CN109112413B - A kind of 12Cr1MoV Mayari and its production technology - Google Patents
A kind of 12Cr1MoV Mayari and its production technology Download PDFInfo
- Publication number
- CN109112413B CN109112413B CN201811232906.0A CN201811232906A CN109112413B CN 109112413 B CN109112413 B CN 109112413B CN 201811232906 A CN201811232906 A CN 201811232906A CN 109112413 B CN109112413 B CN 109112413B
- Authority
- CN
- China
- Prior art keywords
- 12cr1mov
- steel
- mayari
- relaxation
- online
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- 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
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/005—Ferrite
-
- 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
- C21D2211/009—Pearlite
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 Steel (AREA)
Abstract
The present invention relates to a kind of 12Cr1MoV Mayari and its production technologies.By weight percentage, the chemical component of the heat resisting steel are as follows: C:0.08%~0.15%, Si:0.15%~0.30%, Mn:0.40%~0.60%, P :≤0.03%, S :≤0.03%, Cr:0.90%~1.10%, Mo:0.25%~0.35%, V:0.15%~0.28%, Als:0.025%~0.05%, remaining is Fe.The production technology of the heat resisting steel using the online lonneal of controlled rolling-relaxation-technique, can high efficiency, low cost the good ferrite of comprehensive performance+pearlite type 12Cr1MoV Mayari is prepared.The present invention studies influence of the microscopic structure to 12Cr1MoV steel mechanical property using the methods of metallographic microscope, scanning electron microscope, tension test, impact test using the 12Cr1MoV steel of the online lonneal technique preparation different microstructures of controlled rolling-relaxation-.
Description
Technical field
The invention belongs to iron and steel smelting technology fields, and in particular to a kind of 12Cr1MoV Mayari and its production work
Skill.
Background technique
12Cr1MoV steel series low-alloy heat resisting steel has good toughness, craftsmanship and weldability, its group when high-temperature service
It knits that the high-temperature behaviors such as stability, creep resisting ability, oxidation resistance are good, is usually used in the overheat that manufacture uses temperature≤580 DEG C
The steam turbines such as device, reheater, high-pressure bottle, main steam conduit, boiler manfacturing field key components and parts, mechanical property requirements
For ReL >=255MPa, 470MPa≤Rm≤640MPa, A >=21%, Akv >=47J.In order to meet heat-resisting components performance requirement,
12Cr1MoV steel generally uses hot rolling+normalizing+high tempering or controlled rolling and controlled cooling production technology.Organization type mainly has iron
Ferritic+granular bainite microstructure, ferrite+Dispersed precipitate granular carbide, if occur low-carbon lath beam bainite, martensite,
The microscopic structures such as retained austenite, tempering temperature raising can make the tissue breakdowns such as lath beam bainite, and dislocation density reduces, carbonization
Object is grown up roughening, is caused the strength of materials, toughness to reduce, is reduced the applied at elevated temperature performance of material.
Summary of the invention
In order to improve the production efficiency and its mechanical property of 12Cr1MoV Mayari, the present invention provides one kind
12Cr1MoV Mayari and its production technology.The production technology is using the online lonneal work of controlled rolling-relaxation-
Skill, can high efficiency, low cost the good ferrite of comprehensive performance+pearlite type 12Cr1MoV Mayari is prepared.This hair
The bright 12Cr1MoV steel using the online lonneal technique preparation different microstructures of controlled rolling-relaxation-, utilizes metallography microscope
The methods of mirror, scanning electron microscope, tension test, impact test and means research microscopic structure are to 12Cr1MoV steel mechanical property
The influence of energy.
The present invention adopts the following technical scheme:
A kind of 12Cr1MoV Mayari, by weight percentage, the change of the 12Cr1MoV Mayari
It studies and is divided into: C:0.08%~0.15%, Si:0.15%~0.30%, Mn:0.40%~0.60%, P :≤0.03%, S :≤
0.03%, Cr:0.90%~1.10%, Mo:0.25%~0.35%, V:0.15%~0.28%, Als:0.025%~
0.05%, remaining is Fe.
The microscopic structure of the 12Cr1MoV Mayari is ferrite+pearlite+granular carbide.
The 12Cr1MoV Mayari with a thickness of 6.0~8.0mm.
The present invention also provides a kind of production technology of 12Cr1MoV Mayari, the production technology is using control
The technique of the online lonneal of rolling-relaxation-processed.
