CN105463307B - A kind of Q＆P steel with gradient structure and preparation method thereof - Google Patents
A kind of Q＆P steel with gradient structure and preparation method thereof Download PDFInfo
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- CN105463307B CN105463307B CN201510820758.4A CN201510820758A CN105463307B CN 105463307 B CN105463307 B CN 105463307B CN 201510820758 A CN201510820758 A CN 201510820758A CN 105463307 B CN105463307 B CN 105463307B
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
- C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a kind of Q＆P steel with gradient structure, it is made up of the element of following weight percent content：C：0.14 0.29%, Si：1.1 2.8%, Mn：1.8 3.0%, Cr：0.5 1.9%, Al：1.5 3.1%, S：≤ 0.01%, P：≤ 0.01%, remaining is Fe.Its preparation method includes：Austenitizing, carburizing, quenching, temper carbon distribution, quenching Step.The present invention can ensure technology stability and tissue gradient in large-size production, ensure that it has good toughness again while the intensity for increasing steel, and low alloying is with low cost.
Description
Technical field
The present invention relates to a kind of Q＆P steel with gradient structure and preparation method thereof, belong to technical field of metal material.
Background technology
In order to meet auto industry future development to lightweight and the double requirements of high safety, automobile steel is constantly to high intensity
Develop with high-ductility direction, strength and ductility product turns into the important indicator for weighing automobile Steel Properties.The strength and ductility product of first generation automotive sheet steel
Generally 15GPa%, lightweight and safety indexes are all very low；Although the strength and ductility product of second generation automobile steel has reached 50GPa%, its
Cost is higher, processing performance is poor and metallurgical production is difficult larger.So-called third generation automobile steel, refers to that lightweight and security refer to
Absolute altitude is less than the high-strength high plastic-steel of second generation automobile steel in first generation automobile steel, production cost again.
Q＆P steel is the third generation automobile steel with higher-strength and toughness grown up in recent years.Its general principle
It is：Containing Si or（With）Al steel part is first quenched to Ms ~ Mf after austenitizing（Ms is Ms (martensite start) point, and Mf is horse
Family name's body changes end temp）Between a certain temperature, that is, form a number of martensite and retained austenite, then initial at this
Hardening heat or a certain temperature of more than Ms stay for some time, and carbon is distributed from martensite to retained austenite, now geneva
Carbon content in body declines, the carbon content rise in austenite, so that retained austenite richness carbon and can stablize to room temperature, most
The complex tissue being made up of martensite and retained austenite is obtained afterwards, so as to obtain higher intensity and toughness, i.e., good is comprehensive
Close mechanical property.
In recent years, Xu ancestral shines academician on the basis of Q＆P techniques, makes full use of the microalloy elements such as Nb, V and Ti formation carbon
A kind of precipitation strength effect of compound, it is proposed that new Technology for Heating Processing：Quenching-partition-tempering process（Quenching-
Partitioning-Tempering, Q-P-T）.The technique introduces a drawing process after Q＆P processing, makes martensitic matrix
Upper precipitation complicated carbide, further to increase the intensity of steel.
However, with the development of auto industry, intensity and toughness to advanced high-strength steel propose higher and higher requirement.
Although resulting Q＆P steel intensity is higher, its plasticity is poor.Further, since its intensity is higher, its weldability largely reducing
Energy.Therefore, from improving the obdurability and weldability of steel, and from the point of view of economizing on resources, reducing cost, Q＆ is further improved
The combination property of P steel is significant.
Through the literature search discovery to prior art, Xu ancestral shines academician in International Heat Treatment
" Quenching-partitioning- is delivered on and Surface Engineering, 2008,2 (2), 64-68.
The texts of tempering (Q-P-T) process for ultra-high strength steel " one, elaborate quenching-carbon point
Principle with-tempering (Q-P-T) technique, what is utilized is Carbide Precipitation reinforcing to improve the intensity of steel, finally obtains geneva
The heterogeneous structure of body, retained austenite and carbide.It also found in retrieval, the China of Application No. 200810033295.7 is specially
Profit, the patent obtains the three-phase contexture of martensite, retained austenite and nanometer bainite, is obtained using low temperature long time treatment
Nanometer bainite further improve the comprehensive mechanical property of steel.Recently, J. G. Speer etc. are in Metallurgical
" Quenched and are delivered on and Materials Transactions A, 2011,42 (12), 3652-3659.
