA)
  • Biochemistry (AREA)
  • General Health & Medical Sciences (AREA)
  • General Physics & Mathematics (AREA)
  • Immunology (AREA)
  • Pathology (AREA)
  • Investigating And Analyzing Materials By Characteristic Methods (AREA)

Abstract

The present invention relates to ferrous materials to examine field, more particularly to a kind of thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods.The present invention uses properly mixed etchant by selecting strict preparation method of sample so that the thermal power plants can tentatively evaluate and test aging rank under the metallographic microscope of low power number with T/P91 heat resisting steel aging ranking methods by metallographic structure pattern.The phenomenon of growing up of Laves phase average crystallite dimensions when the thermal power plants T/P91 heat resisting steel aging ranking methods of the present invention, considering not only the average grain size of precipitated phase in evaluation criterion, while having considered different degree of agings.Compared to single pass precipitated phase carbide M in the prior art23C6Size judges the degree of aging of heat resisting steel, and the ranking method in the present invention is more accurate, the stricter evaluation criterion of use, for super (super-) critical heat resisting steel in actual production accident prevention more added with guiding value.

Description

Thermal power plants T/P91 based on Brinell hardness tissue and precipitated phase characteristic synthetic Heat resisting steel aging ranking method
Technical field
The present invention relates to ferrous materials to examine field, more particularly to a kind of based on Brinell hardness, tissue and precipitation phase character Comprehensive thermal power plants T/P91 super (super-) critical unit heat resisting steel aging ranking methods.
Background technology
The energy is the material base of economic growth and social development, as energy shortage situation increasingly highlights and environmental pollution Problem increasingly aggravates, and various countries begin to seek to Large Copacity, the development of efficient generating set from last century 70, the eighties.Carry High generating set steam parameter is to improve the maximally efficient solution method of generating efficiency.Countries in the world are just progressively by generator at present The steam parameter of group to overcritical (pressure is higher than 22.19MPa) and super faces from subcritical (16.77MPa, 540 DEG C) lifting Boundary (temperature is higher than 31MPa more than 593 DEG C, pressure) state.
Super (super-) critical equipment is broadly divided into boiler series and steam turbine series.Boiler series are by using superheater tube as generation The small-diameter, thin-walled heat exchanger tube (boiler tube) of table and that superheated steam is transported to main steam pipe and collector of steam turbine etc. is big Bore thick walled steel tube (delivery pipe) is formed.Device temperature typically refers to the vapor (steam) temperature of main steam pipe, by contrast, steam turbine Low 20 DEG C or so of inlet temperature, and high 20 DEG C or so of superheater tube temperature.Therefore, the small-bore boiler tube such as superheater tube mainly makes With the high high intensity high corrosion resistance austenitic heat-resistance steel of Cr contents.It is and large-scale for heavy walls such as the heavy caliber delivery pipes such as main steam pipe Structural member, because thermal stress caused by the temperature difference of inside and outside can aggravate creep fatigue damage, therefore usually using ferritic heat-resistant steel. Compared to austenitic heat-resistance steel, ferritic heat-resistant steel has excellent thermal conductivity, low thermal coefficient of expansion, good anti intercrystalline corrosion The advantages that with anti-stress corrosion performance and relatively low production cost, turn into the preferred steel of super (super-) critical unit critical component Kind.
Because supercritical unit heat resisting steel is long-term use of in high temperature, high pressure and corrosive medium coupling condition, it is organized in length During being on active service aging can occur for the phase, thus cause the performance of novel martensitic heat resisting steel to occur to degenerate so that super (super-) critical The generation of the failure accidents such as unit is cracking in the process of running, booster, the normal operation that can not only influence power plant cause weight Big economic loss, but also be likely to result in the tragedies such as the injures and deaths of personnel and occur while bring extremely severe social influence.
In patent document 1 (publication number CN103630566A, publication date on March 12nd, 2014), one kind is described Super304H steel M23C6The quantitative metallographic analysis method of phase, it uses corrosive agent to corrode metallographic structure, by scanning electricity Sub- microscope obtains metallograph, with reference to the volume hundred of image analysis software adjustment image tonescale range statistics Carbide Precipitation phase Divide and compare content.But methods described does not disclose specific rating scale, is unfavorable for scientific research and technologist is accurately commented Valency degree of aging.
