CN108754079A - It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy - Google Patents
It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy Download PDFInfo
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- CN108754079A CN108754079A CN201810606569.0A CN201810606569A CN108754079A CN 108754079 A CN108754079 A CN 108754079A CN 201810606569 A CN201810606569 A CN 201810606569A CN 108754079 A CN108754079 A CN 108754079A
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials 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 the heat treatment methods that nano-carbide in a kind of promotion steel containing W alloy is precipitated.Its technical solution is：First by steel billet under the conditions of 1100~1200 DEG C 24~48h of soaking, with being furnace-cooled to room temperature.20~40min of austenitizing under the conditions of 850~1000 DEG C, in cryosel quenching-in water.Then it is 10 in vacuum degree‑3~10‑2To be heated to 650~750 DEG C under the conditions of 10~14T with the speed of 3~7 DEG C/min, 0.5~3.0h of isothermal is cooled to room temperature for Pa and magnetic field intensity.The chemical composition of the steel billet is：C is 0.06~0.14wt%, and W is 1.50~3.00wt%, P<0.01wt%, S<0.005wt%, remaining is Fe and inevitable impurity.The temperature of the brine ice is -3~-1 DEG C.Present invention process is simple, at low cost and with short production cycle, is significantly improved with the intensity of this method treated steel containing W alloy.
Description
Technical field
The invention belongs to the technical fields of Carbide Precipitation in steel containing W alloy.More particularly in a kind of promotion steel containing W alloy
The heat treatment method that nano-carbide is precipitated.
Background technology
Unimach is made by alloying, heat treatment and cold and hot working technique on the basis of structural alloy steel
Superhigh intensity, high-ductility and excellent toughness steel material, intensity can be significantly improved, while keeping good plasticity and toughness,
Its tensile strength >=1500MPa (or yield strength >=1380MPa).With greatly improving for steel material research level, surpass
High strength steel has become using the very wide important steel material of one kind, such as undercarriage peace tailing axle, panzer
Armour plate, the bogie of big machinery, the engine housing etc. of rocket some special dimensions.And its application range is gradual
It is expanded to the fields such as off-lying sea deep-sea platform, military equipment, mining machinery, Vehicle Engineering and architectural engineering.High intensity knot of new generation
Structure steel had both needed to meet superpower toughness while superhigh intensity again, so proposing huge challenge to the exploitation of steel grade.
Secondery-hardening Ultrahigh Strength Steel, process characteristic are by quenching-tempering, quenching-carbon distribution or quenching-carbon point
With-tempering etc. techniques, by diffusion-precipitation be distributed alloy carbide generate precipitation strength effect, so that intensity and hardness is obviously carried
Height, while toughness is also improved.But the content of the alloying elements such as precious metal Ni, Co therein is very high, makes production cost
It is very expensive.
Precipitation strength type superhigh intensity steel grade has superhigh intensity, while also having had both excellent plasticity and toughness, wide
It is general to be applied to the numerous areas such as armour steel, armour plate, bearing steel.Scientific and technical personnel have made a large amount of R&D work, such as：
" a kind of 900MPa grades of hot rolling nanometer precipitation strength type high-strength and high-toughness steel and its manufacturing method " (CN108004475A) patented technology,
The patented technology is bainite+Nano-Scaled Carbide by adding the expensive alloying elements such as Nb, Ti, Mo, V to obtain microscopic structure
Tissue, 900MPa grades of hot rolling nanometer precipitation strength type high-strength and high-toughness steels are made, but its alloying component is complicated, with high costs and hot
Complex treatment process.For another " strength type martensite steel and its manufacturing method " (CN104271787A) patented technology, this is specially
Pass through the conjunctions such as the Ni (7.5~11.0%), Cr (10.5~13.5%), Mo (1.75~2.5%) of addition high-content in sharp technology
Gold element, this kind of steel are also to realize superperformance by the precipitation of second phase particles, so that intensity is increased, but alloying element added
It is more, thus it is with high costs, while its heat treatment time is up to multiple hours, low production efficiency.
Invention content
The present invention is directed to overcome the deficiencies in the prior art, it is therefore an objective to provide a kind of simple for process, at low cost and production cycle
The heat treatment method that nano-carbide is precipitated in short promotion steel containing W alloy, this method can improve the intensity of the steel containing W alloy.
To achieve the above object, the technical solution adopted by the present invention is：It is first that steel billet is equal under the conditions of 1100~1200 DEG C
24~48h of heat, with being furnace-cooled to room temperature；20~40min of austenitizing under the conditions of 850~1000 DEG C, in cryosel quenching-in water；
Then it is 10 in vacuum degree-3~10-2Pa and magnetic field intensity with the speed of 3~7 DEG C/min are heated to 650 under the conditions of being 10~14T
~750 DEG C, 0.5~3.0h of isothermal is cooled to room temperature.
The chemical composition of the steel billet is：C is 0.06~0.14wt%, and W is 1.50~3.00wt%, P<0.01wt%, S
<0.005wt%, remaining is Fe and inevitable impurity.
The temperature of the brine ice is -3~-1 DEG C.
Due to the adoption of the above technical scheme, the present invention has following good effect compared with prior art：
1, heat treatment method of the invention is so that its alloying element is cmpletely spread by steel billet after high-temperature homogenization,
Banded structure when hot rolling is eliminated, nonuniform organization is avoided.Then water quenching after austenitizing obtains lath martensite, finally again
Lath martensite is placed in strong magnetic field circumstance and carries out tempering heat treatment, heat treatment process is simple, greatly shortens production
Period improves production efficiency.
2, the present invention is only added to a kind of alloying element W by rational Alloying Design, compared to other patents using multiple
Miscellaneous high a variety of alloying elements realize the carbide of Dispersed precipitate, greatly reduce cost.Secondly low-carbon, high tungsten is selected to close
Gold further realizes the high temperature creep strength under strong magnetic field circumstance.Alloy carbide (M7C3, M23C6, M6C etc.) it is in heat resisting steel
Important composition phase, be precipitated with develop have extremely important influence to the high temperature creep property of the heat resisting steel such as low activation steel.
M23C6Type carbide is easy to be roughened in grain boundaries during high-temperature service, and M can be reduced by reducing C content23C6In the roughening of grain boundaries,
The M of grain boundaries can be stablized by improving W content23C6And solution strengthening effect is improved, so that the intensity of the steel containing W alloy is improved.
3, during high-intensity magnetic field is applied to temper containing W by the present invention, manufacture is a large amount of disperses of the ferrite for matrix
It is distributed the tissue of nano-scaled precipitate particle.The application of high-intensity magnetic field causes phase driving force to increase, and the forming core barrier of carbide is made to subtract
It is low, increase the nucleation rate of carbide.During not adding magnetic field in tempering, precipitate particle surface density is about 22.9%,
Precipitation size is 5~15nm, and after applying magnetic field, size, which is precipitated, to be basically unchanged, but precipitation particles surface density increases to 31.6%,
Increasing about 39% when than not applying magnetic field, it is seen that the precipitation of nano-carbide during temper containing W is greatly facilitated in high-intensity magnetic field,
Precipitation strength effect is enhanced, the intensity of the steel containing W alloy is made to improve.
Therefore, present invention process is simple, at low cost and with short production cycle, strong with this method treated steel containing W alloy
Degree significantly improves.
Description of the drawings
Fig. 1 is the transmission electron microscope that the nano-carbide of steel containing W alloy that a kind of heat treatment method of the present invention obtains is precipitated
Figure；
Fig. 2 is the transmission electron microscope that the nano-carbide of steel containing W alloy that Fig. 1 the methods obtain under no magnetic field condition is precipitated
Figure；
Fig. 3 is the transmission electricity that the nano-carbide of steel containing W alloy that another heat treatment method of the present invention obtains is precipitated
Mirror figure；
Fig. 4 is the transmission electron microscope that the nano-carbide of steel containing W alloy that Fig. 3 the methods obtain under no magnetic field condition is precipitated
Figure.
Specific implementation mode
The invention will be further described with reference to the accompanying drawings and detailed description, not to the scope of the present invention
Limitation.
Embodiment 1
It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy, first by steel billet at 1100~1150 DEG C
Under the conditions of 36~48h of soaking, with being furnace-cooled to room temperature.20~30min of austenitizing under the conditions of 900~1000 DEG C, in cryosel
The temperature of quenching-in water, the brine ice is -3~-1 DEG C.Then it is 10 in vacuum degree-3~10-2Pa and magnetic field intensity be 10~
700~750 DEG C are heated to the speed of 3~7 DEG C/min under the conditions of 13T, 0.5~2.5h of isothermal is cooled to room temperature.
The chemical composition of the steel billet is：C is 0.06~0.12wt%, and W is 1.50~2.50wt%, P<0.01wt%, S
<0.005wt%, remaining is Fe and inevitable impurity.
Fig. 1 is a kind of transmission electron microscope picture that the steel containing W alloy that heat treatment method obtains nanometer is precipitated, figure described in the present embodiment
2 be the transmission electron microscope that remaining is precipitated with the nanometer of steel containing W alloy obtained under Fig. 1 the method the same terms in addition to no high-intensity magnetic field
Figure.
Wherein：Black nano particle is M6C-type carbide.Known by the comparison of Fig. 1 and Fig. 2, applies the magnetic fields 12T and be tempered
In the product of heat treatment, nano-carbide is precipitated quantity and obviously increases, and Carbide Precipitation surface density increases compared with no magnetic-field heat treatment
About 39%, illustrate to apply the nucleation rate that high-intensity magnetic field significantly increases carbide, enhance precipitation strength effect, makes to contain W alloy
The intensity of steel significantly improves.
Embodiment 2
It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy, first by steel billet at 1150~1200 DEG C
Under the conditions of 24~36h of soaking, with being furnace-cooled to room temperature.30~40min of austenitizing under the conditions of 850~950 DEG C, in brine ice
The temperature of middle quenching, the brine ice is -3~-1 DEG C.Then vacuum degree is 10-3~10-2Pa and magnetic field intensity are 11~14T
Under the conditions of with the speed of 3~7 DEG C/min be heated to 650~700 DEG C, 1.0~3.0h of isothermal is cooled to room temperature.
The chemical composition of the steel billet is：C is 0.08~0.14wt%, and W is 2.00~3.00wt%, P<0.01wt%, S
<0.005wt%, remaining is Fe and inevitable impurity.
Fig. 3 is a kind of transmission electron microscope picture that the steel containing W alloy that heat treatment method obtains nanometer is precipitated, figure described in the present embodiment
4 be the transmission electron microscope that remaining is precipitated with the nanometer of steel containing W alloy obtained under Fig. 3 the method the same terms in addition to no high-intensity magnetic field
Figure.
Wherein：Black nano particle is M6C-type carbide.Known by the comparison of Fig. 3 and Fig. 4, applies the magnetic fields 12T and be tempered
In the product of heat treatment, nano-carbide is precipitated quantity and obviously increases, and Carbide Precipitation surface density increases compared with no magnetic-field heat treatment
About 55%, illustrate to apply the nucleation rate that high-intensity magnetic field significantly increases carbide, enhance precipitation strength effect, makes to contain W alloy
The intensity of steel significantly improves.
Present embodiment has following good effect compared with prior art：
1, the heat treatment method of present embodiment is so that its alloying element is filled completely by steel billet after high-temperature homogenization
Divide diffusion, eliminates banded structure when hot rolling, avoid nonuniform organization.Then water quenching after austenitizing, obtains lath martensite,
Last lath martensite is placed in strong magnetic field circumstance again carries out tempering heat treatment, and heat treatment process is simple, contracts significantly
Short production cycle improves production efficiency.
2, present embodiment is only added to a kind of alloying element W by rational Alloying Design, specially compared to other
Profit realizes the carbide of Dispersed precipitate using complicated high a variety of alloying elements, greatly reduces cost.Secondly it selects low
Carbon, high-tungsten alloy further realize the high temperature creep strength under strong magnetic field circumstance.Alloy carbide (M7C3, M23C6, M6C etc.)
It is the important composition phase in heat resisting steel, precipitation has the high temperature creep property of the heat resisting steel such as low activation steel with differentiation of crucial importance
Influence.M23C6Type carbide is easy to be roughened in grain boundaries during high-temperature service, and M can be reduced by reducing C content23C6In grain boundaries
Roughening, the M of grain boundaries can be stablized by improving W content23C6And solution strengthening effect is improved, so that the intensity of the steel containing W alloy is improved.
3, during high-intensity magnetic field is applied to temper containing W by present embodiment, manufacture be ferrite be matrix
The tissue of a large amount of Dispersed precipitate nano-scaled precipitate particles.The application of high-intensity magnetic field causes phase driving force to increase, and makes the shape of carbide
Core barrier lowers, and increases the nucleation rate of carbide.During not adding magnetic field in tempering, precipitate particle surface density is about
22.9%, precipitation size is 5~15nm, and after applying magnetic field, size, which is precipitated, to be basically unchanged, but precipitation particles surface density increases to
31.6%, increase about 39% when than not applying magnetic field, it is seen that nano-carbide during temper containing W is greatly facilitated in high-intensity magnetic field
Precipitation, enhance precipitation strength effect, so that the intensity of the steel containing W alloy is improved.
Therefore, present embodiment is simple for process, at low cost and with short production cycle, and with this method, treated containing W conjunctions
The intensity of Jin Gang significantly improves.
Claims (2)
1. a kind of promoting the heat treatment method that nano-carbide is precipitated in steel containing W alloy, it is characterised in that：First by steel billet 1100
24~48h of soaking under the conditions of~1200 DEG C, with being furnace-cooled to room temperature；Under the conditions of 850~1000 DEG C austenitizing 20~
40min, in cryosel quenching-in water；Then it is 10 in vacuum degree-3~10-2Pa and magnetic field intensity be 10~14T under the conditions of with 3~7
DEG C/speed of min is heated to 650~750 DEG C, 0.5~3.0h of isothermal is cooled to room temperature；
The chemical composition of the steel billet is：C is 0.06~0.14wt%, and W is 1.50~3.00wt%, P<0.01wt%, S<
0.005wt%, remaining is Fe and inevitable impurity.
2. promoting the heat treatment method that nano-carbide is precipitated in steel containing W alloy according to claim 1, it is characterised in that institute
The temperature for stating brine ice is -3~-1 DEG C.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810606569.0A CN108754079A (en) | 2018-06-13 | 2018-06-13 | It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy |
| US16/413,589 US20190382859A1 (en) | 2018-06-13 | 2019-05-15 | Heat treatment method for accelerating precipitation of nanoscale carbides in w-containing alloy steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810606569.0A CN108754079A (en) | 2018-06-13 | 2018-06-13 | It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy |
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| Publication Number | Publication Date |
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| CN108754079A true CN108754079A (en) | 2018-11-06 |
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ID=64022414
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| CN201810606569.0A Pending CN108754079A (en) | 2018-06-13 | 2018-06-13 | It is a kind of to promote the heat treatment method that nano-carbide is precipitated in steel containing W alloy |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110066955A (en) * | 2019-05-24 | 2019-07-30 | 东北大学 | A kind of twinning induced plasticity steel and preparation method thereof |
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| JPS61237328A (en) * | 1985-04-11 | 1986-10-22 | Denki Kagaku Kogyo Kk | Ion source structure by alloy including liquid boron |
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2018
- 2018-06-13 CN CN201810606569.0A patent/CN108754079A/en active Pending
-
2019
- 2019-05-15 US US16/413,589 patent/US20190382859A1/en not_active Abandoned
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| JPS61237328A (en) * | 1985-04-11 | 1986-10-22 | Denki Kagaku Kogyo Kk | Ion source structure by alloy including liquid boron |
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| CN1861825A (en) * | 2006-05-27 | 2006-11-15 | 中国科学院等离子体物理研究所 | Structure steel material suitable for fusion reactor |
| CN106148659A (en) * | 2015-04-17 | 2016-11-23 | 中国科学院金属研究所 | A kind of preparation technology of high-strength plasticity Ultra-fine Grained low activation ferrite/martensite steel |
| CN105274440A (en) * | 2015-11-20 | 2016-01-27 | 北京科技大学 | Oxide dispersion strengthened (ODS) steel preparing method and martensitic steel |
| CN105925892A (en) * | 2016-06-21 | 2016-09-07 | 宝山钢铁股份有限公司 | 780 MPa-grade hot-rolled high-reaming dual-phase steel and manufacturing method thereof |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110066955A (en) * | 2019-05-24 | 2019-07-30 | 东北大学 | A kind of twinning induced plasticity steel and preparation method thereof |
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