Partitioned Microstructures Produced via Gleeble Simulations of Hot-Strip
The text of Mill Cooling Practices " one, it is indicated that by improving the obdurability of Q＆P steel in high temperature hot rolling be effective, but
Macrostructure's distribution of steel part is not accounted for, gradient microscopic structure is not formed.
It also found in retrieval, the Chinese patent of Application No. 201110154249.4 discloses a kind of carbon silicomanganese system hot rolling
Q＆P steel and preparation method thereof.Material composition is C:1.5-2.5%,Si:1.3-1.8%,Mn:1.3-2.0%,S≤0.01%,P≤
0.01%, surplus is Fe.Through smelting, be forged into steel billet, hot rolling be finally obtained martensite, retained austenite microscopic structure.
The Chinese patent of Application No. 201310121568.4, discloses a kind of grade high-strength hot-rolled Q＆P steel of 700MPa and its manufacturer
Method, the invention is by rational composition design, on plain C-Mn steel component base, and cementite is suppressed by carrying high Si content
Separate out, micro- Ti handles fining austenite grains, improve the austenite transition kinetics that Al content accelerates process air cooler；Use simultaneously
Hot continuous rolling process coordinates sub-sectional cooling technique, obtains containing pro-eutectoid ferrite+martensite+retained austenite tissue.
The content of the invention
The present invention is intended to provide a kind of carburizing Q＆P steel that center portion plasticity is good, case hardness is high and preparation method thereof, and the steel
With gradient microscopic structure.
The invention provides a kind of Q＆P steel with gradient structure, consist of the following components in percentage by weight：
C：0.14-0.29%,
Si：1.1-2.8%,
Mn：1.8-3.0%,
Cr：0.5-1.9%,
Al：1.5-3.1%,
S：≤ 0.01%,
P：≤ 0.01%,
Remaining is Fe.
Further, the Q＆P steel with gradient structure, is consisted of the following components in percentage by weight：
C：0.15-0.28%,
Si：1.16-2.11%,
Mn：1.80-2.48%,
Cr：0.9-1.9%,
Al：1.6-3.0%,
S：≤ 0.01%,
P：≤ 0.01%,
Remaining is Fe.
Carbon content when wherein Cr and Al addition can increase intercritical annealing in austenite and reduce the Ms of the austenite
Temperature（Martensite transformation temperature）To lower temperature.
The invention provides a kind of preparation method of the above-mentioned Q＆P steel with gradient structure, mainly include the following steps that：
The first step, is heated rapidly to 800-1100 DEG C of austenitizing temperature by steel first, and isothermal 5-30min makes abundant Austria
Family name's body；
Second step, then carries out case-carbonizing, carburizing time is 10-50h at 700-900 DEG C, and whole carburizing process will be with
Nitrogen is carried out for atmosphere；
3rd step, rapid quenching to a certain hardening heat between Ms and Mf（200-500℃）, and in this temperature range
2-9h is incubated in inherent nitrogen atmosphere；
4th step, then in 300-600 DEG C of temperature, isothermal 5-600min carries out carbon distribution, make carbon from martensite to
Retained austenite is distributed, and now the carbon content in martensite declines, the carbon content rise in austenite, so that retained austenite
Rich carbon and it can stablize to room temperature；
5th step, is finally quenched into room temperature again, and the gradient complex phase group of stable martensite and retained austenite is obtained in room temperature
Knit.