In patent document 2 (publication number CN103063549A, publication date on April 24th, 2013), a kind of T/P91 steel is described Based on the aging ranking method of precipitated phase particle diameter size, the metallographic structure after corrosion is calculated by SEM Precipitated phase average particulate diameter, and the size according to precipitated phase average diameter of particles is further disclosed, T/P91 steel agings are commented Calibration standard is divided into 5 grades.But methods described is graded according to the size of the precipitated phase average diameter of particles of acquisition, evaluation Reference standard is single, causes grading error larger, is unfavorable for production application.
The content of the invention
It is an object of the invention to provide it is a kind of simple, be accurately based on Brinell hardness, tissue and precipitated phase characteristic synthetic Thermal power plants T/P91 heat resisting steel aging ranking methods, can be used for instructing thermal power plant's Site Detection and security evaluation Reliability, the degree of aging of the supercritical unit heat resisting steel after longtime running is accurately evaluated, and then instruct work Artist person takes appropriate measures, and ensures the safe operation of unit, avoids major accident.
In order to reach foregoing invention purpose, the present invention is as follows using technical scheme：
A kind of thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic are graded with the aging of T/P91 heat resisting steel Method, comprise the following steps：
(1) sample and hardness determination are cut
Sample is cut from examined pipe, the sample includes examining the whole wall thickness section at position；Hardness measurement Using Brinell hardness method of testing, performed according to GB standard methods described；
(2) sample is smooth with polishing
The inspection face of sample first have to carry out it is smooth, from cutting on line or emery wheel hands- operation, with emulsion or cold But water cools down to sample, grinds the time as 20~50 seconds；After sample is smooth, ground, used successively with sand paper is from coarse to fine 150#, 240#, 400#, 800#, 1200#, 2000# sand paper are ground successively；
(3) sample polishing and etch
Grinding cut is removed using the method for mechanical polishing during polishing and distortion layer, antiscuffing paste granularity are selected No. W2.5, adopted With can the simultaneously rotten etchant for carving crystal boundary and tissue topography be corroded；
(4) metallographic structure photo
Metallograph selects representational visual field to carry out metallographic under the enlargement ratio of 100~500 times of metallographic microscope Tissue topography's observation carries out the evaluation of aging rank, amplifies 1000~2000 times of calculating precipitated phase chis under a scanning electron microscope The evaluation of little progress row aging rank；
(5) aging rank is evaluated
Grown up rule according to the change of heat resisting steel Brinell hardness, microstructure evolution and Second Phase Precipitation, from slight aging to complete Aging is divided into 5 ranks；
1 grade of aging is ultralight degree aging rank：Tissue topography is still tiny lath martensite tissue；Carbide M23C6Uniformly Small and dispersed is distributed in original austenite crystal prevention, on martensite lath circle, average grain size≤0.6 μm, and Brinell hardness HB >= 180；
2 grades of aging is slight aging rank：Martensite packets occur to merge and fragmentation, organize to there is thick lath Based on beam and subgrain；Carbide M23C6Generation aggregation roughening, 0.6 μm<Average grain size≤0.9 μm；160≤HB of hardness< 180；
3 grades of aging is mittlere alterung rank：A large amount of subgrains occur after martensite lath merging and fragmentation, and tissue is clearly visible A large amount of martensite blocks for deteriorating to ferritic structure；Large-size carbon compound M23C6Start annex small size carbide, 0.9 μm<Greatly Particle size≤1.5 μm, 150≤HB of Brinell hardness<160；
4 grades of aging is severe aging rank：Bulk ferrite merges, and tissue sees that whole former crystal grain difficult to understand all deteriorates to The ferritic structure of brilliant white；Carbide M23C6It is evenly distributed on matrix and crystal boundary, size difference is obvious, 1.5 μm<Big Particle size≤2.0 μm, 135≤HB of Brinell hardness<150；
5 grades of aging is complete aging rank：Multiple original austenite ferrite crystal grains merge, and tissue sees large stretch of brilliant white The ferritic structure of color；Carbide M23C6Size is substantially grown up and quantity is reduced, other small sizes M23C6Be partly dissolved or< 50nm, now bulky grain size>2.0 μm, Brinell hardness HB<135.
Described aging ranking method, in step (1), the cutting of sample uses mechanical means, to sample during cutting processing Cooled down, prevent tissue from changing；Sample removes heat affected area after cutting according to gas flame cuttiug completely.