In the technique of the online lonneal of the rolling-relaxation-, austenitizing technique is 1200 DEG C and maintains 2 hours, finish to gauge
Temperature is 830~885 DEG C, and relaxation temperature is 710~760 DEG C, is cooled to 240~280 with the control of 8 DEG C/s~13 DEG C/s cooling rate
DEG C, 2h is kept the temperature, room temperature is then air-cooled to.
Beneficial effects of the present invention:
The present invention using controlled rolling-relaxation processing-online tempering process, can high efficiency, low cost preparation comprehensive performance it is good
Ferrite+pearlite type 12Cr1MoV Mayari.The present invention is using the online lonneal work of controlled rolling-relaxation-
Skill prepares the 12Cr1MoV steel of different microstructures, is tried using metallographic microscope, scanning electron microscope, tension test, impact
It the methods of tests and influence of the means research microscopic structure to 12Cr1MoV steel mechanical property.The study found that increasing sheet pearly-lustre
Body content, intensity, the hardness of 12Cr1MoV steel increase；Fining ferrite grains, increase granular carbide can significantly improve
The elongation of 12Cr1MoV steel；The granular carbide content for being distributed in ferrite grain boundaries increases, the impact flexibility of 12Cr1MoV steel
It is substantially reduced.Sheet content of pearlite in alloy, the content of granular carbide and distribution are to influence 12Cr1MoV Mayari power
Learn the principal element of performance.
Detailed description of the invention
Fig. 1 is the schematic diagram of the online lonneal technique of controlled rolling-relaxation-；
Fig. 2 is the microstructure picture of 12Cr1MoV Mayari, wherein figure (a) is metallographic structure photo, is schemed (b)
For SEM macrograph；
Fig. 3 is the granular carbide SEM photograph and EDS map of 12Cr1MoV Mayari, wherein figure (a) is along iron
Ferritic interface distributions granular carbide SEM photograph, figure (b) are granular carbide EDS map；
Fig. 4 is the metallographic structure photo of 12Cr1MoV Mayari, wherein figure (a) is the gold that embodiment 1 tests steel
Phase constitution photo, figure (b) are the metallographic structure photo that embodiment 2 tests steel, and figure (c) is the metallographic structure that embodiment 5 tests steel
Photo；
Fig. 5 is the pearlite and carbide volume fraction figure that embodiment 1-5 tests steel；
Fig. 6 is the ferritic structure average-size figure that embodiment 1-5 tests steel；
Fig. 7 tests the mechanical experimental results figure of steel for embodiment 1-5, wherein figure (a) is experiment steel yield strength, resists
The test result figure of tensile strength, figure (b) are the test result figure for testing steel elongation, and figure (c) is experiment steel impact absorbing energy
Test result figure, figure (d) are the test result figure for testing steel hardness.
Specific embodiment
Below in conjunction with drawings and examples, a specific embodiment of the invention is described in more details, so as to energy
The advantages of enough more fully understanding the solution of the present invention and its various aspects.However, specific embodiments described below and reality
It applies example to be for illustrative purposes only, rather than limiting the invention.
In following embodiment, the main chemical compositions of 12Cr1MoV experiment steel used are as follows: by weight percentage, C:
0.08%~0.15%, Si:0.15%~0.30%, Mn:0.40%~0.60%, P :≤0.03%, S :≤0.03%, Cr:
0.90%~1.10%, Mo:0.25%~0.35%, V:0.15%~0.28%, Als:0.025%~0.05%, remaining is
Fe。
In following embodiment, 12Cr1MoV tests steel processing and test method are as follows: intercepts 10mm along experiment steel transverse direction
× 10mm × thickness metallographic specimen inlays grinding, polishing after sample, is corroded with 3% nital, using Leica DMI 8C
Type inverted metallurgic microscope observation analysis microscopic structure uses transversal using Photoshop software statistics microscopic structure volume fraction
The size of method measurement crystal grain；Analysis experiment steel microscopic structure and micro- is further looked at using quanta200 scanning electron microscope (contain EDS)
Area's ingredient；Longitudinal plate stretching is carried out according to GB/T228.1-2010 standard using WDW-200 microcomputer controlled electronic universal tester
Test, sample marking distance 80mm；Semi-automatic shock machine is controlled according to GB/T 229-2007 standard using JB-W300B microcomputer
Side knock performance, size of sample are 10 × 5 × 55mm V-notch to test experiments steel at room temperature；It is micro- hard using HVS-1000
The hardness of degree meter measurement experiment steel.