The invention provides the preparation method of the preferred Q＆P steel with gradient structure, comprise the following steps：
The first step, is heated rapidly to 850-950 DEG C of austenitizing temperature by steel first, and isothermal 6-20min makes abundant Ovshinsky
Body；
Second step, then carries out case-carbonizing, carburizing time is 10-20h at 740-850 DEG C, and whole carburizing process will be with
Nitrogen is carried out for atmosphere；
3rd step, rapid quenching to a certain hardening heat between Ms and Mf（300-450℃）, and in this temperature range
2-4h is incubated in inherent nitrogen atmosphere；
4th step, then in 330-500 DEG C of temperature, isothermal 5-30min carries out carbon distribution, makes carbon from martensite to residual
Carbon content rise in remaining austenite distribution, now the carbon content decline in martensite, austenite, so that retained austenite is rich
Carbon and it can stablize to room temperature；
5th step, is finally quenched into room temperature again, and the gradient complex phase group of stable martensite and retained austenite is obtained in room temperature
Knit.
The invention provides a kind of low-alloy high-strength toughness Multiphase Steel and its heat treatment method for meeting large-scale production, adopt
With above-mentioned technical proposal, using the method for carburizing+quenching+carbon distribution, steel is set to obtain gradient heterogeneous structure.The present invention and tradition
Q＆P techniques are compared, and realize that carbon occurs in drawing process to be distributed with phase transformation design by carburizing and new alloy, the technology can
Ensure technology stability and tissue gradient in large-size production.
The present invention first has to ensure the high intensity of steel, and its matrix need to select martensitic structure, and the martensitic structure should
This is based on the thin lath martensite containing high density dislocation.Secondly, carbon is quenched by advanced Technology for Heating Processing to distribute（Q&P）Come
Make there are retained austenitic film between martensite lath.Final pair obtained containing dislocation type martensite and retained austenite
Phase complex tissue.The toughness of prepared steel is greatly improved and maintains higher intensity.Its high intensity derives from horse
The refined crystalline strengthening and dislocation strengthening of family name's body and complex tissue, good plasticity, which is derived from tissue, has appropriate retained austenite
With the softening of initial quenched martensite tissue, and the heterogeneous structure with gradient.
Beneficial effects of the present invention：
（1）The present invention is designed by new alloy and phase transformation and realizes higher strength and ductility product, by hardening heat control certain
In the range of, the technology can ensure technology stability and tissue gradient in large-size production；
（2）The surface of Q＆P steel prepared by the present invention is due to have passed through carburizing, and its surface texture is high carbon martensite and remnants
Austenite, its core structure is low-carbon martensite and retained austenite；
（3）The technique that the present invention obtains this gradient structure is simple, and it is good to ensure that it has again while the intensity for increasing steel
Good toughness, and low alloying is with low cost, the extensive prospect with industrial practical application.Can be widely applied to it is frayed or
Shock proof part, especially in terms of vehicle, mine mechanism.
Embodiment
The present invention is further illustrated below by embodiment, but is not limited to following examples.
Embodiment 1
The component and weight percent content of steel of the embodiment of the present invention be：C：0.15%, Si：2.11%, Mn：1.80%, Cr：
0.9%, Al：3.0%, S：0.0065%, P：0.0078%, remaining is Fe.
The steel chooses the thin lath martensite steel containing high density dislocation.
Steel is heated rapidly to austenitizing temperature first（850℃）Isothermal 10min, makes abundant austenitizing；Then exist
740 DEG C of progress case-carbonizings, carburizing time is 10h, and whole carburizing process will be carried out by atmosphere of nitrogen；Rapid quenching is to Ms
A certain 300 DEG C of the hardening heat between Mf, and 3h is incubated in nitrogen atmosphere in this temperature range.Then necessarily it is being tempered
330 DEG C of isothermal 10min of temperature carry out carbon distribution；Room temperature is finally quenched into again, and stable martensite and residual austenite are obtained in room temperature
The gradient heterogeneous structure of body.
According to GB/T228.1-2010《Metal material stretching test part 1：Room temperature test method》Inspection institute obtains complex phase
Product made from steel, stretching experiment is carried out on Zwick T1-FR020TN A50 standard tensile test machines.After tested, the center portion tension of steel
Intensity Rm is 1457MPa, center portion yield strength Rp0.2For 892MPa, breaking elongation is 22.9%.Case-carbonizing layer hardness be
560HV。
Embodiment 2
The component and weight percent content of steel of the embodiment of the present invention be：C：0.18%, Si：2.01%, Mn：2.03%, Cr：
0.9%, Al：2.5%, S：0.0053%, P：0.0068%, remaining is Fe.