Described aging ranking method, in step (1), for thicker part, it is allowed to if cutting dry sample, ensure covering It is whole to examine section；GB standard is that GB/T 231.4-2009 metal materials Brinell hardness tests the 4th part：Hardness number table.
Described aging ranking method, in step (3), etchant is picric acid hydrochloride alcohol solution, each component in solution For：Picric acid 1g, hydrochloric acid 5ml, alcohol 100ml, etching time are 40~80 seconds.
Described aging ranking method, in step (4), when metallographic structure photo obtains, ensure diameter or diagonal in visual field At least 4 crystal grain in the range of line length, if selecting more low range when coarse grains are serious.
Described aging ranking method, in step (4), precipitate size statistics, which calculates, uses Image-pro plus softwares Adjust image tonescale and carry out analytic statistics, or statistics calculating is carried out with ImageJ softwares.
Described aging ranking method, in step (5), when the failure state between two ranks, use half Level represents.
Described aging ranking method, in step (5), when the thermal power plants exist with the heat-resisting structure of steel of T/P91 During aging non-uniform phenomenon, evaluated respectively according to its concrete condition；When it is uneven for entirety, with degree of aging most serious Aging rank is used as evaluation final result, and the note in conclusion is evaluated；When simply local uneven, then to be primarily present Form, i.e., identical aging level organization account for more than 85% aging rank of total inspection area as evaluation final result.
Advantages of the present invention and beneficial effect are：
(1) present invention is by selecting strict preparation method of sample, and uses properly mixed etchant so that the fire Electric power plant can pass through metallographic structure pattern with T/P91 heat resisting steel aging ranking methods under the metallographic microscope of low power number Preliminary evaluation and test aging rank, the ranking method in the present invention is simple, and the technologist of factory is easily mastered, and is greatly reduced simultaneously Testing cost.
(2) thermal power plants T/P91 heat resisting steel aging ranking methods of the invention, analysis is considered not only in evaluation criterion The phenomenon of growing up of Laves phase averages crystallite dimension when going out the average grain size of phase, while having considered different degree of agings. Compared to single pass precipitated phase carbide M in the prior art23C6Size judges the degree of aging of heat resisting steel, in the present invention Ranking method is more accurate, employs stricter evaluation criterion, for the thing of super (super-) critical heat resisting steel in actual production Therefore prevention is more added with guiding value.
Brief description of the drawings
Fig. 1 (a)-(c) is that (1 grade old for ultralight degree aging rank with P91 heat resisting steel aging ranks for thermal power plants of the present invention Change) when metallurgical tissue picture.Wherein, Fig. 1 (a) metallographics 200 ×；Fig. 1 (b) metallographics 500 ×；Fig. 1 (c) scannings 2000 ×.
Fig. 2 (a)-(c) is that (2 grades old for slight aging rank with P91 heat resisting steel aging ranks for thermal power plants of the present invention Change) when metallurgical tissue picture.Wherein, Fig. 2 (a) metallographics 200 ×；Fig. 2 (b) metallographics 500 ×；Fig. 2 (c) scannings 2000 ×.
Fig. 3 (a)-(c) is that (3 grades old for mittlere alterung rank with P91 heat resisting steel aging ranks for thermal power plants of the present invention Change) when metallurgical tissue picture.Wherein, Fig. 3 (a) metallographics 200 ×；Fig. 3 (b) metallographics 500 ×；Fig. 3 (c) scannings 2000 ×.
Fig. 4 (a)-(c) is that (4 grades old for severe aging rank with P91 heat resisting steel aging ranks for thermal power plants of the present invention Change) when metallurgical tissue picture.Wherein, Fig. 4 (a) metallographics 200 ×；Fig. 4 (b) metallographics 500 ×；Fig. 4 (c) scannings 2000 ×.
Fig. 5 (a)-(c) is that (5 grades old for complete aging rank with P91 heat resisting steel aging ranks for thermal power plants of the present invention Change) when metallurgical tissue picture.Wherein, Fig. 5 (a) metallographics 100 ×；Fig. 5 (b) metallographics 200 ×；Fig. 5 (c) scannings 1000 ×.
Fig. 6 (a)-(c) is the thermal power plants heat-resisting structure of steel metallographics of P91 and scan image in the embodiment of the present invention.Its In, Fig. 6 (a) metallographics 100 ×；Fig. 6 (b) metallographics 200 ×；Fig. 6 (c) scannings 2000 ×.
Embodiment
Below, the present invention is further elaborated on by embodiment and accompanying drawing.
Embodiment 1：
It is that Π types are arranged that sampling, which is selected from No. 1 boiler of certain power plant 600MW supercritical generating sets, evaporation capacity 1900t/h, reheating Equipment matter be full martensitic structure P91 steel, specification be 682 × 23.5mm of Φ 90 ° of elbows, reheater outlet vapor pressure 4.63MPa, 569 DEG C of outlet steam temperature, unit have added up operation 51381h.
(1) sample is cut