Embodiment 1
It is used in certain factory's hot rolling line using the online lonneal technique preparation 12Cr1MoV experiment of controlled rolling-relaxation-
Steel, the online lonneal technique of the rolling-relaxation-is as shown in Figure 1, wherein hot incoming slab is with a thickness of 210mm, austenitizing
Technique is 1200 DEG C of maintenance 2h, and finishing temperature is 885 DEG C, and relaxation temperature is 760 DEG C, with the control of 8 DEG C/s~13 DEG C/s cooling rate
240~280 DEG C are cooled to, 2h is kept the temperature, is then air-cooled to room temperature, experiment steel product obtained is with a thickness of 8mm.
Embodiment 2
It is used in certain factory's hot rolling line using the online lonneal technique preparation 12Cr1MoV experiment of controlled rolling-relaxation-
Steel, the online lonneal technique of the rolling-relaxation-is as shown in Figure 1, wherein hot incoming slab is with a thickness of 210mm, austenitizing
Technique is 1200 DEG C of maintenance 2h, and finishing temperature is 885 DEG C, and relaxation temperature is 730 DEG C, with the control of 8 DEG C/s~13 DEG C/s cooling rate
240~280 DEG C are cooled to, 2h is kept the temperature, is then air-cooled to room temperature, experiment steel product obtained is with a thickness of 8mm.
Embodiment 3
It is used in certain factory's hot rolling line using the online lonneal technique preparation 12Cr1MoV experiment of controlled rolling-relaxation-
Steel, the online lonneal technique of the rolling-relaxation-is as shown in Figure 1, wherein hot incoming slab is with a thickness of 210mm, austenitizing
Technique is 1200 DEG C of maintenance 2h, and finishing temperature is 885 DEG C, and relaxation temperature is 710 DEG C, with the control of 8 DEG C/s~13 DEG C/s cooling rate
240~280 DEG C are cooled to, 2h is kept the temperature, is then air-cooled to room temperature, experiment steel product obtained is with a thickness of 8mm.
Embodiment 4
It is used in certain factory's hot rolling line using the online lonneal technique preparation 12Cr1MoV experiment of controlled rolling-relaxation-
Steel, the online lonneal technique of the rolling-relaxation-is as shown in Figure 1, wherein hot incoming slab is with a thickness of 250mm, austenitizing
Technique is 1200 DEG C of maintenance 2h, and finishing temperature is 830 DEG C, and relaxation temperature is 730 DEG C, with the control of 8 DEG C/s~13 DEG C/s cooling rate
240~280 DEG C are cooled to, 2h is kept the temperature, is then air-cooled to room temperature, experiment steel product obtained is with a thickness of 6mm.
Embodiment 5
It is used in certain factory's hot rolling line using the online lonneal technique preparation 12Cr1MoV experiment of controlled rolling-relaxation-
Steel, the online lonneal technique of the rolling-relaxation-is as shown in Figure 1, wherein hot incoming slab is with a thickness of 250mm, austenitizing
Technique is 1200 DEG C of maintenance 2h, and finishing temperature is 830 DEG C, and relaxation temperature is 750 DEG C, with the control of 8 DEG C/s~13 DEG C/s cooling rate
240~280 DEG C are cooled to, 2h is kept the temperature, is then air-cooled to room temperature, experiment steel product obtained is with a thickness of 6mm.
Experimental results
(1) 12Cr1MoV tests steel microscopic structure
As shown in Fig. 2, preparing the microscopic structure of 12Cr1MoV experiment steel using the online tempering process of controlled rolling-relaxation-
For isometric ferrite+pearlite+granular carbide, medium pearlite is sheet；As shown in Fig. 3 (a), 12Cr1MoV tests steel
In granular carbide along ferrite interface distributions.Fig. 3's (b) the result shows that 12Cr1MoV experiment steel in carbide it is main at
It is divided into Fe, Cr, Mo, V and C, it is known that the carbide in experiment steel mainly includes M3C and MC.