Steel is heated rapidly to austenitizing temperature first（900℃）Isothermal 8min, makes abundant austenitizing；Then exist
770 DEG C of progress case-carbonizings, carburizing time is 15h, and whole carburizing process will be carried out by atmosphere of nitrogen；Rapid quenching is to Ms
A certain 350 DEG C of the hardening heat between Mf, and 3h is incubated in nitrogen atmosphere in this temperature range.Then necessarily it is being tempered
400 DEG C of isothermal 10min of temperature carry out carbon distribution.Room temperature is finally quenched into again, and stable martensite and residual austenite are obtained in room temperature
The gradient heterogeneous structure of body.
After tested, the center portion tensile strength Rm of steel is 1421MPa, center portion yield strength Rp0.2For 873MPa, breaking elongation
For 23.8%.Case-carbonizing layer hardness is 580HV.
Embodiment 3
The component and weight percent content of steel of the embodiment of the present invention be：C：0.21%, Si：1.16%, Mn：2.32%, Cr：
1.1%, Al：1.6%, S：0.0051%, P：0.0069%, remaining is Fe.
Steel is heated rapidly to austenitizing temperature first（900℃）Isothermal 15min, makes abundant austenitizing；Then exist
800 DEG C of progress case-carbonizings, carburizing time is 20h, and whole carburizing process will be carried out by atmosphere of nitrogen；Rapid quenching is to Ms
A certain 400 DEG C of the hardening heat between Mf, and 4h is incubated in nitrogen atmosphere in this temperature range.Then necessarily it is being tempered
420 DEG C of isothermal 10min of temperature carry out carbon distribution.Room temperature is finally quenched into again, and stable martensite and residual austenite are obtained in room temperature
The gradient heterogeneous structure of body.
After tested, the center portion tensile strength Rm of steel is 1415MPa, center portion yield strength Rp0.2For 871MPa, breaking elongation
For 24.7%.Case-carbonizing layer hardness is 606HV.
Embodiment 4
The component and weight percent content of steel of the embodiment of the present invention be：C：0.28%, Si：1.16%, Mn：2.48%, Cr：
1.9%, Al：1.8%, S：0.0052%, P：0.0054%, remaining is Fe.
Steel is heated rapidly to austenitizing temperature first（920℃）Isothermal 15min, makes abundant austenitizing；Then exist
850 DEG C of progress case-carbonizings, carburizing time is 20h, and whole carburizing process will be carried out by atmosphere of nitrogen；Rapid quenching is to Ms
A certain 450 DEG C of the hardening heat between Mf, and 4h is incubated in nitrogen atmosphere in this temperature range.Then necessarily it is being tempered
500 DEG C of isothermal 6min of temperature carry out carbon distribution.Room temperature is finally quenched into again, and stable martensite and retained austenite are obtained in room temperature
Gradient heterogeneous structure.
After tested, the center portion tensile strength Rm of steel is 1463MPa, center portion yield strength Rp0.2For 882MPa, breaking elongation
For 23.6%.Case-carbonizing layer hardness is 622HV.
Above is being elaborated to embodiments of the invention, carried out in fact lower premised on technical solution of the present invention
Apply.The above embodiment of the present invention can also make a variety of changes, i.e., every claims according to the present patent application and say
Simple, equivalent changes and modifications that bright book content is made, fall within the claims of patent of the present invention.