Sample is cut from examined pipe, the sample should include the whole wall thickness section for examining position, and consider Transverse and longitudinal position to difference；For thicker part, it is allowed to if cutting dry sample, it is necessary to ensure to cover whole inspection section；Hardness Measurement uses Brinell hardness method of testing, and according to national standard, (GB/T 231.4-2009 metal materials Brinell hardness tests the 4th part： Hardness number table) methods described execution.The cutting of sample uses mechanical means, needs to cool down sample during cutting processing, prevents Only tissue changes；If sample must use gas flame cuttiug, need completely to remove heat affected area after cutting.
(2) sample is smooth with polishing
The inspection face of sample first has to carry out smooth, cutting on line or emery wheel hands- operation, uses emulsion or cooling Water cools down to sample, grinds the time as 20~50 seconds, ensures that the inspection face of sample is smooth；After sample is smooth, with sand paper by Slightly to carefully grinding successively, ground successively using 150#, 240#, 400#, 800#, 1200#, 2000# sand paper；
(3) sample polishing and etch
Grinding cut is removed using the method for mechanical polishing and distortion layer, antiscuffing paste granularity select No. W2.5, etchant is adopted With picric acid hydrochloride alcohol solution, each group is divided into solution：Picric acid 1g, hydrochloric acid 5ml, 100 milliliters of alcohol, etching time 40 ~80 seconds；
(4) metallographic structure photo
Metallograph selects representational visual field to carry out aging under the enlargement ratio of 100~500 times of metallographic microscope The evaluation of rank, metallographic structure photo should ensure that in visual field at least 4 crystal grain in the range of diameter or catercorner length when obtaining, More low range can be selected when if coarse grains are serious.Precipitate size statistics is calculated using Image-pro plus softwares adjustment figure As color range carries out analytic statistics.
(5) aging rank is evaluated
Grown up rule according to the change of heat resisting steel Brinell hardness, microstructure evolution and Second Phase Precipitation, from slight aging to complete Aging is divided into 5 ranks；
As shown in Fig. 1 (a)-(c), ultralight degree aging rank (1 grade of aging)：Tissue topography is still tiny lath martensite group Knit；Carbide M23C6Uniform small and dispersed is distributed in original austenite crystal prevention, on martensite lath circle, the μ of average grain size≤0.6 M, Brinell hardness HB >=180.
As shown in Fig. 2 (a)-(c), slight aging rank (2 grades of aging)：Martensite packets occur to merge and fragmentation, group Knit to occur based on thick lath beam and subgrain；Carbide M23C6Generation aggregation roughening, 0.6 μm<Average grain size≤0.9 μm；160≤HB of hardness<180.
As shown in Fig. 3 (a)-(c), mittlere alterung rank (3 grades of aging)：A large amount of subgrains after martensite lath merging and fragmentation Occur, tissue can be clearly visible a large amount of martensite blocks for deteriorating to ferritic structure；Large-size carbon compound M23C6Start to annex small Size carbide, 0.9 μm<Bulky grain size≤1.5 μm, 150≤HB of Brinell hardness<160.
As shown in Fig. 4 (a)-(c), severe aging rank (4 grades of aging)：Bulk ferrite merges, and tissue can be seen Whole former crystal grain difficult to understand all deteriorates to the ferritic structure of brilliant white；Carbide M23C6It is evenly distributed on matrix and crystal boundary, size is big Small difference is obvious, 1.5 μm<Bulky grain size≤2.0 μm, 135≤HB of Brinell hardness<150.
As shown in 5 (a)-(c), complete aging rank (5 grades of aging)：Multiple original austenite ferrite crystal grains merge, Tissue is it can be seen that the ferritic structure of large stretch of brilliant white；Carbide M23C6Size is substantially grown up and quantity is seldom, other small sizes M23C6Be partly dissolved or<50nm, now bulky grain size>2.0 μm, Brinell hardness HB<135.
When the failure state between two ranks, represented using half grade, such as：1.5 grades, 2.5 grades etc..When described There is aging non-uniform phenomenon in thermal power plants, should be evaluated respectively according to its concrete condition with the heat-resisting structure of steel of T/P91；When it For it is overall uneven when, using the aging rank of degree of aging most serious as evaluating final result, and be attached with conclusion is evaluated Explanation；, then should be in the form of being primarily present when being that part is uneven, i.e., identical aging level organization accounts for the 85% of total inspection area Aging rank above is as evaluation final result.With the above method, the Brinell hardness for obtaining P91 under the state is HB153.
The metallographic structure as obtained as shown in Fig. 6 (a)-(c) by above method and precipitated phase scan tissue picture, A large amount of subgrains occur after analyzing microstructure martensite lath merging and fragmentation, and tissue, which can be clearly visible, largely deteriorates to ferrite The martensite block of tissue；Large-size carbon compound M23C6Start to annex small size carbide, should using Image-pro plus statistics Precipitate size is 1.3 μm, therefore can be determined that the pipeline is currently at present invention provide that 3 grades of aging rank, i.e., moderate is old Change rank.