As shown in figure 4, the metallographic microstructure of experiment steel prepared under different process is ferrite+sheet pearly-lustre
Body+granular carbide.Ferritic volume fraction difference is little in each experiment steel, but ferritic size, pearlite morphology, grain
Shape carbide has larger difference.The experiment steel ferrite grain size of embodiment 1 is relatively fine, sheet content of pearlite in alloy is more and divides
Cloth is more uniform, and there are more granular carbides at ferrite interface；Embodiment 2 tests steel ferrite crystal grain and sheet pearlite
Size is coarseer, and content and embodiment 1 experiment the steel difference of pearlite are little, and the content of granular carbide is less than embodiment 1
Sample；Embodiment 5 tests steel medium pearlite content, ferrite size is less than embodiment 1 and tests steel, and granular carbide is distributed more
Uniformly, sheet content of pearlite in alloy is few, and granular carbide content is most.
Ferrite volume fraction and its average-size, carbide in experiment steel have been counted using area-method and division lines method respectively
Volume fraction, the results showed that for five kinds of ferritic volume fraction ranges of experiment steel between 87%~89%, difference is unobvious, and
Ferritic crystallite dimension difference is larger, and as shown in Figure 5 and Figure 6, the experiment steel ferrite crystal grain of embodiment 5 is most thin, average-size
About 6.83 μm, the experiment steel ferrite crystal grain of embodiment 3 is most coarse, and about 12.17 μm of average-size；Embodiment 1-3 tests steel middle layer
Shape content of pearlite in alloy is 9.0%~10.0%, and embodiment 4-5 tests steel laminate content of pearlite in alloy about 4.5%~6.0%, and
Granular carbide content is significantly more than embodiment 1-3 experiment steel in embodiment 4-5 experiment steel, and wherein embodiment 5 tests grain in steel
Shape carbide content about 6.31%, embodiment 3 test granular carbide content about 2.11% in steel.
(2) 12Cr1MoV tests steel mechanical property
Plate stretching and impact test are carried out to experiment steel at room temperature, test 12Cr1MoV tests the mechanical property of steel, as a result
As shown in table 1, wherein room temperature impact function experimental result has been converted into 10 × 10 × 55mm V-notch Standard run results, performance
Test result shows that five kinds of prepared experiment steel mechanical properties meet design requirement, but tests the mechanical property of steel because micro-
Difference is organized there are larger difference, such as elongation, hardness, toughness, microscopic structure statistical data shows in five kinds of experiment steel
Ferritic structure volume fraction difference is unobvious, so the pattern of ferrite grain size, pearlite, carbide content etc.
It is the principal element for influencing experiment steel mechanical property, as a result as shown in fig. 7, embodiment 4, embodiment 5 and embodiment 1-3 test steel
It compares, tensile strength and yield strength are lower, and room temperature impact value is significant lower, and elongation after fracture is significantly higher, and implement
The microhardness of example 1-5 experiment steel gradually decreases.
The mechanical property of 1 12Cr1MoV of table experiment steel
Test result show embodiment 1-3 experiment steel in sheet pearlite volume fraction it is higher, intensity, hardness compared with
Height, and plasticity is lower, influence of the granular carbide to experiment hardness of steel, hardness and plasticity is unobvious；Embodiment 4-5 is tested in steel
Granular carbide content is more, sheet content of pearlite in alloy is few, and ballistic work is lower；According to metal material refined crystalline strengthening theory (Hall-
Petch formula), intensity, hardness, plasticity and the toughness for testing steel should be refined with ferrite grain size and be improved, but real
The mechanical property changing rule for testing steel is not obviously consistent with ferrite grain size changing rule, and embodiment 5 tests iron element in steel
Body size is most tiny, and granular carbide is most, and intensity and impact flexibility are minimum, it can thus be appreciated that sheet content of pearlite in alloy is to reality
Test hardness of steel, the influence of hardness is greater than the influence of fetrite grain refinement, granular carbide and sheet pearlite are to influence
Test the principal element of steel plasticity and toughness.Yan Wei et al. is in " influence of the pearlitic spheroidization to 20G tensile mechanical properties " (" pressure
Force container ", 2003, the 8th phase of volume 20) in a text studies have shown that granular carbide is to the inhibition (dislocation of dislocation motion
Fill in product module type) it is small compared with sheet pearlite, sheet content of pearlite in alloy is more, and the tensile strength and yield strength of material are higher,
Carbide can increase uniformity when material deformation, drop stress concentration, be conducive to mention in spherical, ferrite crystal grain is tiny
The plasticity of high material.However embodiment 4, embodiment 5 experiment steel laminate content of pearlite in alloy are few, granular carbide content is more, iron
Ferritic crystallite dimension is tiny, and impact flexibility is lower instead, and main cause is that granular carbide is present in ferrite grain boundaries, can drop
Lower bound surface intensity accelerates crackle to extend along crystal boundary, reduces impact flexibility.