Claims (4)
1. a kind of Q＆P steel with gradient structure, is consisted of the following components in percentage by weight：
C：0.14-0.29%,
Si：1.1-2.8%,
Mn：1.8-3.0%,
Cr：0.5-1.9%,
Al：1.5-3.1%,
S：≤ 0.01%,
P：≤ 0.01%,
Remaining is Fe；
It is characterized in that：The preparation method of the Q＆P steel with gradient structure comprises the following steps：
The first step, is heated rapidly to 800-1100 DEG C of austenitizing temperature by steel first, and isothermal 5-30min makes abundant austenite
Change；
Second step, then carries out case-carbonizing, carburizing time is 10-50h, and whole carburizing process will be with nitrogen at 700-900 DEG C
Carried out for atmosphere；
3rd step, rapid quenching is incubated in nitrogen atmosphere 2-9h to 200-500 DEG C；
4th step, then in 300-600 DEG C of temperature, isothermal 5-600min carries out carbon distribution, makes carbon from martensite to remnants
Austenite is distributed, and now the carbon content in martensite declines, the carbon content rise in austenite, so that retained austenite richness carbon
And can stablize to room temperature；
5th step, is finally quenched into room temperature again, and stable martensite and the gradient heterogeneous structure of retained austenite are obtained in room temperature.
2. the Q＆P steel according to claim 1 with gradient structure, it is characterised in that：By the group of following percentage by weight
It is grouped into：
C：0.15-0.28%,
Si：1.16-2.11%,
Mn：1.80-2.48%,
Cr：0.9-1.9%,
Al：1.6-3.0%,
S：≤ 0.01%,
P：≤ 0.01%,
Remaining is Fe.
3. the Q＆P steel according to claim 1 with gradient structure, it is characterised in that：Comprise the following steps：
The first step, is heated rapidly to 850-950 DEG C of austenitizing temperature by steel first, and isothermal 6-20min makes abundant austenite
Change；
Second step, then carries out case-carbonizing, carburizing time is 10-20h, and whole carburizing process will be with nitrogen at 740-850 DEG C
Carried out for atmosphere；
3rd step, rapid quenching is incubated 2-4h to 300-450 DEG C, and in this temperature range in nitrogen atmosphere；
4th step, then in 330-500 DEG C of temperature, isothermal 5-30min carries out carbon distribution, makes carbon from martensite to remaining difficult to understand
Family name's body is distributed, and now carbon content in martensite declines, the carbon content rise in austenite so that retained austenite richness carbon and
It can stablize to room temperature；
5th step, is finally quenched into room temperature again, and stable martensite and the gradient heterogeneous structure of retained austenite are obtained in room temperature.
4. the Q＆P steel according to claim 1 with gradient structure, it is characterised in that：The steel, which is chosen, contains high density
The thin lath martensite of dislocation.
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| CN105734213B (en) * | 2016-05-08 | 2017-09-29 | 东北大学 | A kind of Q ＆ P steel plates and its twice partition preparation method |
| CN108070791B (en) * | 2016-11-18 | 2021-12-21 | 北方工业大学 | High-strength anchor rod for mine reinforcement |
| CN107227433A (en) * | 2017-05-26 | 2017-10-03 | 中北大学 | A kind of high-performance martensitic-austenitic dual phase steel and preparation method thereof |
| CN108893734B (en) * | 2018-07-02 | 2020-06-16 | 中北大学 | Low-carbon steel surface multiphase coating and preparation method thereof |
| CN113201739A (en) * | 2021-05-11 | 2021-08-03 | 中国航发常州兰翔机械有限责任公司 | Heat treatment process for 30CrNi3A structural steel part for aero-engine transmission |
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| US4191599A (en) * | 1978-09-13 | 1980-03-04 | Ford Motor Company | Method of heat treating high carbon alloy steel parts to develop surface compressive residual stresses |
| CN101225499B (en) * | 2008-01-31 | 2010-04-21 | 上海交通大学 | Low-alloy super-strength multiphase steel and heat treatment method thereof |
| FI20115702L (en) * | 2011-07-01 | 2013-01-02 | Rautaruukki Oyj | METHOD FOR PRODUCING HIGH-STRENGTH STRUCTURAL STEEL AND HIGH-STRENGTH STRUCTURAL STEEL |
| JP5910168B2 (en) * | 2011-09-15 | 2016-04-27 | 臼井国際産業株式会社 | TRIP type duplex martensitic steel, method for producing the same, and ultra high strength steel processed product using the TRIP type duplex martensitic steel |
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