Claims (8)

  1. A kind of 1. thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel agings grading side Method, it is characterised in that comprise the following steps：
    (1) sample and hardness determination are cut
    Sample is cut from examined pipe, the sample includes examining the whole wall thickness section at position；Hardness measurement uses Brinell hardness method of testing, performed according to GB standard methods described；
    (2) sample is smooth with polishing
    The inspection face of sample first have to carry out it is smooth, from cutting on line or emery wheel hands- operation, with emulsion or cooling water Sample is cooled down, grinds the time as 20~50 seconds；After sample is smooth, ground successively with sand paper is from coarse to fine, using 150#, 240#, 400#, 800#, 1200#, 2000# sand paper are ground successively；
    (3) sample polishing and etch
    Grinding cut and distortion layer are removed using the method for mechanical polishing during polishing, antiscuffing paste granularity selects No. W2.5, using can Crystal boundary of rotten quarter and the etchant of tissue topography are corroded simultaneously；
    (4) metallographic structure photo
    Metallograph selects representational visual field to carry out metallographic structure under the enlargement ratio of 100~500 times of metallographic microscope Morphology observation carries out the evaluation of aging rank, amplifies 1000~2000 times of calculating precipitate sizes under a scanning electron microscope and enters The evaluation of row aging rank；
    (5) aging rank is evaluated
    Grown up rule according to the change of heat resisting steel Brinell hardness, microstructure evolution and Second Phase Precipitation, from slight aging to complete aging It is divided into 5 ranks；
    1 grade of aging is ultralight degree aging rank：Tissue topography is still tiny lath martensite tissue；Carbide M23C6It is uniformly tiny Dispersed precipitate is on original austenite crystal prevention, martensite lath circle, average grain size≤0.6 μm, Brinell hardness HB >=180；
    2 grades of aging is slight aging rank：Martensite packets occur merge and fragmentation, organize with occur thick lath beam and Based on subgrain；Carbide M23C6Generation aggregation roughening, 0.6 μm<Average grain size≤0.9 μm；160≤HB of hardness<180；
    3 grades of aging is mittlere alterung rank：A large amount of subgrains occur after martensite lath merging and fragmentation, and tissue is clearly visible a large amount of Deteriorate to the martensite block of ferritic structure；Large-size carbon compound M23C6Start annex small size carbide, 0.9 μm<Bulky grain Size≤1.5 μm, 150≤HB of Brinell hardness<160；
    4 grades of aging is severe aging rank：Bulk ferrite merges, and tissue sees that whole former crystal grain difficult to understand all deteriorates to brilliant white Ferritic structure；Carbide M23C6It is evenly distributed on matrix and crystal boundary, size difference is obvious, 1.5 μm<Bulky grain chi It is very little≤2.0 μm, 135≤HB of Brinell hardness<150；
    5 grades of aging is complete aging rank：Multiple original austenite ferrite crystal grains merge, and tissue sees large stretch of brilliant white Ferritic structure；Carbide M23C6Size is substantially grown up and quantity is reduced, other small sizes M23C6Be partly dissolved or<50nm, this When bulky grain size>2.0 μm, Brinell hardness HB<135.
  2. 2. according to the aging ranking method described in claim 1, it is characterised in that in step (1), the cutting of sample is using machinery Method, sample is cooled down during cutting processing, prevent tissue from changing；Sample is according to gas flame cuttiug, by heat after cutting The zone of influence removes completely.
  3. 3. according to the aging ranking method described in claim 1, it is characterised in that in step (1), for thicker part, permit If being permitted to cut dry sample, ensure that covering is whole and examine section；GB standard is GB/T231.4-2009 metal material Brinell hardness Test the 4th part：Hardness number table.
  4. 4. according to the aging ranking method described in claim 1, it is characterised in that in step (3), etchant is picric acid hydrochloric acid Alcoholic solution, each group is divided into solution：Picric acid 1g, hydrochloric acid 5ml, alcohol 100ml, etching time are 40~80 seconds.
  5. 5. according to the aging ranking method described in claim 1, it is characterised in that in step (4), metallographic structure photo obtains When, ensure in visual field at least 4 crystal grain in the range of diameter or catercorner length, if selecting more low power when coarse grains are serious Rate.
  6. 6. according to the aging ranking method described in claim 1, it is characterised in that in step (4), precipitate size statistics calculates Analytic statistics is carried out using Image-pro plus softwares adjustment image tonescale, or statistics calculating is carried out with ImageJ softwares.
  7. 7. according to the aging ranking method described in claim 1, it is characterised in that in step (5), when between two ranks Failure state, use half grade expression.
  8. 8. according to the aging ranking method described in claim 1, it is characterised in that in step (5), when the thermal power plants are used When aging non-uniform phenomenon be present in the heat-resisting structure of steel of T/P91, evaluated respectively according to its concrete condition；When it is uneven for entirety When, using the aging rank of degree of aging most serious as evaluation final result, and the note in conclusion is evaluated；When simply office Portion is uneven, then in the form of being primarily present, i.e., identical aging level organization accounts for more than 85% aging rank of total inspection area As evaluation final result.
CN201610833351.XA 2016-09-20 2016-09-20 Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods Pending CN107843591A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201610833351.XA CN107843591A (en) 2016-09-20 2016-09-20 Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201610833351.XA CN107843591A (en) 2016-09-20 2016-09-20 Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods

Publications (1)

Publication Number Publication Date
CN107843591A true CN107843591A (en) 2018-03-27

Family

ID=61656824

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201610833351.XA Pending CN107843591A (en) 2016-09-20 2016-09-20 Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods

Country Status (1)

Country Link
CN (1) CN107843591A (en)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109002628A (en) * 2018-07-31 2018-12-14 天津大学 A kind of elevated temperature strength prediction technique for the martensite steel degenerated based on microstructure
CN109307630A (en) * 2018-09-30 2019-02-05 中国大唐集团科学技术研究院有限公司华中分公司 The aging ranking method of fired power generating unit jet chimney 15Cr1Mo1V steel based on on-site test hardness and metallographic structure
CN109540636A (en) * 2018-12-11 2019-03-29 渤海造船厂集团有限公司 A kind of low medium alloy steel original austenite Display of Grain Boundary method of quenched and tempered state
CN110333192A (en) * 2019-05-29 2019-10-15 合肥通用机械研究院有限公司 The quick method of determination and evaluation of harmful precipitated phase in a kind of two phase stainless steel
CN112505080A (en) * 2020-11-10 2021-03-16 浙江浙能兰溪发电有限责任公司 Safety assessment method for P91 pipeline and header of power station boiler

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103063549A (en) * 2012-12-26 2013-04-24 广东电网公司电力科学研究院 Ageing rating method for T/P91 steel based on diameter of precipitated phase particle

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103063549A (en) * 2012-12-26 2013-04-24 广东电网公司电力科学研究院 Ageing rating method for T/P91 steel based on diameter of precipitated phase particle

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
李灼贤 等: "电站Ｔ91炉管服役后的老化状况量化评定", 《广东电力》 *
赵君: "火力发电厂锅炉用SA213-T91材料的组织性能演化研究", 《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》 *

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109002628A (en) * 2018-07-31 2018-12-14 天津大学 A kind of elevated temperature strength prediction technique for the martensite steel degenerated based on microstructure
CN109002628B (en) * 2018-07-31 2022-10-21 天津大学 High-temperature strength prediction method of martensitic steel based on microstructure degradation
CN109307630A (en) * 2018-09-30 2019-02-05 中国大唐集团科学技术研究院有限公司华中分公司 The aging ranking method of fired power generating unit jet chimney 15Cr1Mo1V steel based on on-site test hardness and metallographic structure
CN109540636A (en) * 2018-12-11 2019-03-29 渤海造船厂集团有限公司 A kind of low medium alloy steel original austenite Display of Grain Boundary method of quenched and tempered state
CN110333192A (en) * 2019-05-29 2019-10-15 合肥通用机械研究院有限公司 The quick method of determination and evaluation of harmful precipitated phase in a kind of two phase stainless steel
CN112505080A (en) * 2020-11-10 2021-03-16 浙江浙能兰溪发电有限责任公司 Safety assessment method for P91 pipeline and header of power station boiler

Similar Documents

Publication Publication Date Title
CN107843706A (en) Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P92 heat resisting steel aging ranking methods
CN107843591A (en) Thermal power plants based on Brinell hardness tissue and precipitated phase characteristic synthetic T/P91 heat resisting steel aging ranking methods
Duarte et al. Failure analysis of the wall tubes of a water-tube boiler
CN109307630B (en) Aging rating method of 15Cr1Mo1V steel for steam pipeline of thermal power unit based on-site hardness and metallographic structure detection
Xu et al. Low cycle fatigue behavior and microstructure evolution of a novel Fe-22Cr-15Ni austenitic heat-resistant steel
Liu et al. Failure investigation of a 304 stainless steel geothermal tube
Chen et al. Failure analysis on abnormal leakage of TP321 stainless steel pipe of medium temperature shifting gas in hydrogen production system
Zangeneh et al. Failure investigation of a deaerating feed-water heater in a power plant
Totemeier et al. Effect of normalization temperature on the creep strength of modified 9Cr-1Mo steel
Abou-Elazm et al. Failure investigation of secondary super-heater tubes in a power boiler
Li et al. Failure analysis of reheater tubes in a 350 MW supercritical circulating fluidized bed boiler
Chen et al. Effect of different loading conditions on corrosion fatigue crack growth rate of a nickel-based alloy in supercritical water
Marquez et al. Failure analysis of carbon steel tubes in a reformed gas boiler feed water preheater
CN109187543A (en) A kind of in-service ethylene cracking tube embrittlement classification lifetime estimation method
Yang et al. Crack investigation of martensitic stainless steel turbine blade in thermal power plant
Feng et al. Failure analysis of welded joint leakage of TP321 pressure pipeline
Guerre et al. SCC crack growth rate of alloy 82 in PWR primary water conditions—effect of a thermal treatment
CN107356449B (en) A kind of sampling method of nuclear steam generator heat-transfer pipe prefabricated batch inspection
Hu et al. Leakage failure analysis on water wall pipes of an ultra-supercritical boiler
CN115326796A (en) Method for judging abnormal growth tendency of crystal grains of supplied Super304H steel pipe in high-temperature long-time service and application
Guan et al. Quantitative study of creep cavity area of HP40 furnace tubes
Yamazaki et al. Creep-Fatigue Damage for Boiler Header Stub Mock-Up Specimen of 47Ni–23Cr–23Fe–7W Alloy
Almazrouee et al. Role of oxide notching and degraded alloy microstructure in remarkably premature failure of steam generator tubes
Wang et al. Effect of Carbon on Stress-Relief Cracking Susceptibility of T23 Steel
Liu et al. Failure Analysis on Explosion of High Temperature Superheater Tube for Supercritical Boiler

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
RJ01 Rejection of invention patent application after publication

Application publication date: 20180327

RJ01 Rejection of invention patent application after publication