In terms of comprehensive, the present invention can high efficiency, low cost preparation synthesis using controlled rolling-relaxation processing-online tempering process
Ferrite of good performance+pearlite type 12Cr1MoV Mayari.The present invention is online low using controlled rolling-relaxation-
The 12Cr1MoV steel of warm tempering process preparation different microstructures, has studied microscopic structure to 12Cr1MoV steel room-temperature mechanical property
Influence.The result shows that 12Cr1MoV steel mechanical property is by sheet content of pearlite in alloy, granular carbide content and distribution, iron
Ferritic crystallite dimension combined influence.Lamellar pearlite is the principal element for guaranteeing ferrite+pearlite type hardness of steel, hardness, is increased
Add sheet content of pearlite in alloy, intensity, the hardness of 12Cr1MoV steel increase.And fining ferrite grains, reduction sheet pearly-lustre
Body increases an important factor for granular carbide is guarantee material plasticity, and fining ferrite grains, increase granular carbide obviously mention
The elongation of high 12Cr1MoV steel.Granular carbide along ferrite interface distributions can reduce the impact flexibility of material, intensity, point
Cloth increases in the granular carbide content of ferrite grain boundaries, and the impact flexibility of 12Cr1MoV steel is substantially reduced.Therefore, sheet pearl
Body of light content, the content of granular carbide and distribution are to influence the principal element of 12Cr1MoV low-alloy refractory steel mechanical property.
Claims (3)
1. a kind of 12Cr1MoV Mayari, it is characterised in that: by weight percentage, the 12Cr1MoV low-alloy is resistance to
The chemical component of hot steel are as follows: C:0.08%~0.15%, Si:0.15%~0.30%, Mn:0.40%~0.60%, P :≤
0.03%, S :≤0.03%, Cr:0.90%~1.10%, Mo:0.25%~0.35%, V:0.15%~0.28%, Als:
0.025%~0.05%, remaining is Fe；The microscopic structure of the 12Cr1MoV Mayari is ferrite+pearlite+grain
Shape carbide；The production technology of the 12Cr1MoV Mayari uses the work of the online lonneal of controlled rolling-relaxation-
Skill；In the technique of the online lonneal of the rolling-relaxation-, austenitizing technique is 1200 DEG C and maintains 2 hours, finishing temperature
It is 830~885 DEG C, relaxation temperature is 710~760 DEG C, 240~280 DEG C are cooled to the control of 8 DEG C/s~13 DEG C/s cooling rate,
2h is kept the temperature, room temperature is then air-cooled to.
2. 12Cr1MoV Mayari according to claim 1, it is characterised in that: the 12Cr1MoV low-alloy is resistance to
Hot steel with a thickness of 6.0~8.0mm.
3. the production technology of 12Cr1MoV Mayari described in any one of -2 according to claim 1, it is characterised in that:
The technique that the production technology uses the online lonneal of controlled rolling-relaxation-.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811232906.0A CN109112413B (en) | 2018-10-22 | 2018-10-22 | A kind of 12Cr1MoV Mayari and its production technology |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811232906.0A CN109112413B (en) | 2018-10-22 | 2018-10-22 | A kind of 12Cr1MoV Mayari and its production technology |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109112413A CN109112413A (en) | 2019-01-01 |
| CN109112413B true CN109112413B (en) | 2019-11-15 |
Family
ID=64855263
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811232906.0A Active CN109112413B (en) | 2018-10-22 | 2018-10-22 | A kind of 12Cr1MoV Mayari and its production technology |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109112413B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109930064B (en) * | 2019-03-11 | 2020-09-22 | 江苏利淮钢铁有限公司 | Corrosion-resistant heat-resistant steel for high-pressure boiler pipe and production method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102269756A (en) * | 2011-08-01 | 2011-12-07 | 嘉兴市特种设备检测院 | Field test method of 12Cr1MoV steel pearlite nodularization level |
| CN104775078A (en) * | 2015-03-13 | 2015-07-15 | 武汉钢铁(集团)公司 | Low yield ratio steel (Rel>620MPa) for fireproof structure and production method thereof |
| CN107099752A (en) * | 2017-03-23 | 2017-08-29 | 舞阳钢铁有限责任公司 | A kind of low-alloy 12Cr1MoV steel plates and its production method |
| CN108411200A (en) * | 2018-04-02 | 2018-08-17 | 武汉科技大学 | A kind of high work hardening rate hot rolling Q＆P steel plates and preparation method thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3480061B2 (en) * | 1994-09-20 | 2003-12-15 | 住友金属工業株式会社 | High Cr ferritic heat resistant steel |
-
2018
- 2018-10-22 CN CN201811232906.0A patent/CN109112413B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102269756A (en) * | 2011-08-01 | 2011-12-07 | 嘉兴市特种设备检测院 | Field test method of 12Cr1MoV steel pearlite nodularization level |
| CN104775078A (en) * | 2015-03-13 | 2015-07-15 | 武汉钢铁(集团)公司 | Low yield ratio steel (Rel>620MPa) for fireproof structure and production method thereof |
| CN107099752A (en) * | 2017-03-23 | 2017-08-29 | 舞阳钢铁有限责任公司 | A kind of low-alloy 12Cr1MoV steel plates and its production method |
| CN108411200A (en) * | 2018-04-02 | 2018-08-17 | 武汉科技大学 | A kind of high work hardening rate hot rolling Q＆P steel plates and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109112413A (en) | 2019-01-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Li et al. | Microstructure and mechanical properties of an ultrahigh-strength 40SiMnNiCr steel during the one-step quenching and partitioning process | |
| Hanzaki et al. | Retained austenite characteristics in thermomechanically processed Si-Mn transformation-induced plasticity steels | |
| JPWO2007058364A1 (en) | Steel for warm working, warm working method using the steel, and steel and steel parts obtained thereby | |
| Zhang et al. | Evolution of microstructure and mechanical properties of 9Cr ferrite/martensite steels with different Si content after long-term aging at 550° C | |
| CN110628993A (en) | HB460 MPa-grade high-strength high-toughness fire-cut crack-resistant wear-resistant steel and production method thereof | |
| Mu et al. | Influences of hot stamping parameters on mechanical properties and microstructure of 30MnB5 and 22MnB5 quenched in flat die | |
| Carvalho et al. | Development of a complex multicomponent microstructure on commercial carbon-silicon grade steel by governing the phase transformation mechanisms to design novel quenching and partitioning processing | |
| CN109112413B (en) | A kind of 12Cr1MoV Mayari and its production technology | |
| Jabłońska et al. | A study of mechanical properties of high manganese steels after different rolling conditions | |
| Güler et al. | Influence of heat treatment parameters on the microstructure and mechanical properties of boron-alloyed steels | |
| Du et al. | Coupled effects of banded structure and carbide precipitation on mechanical performance of Cr–Ni–Mo–V steel | |
| Ding et al. | Enhanced strength-plasticity matching of lamellar 1 GPa-grade dual-phase steels via cyclic intercritical quenching | |
| Xia et al. | Cyclic deformation behaviours of 18Mn3Si2CrNiMo multiphase (martensite/bainite/retained austensite) steel | |
| Singh et al. | Grain refinement, strain hardening and fracture in thermomechanically processed ultra-strong microalloyed steel | |
| Sun et al. | Quantitative evaluation of the contribution of carbide-free bainite, lath martensite, and retained austenite on the mechanical properties of C-Mn-Si high-strength steels | |
| Ibrahim | Comparison of impact properties for carbon and low alloy steels | |
| CN109837367A (en) | Refine the heat treatment process on the island M-A in low-carbon low-alloy steel granular bainite microstructure | |
| Rojacz et al. | Deformation and strain hardening of different steels in impact dominated systems | |
| Güler et al. | Effect of heat treatment on the microstructure and mechanical properties of 30MnB5 boron steel | |
| Yao et al. | Investigation on Microstructure and Properties of Low‐Carbon Wear‐Resistant Steels with Addition of Cr and Ni | |
| Pang et al. | Complex precipitation mechanism of Ti-Nb-V microalloyed bainitic base high strength steel | |
| Zhao et al. | Effect of Secondary Welding Thermal Cycle Peak Temperature on Microstructure and Properties in Simulated Reheat Coarse Grain Heat Affected Zone of High Strength Medium-Mn Steel | |
| Wang et al. | The effect of peak temperature on HAZ microstructure and toughness of V-and Nb-bearing microalloyed steels | |
| Alza | Isothermal treatment at low temperatures applied to aisi 4340 steel: effects on hardness, toughness and microstructure | |
| Li et al. | The Ductile-Brittle Transition Mechanism of 15MnTi Steel Under Dynamic Loading |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |