CN105463307A - Q&P steel with gradient structure and manufacturing method thereof - Google Patents
Q&P steel with gradient structure and manufacturing method thereof Download PDFInfo
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- CN105463307A CN105463307A CN201510820758.4A CN201510820758A CN105463307A CN 105463307 A CN105463307 A CN 105463307A CN 201510820758 A CN201510820758 A CN 201510820758A CN 105463307 A CN105463307 A CN 105463307A
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- 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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- 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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- 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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- 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
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- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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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Abstract
The invention discloses Q&P steel with a gradient structure. The Q&P steel comprises, by weight percent, 0.14-0.29% of C, 1.1-2.8% of Si, 1.8-3.0% of Mn, 0.5-1.9% of Cr, 1.5-3.1% of Al, smaller than or equal to 0.01% of S, smaller than 0.01% of P and the balance Fe. A manufacturing method of the Q&P steel includes the steps of austenitizing, carburizing, quenching, tempered carbon distributing and quenching. According to the Q&P steel and the manufacturing of the Q&P steel, technology stability and organization gradient can be ensured in production of large-size products, strength of the steel is improved, good toughness of the steel is also ensured, and low alloying cost is low.
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.
Background technology
In order to meet the double requirements of automotive industry future development to lightweight and high safety, automobile steel is constantly to high strength and high-ductility future development, and strength and ductility product becomes the important indicator weighing automobile steel performance.The strength and ductility product of first-generation automotive sheet steel is generally 15GPa%, and lightweight and safety indexes are all very low; Although the strength and ductility product of s-generation automobile steel reaches 50GPa%, its cost is higher, processing performance is poor and metallurgical production is difficult larger.So-called third generation automobile steel, refers to lightweight and safety indexes higher than first-generation automobile steel, production cost again lower than the high-strength high plastic-steel of s-generation automobile steel.
Q & P steel is the third generation automobile steel with higher-strength and toughness grown up in recent years.Its ultimate principle is: containing Si or (with) first after austenitizing, to be quenched to Ms ~ Mf(Ms be Ms (martensite start) point for the steel part of Al, Mf is martensitic transformation end temp) between a certain temperature, namely martensite and the residual austenite of some amount is formed, stay for some time in this initial quench temperature or a certain temperature of more than Ms again, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, carbon content in austenite raises, thus make the rich carbon of residual austenite and can stablize to room temperature, finally obtain the complex tissue be made up of martensite and residual austenite, thus obtain higher intensity and toughness, namely good comprehensive mechanical property.
In recent years, Xu ancestral shines academician on the basis of Q & P technique, make full use of the precipitation strength effect that the microalloy elements such as Nb, V and Ti form carbide, propose a kind of novel thermal treatment process: quenching-partition-tempering process (Quenching-Partitioning-Tempering, Q-P-T).This technique introduces a drawing process after Q & P process, makes martensitic matrix separates out complicated carbide, to increase the intensity of steel further.
But, along with the development of automotive industry, more and more higher requirement is proposed to the intensity of advanced high-strength steel and toughness.Although the Q & P steel intensity obtained is higher, its plasticity is poor.In addition, because its intensity is higher, largely reducing its welding property.Therefore, from the obdurability and the weldability that improve steel, and the angle consideration economizing on resources, reduce costs, the over-all properties improving Q & P steel is further significant.
Through finding the literature search of prior art, Xu ancestral shines academician at InternationalHeatTreatmentandSurfaceEngineering, 2008,2 (2), 64-68. delivers " Quenching-partitioning-tempering (Q-P-T) processforultra-highstrengthsteel " civilian, set forth the principle of quenching-carbon distribution-tempering (Q-P-T) technique, what utilize is that Carbide Precipitation strengthening improves the intensity of steel, finally obtains the heterogeneous structure of martensite, residual austenite and carbide.Also find in retrieval, application number is the Chinese patent of 200810033295.7, this patent obtains the three-phase contexture of martensite, residual austenite and nanometer bainite, and the nanometer bainite utilizing low temperature long time treatment to obtain improves the comprehensive mechanical property of steel further.Recently, J.G.Speer etc. are at MetallurgicalandMaterialsTransactionsA, 2011,42 (12), 3652-3659. delivers " QuenchedandPartitionedMicrostructuresProducedviaGleebleS imulationsofHot-StripMillCoolingPractices " civilian, point out that the obdurability by improving Q & P steel in high temperature hot rolling is effective, but do not consider macrostructure's distribution of steel part, do not form gradient microstructure.
Also find in retrieval, application number is the Chinese patent of 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%, and surplus is Fe.Through smelting, being forged into the microstructure that steel billet, hot rolling finally obtain martensite, residual austenite.Application number is the Chinese patent of 201310121568.4, disclose a kind of 700MPa grade high-strength hot-rolled Q & P steel and manufacture method thereof, this invention is designed by reasonable component, on plain C-Mn steel component base, the precipitation of cementite is suppressed by carrying high Si content, micro-Ti process fining austenite grains, improves the austenitic transformation kinetics that Al content accelerates process air cooler; Adopt hot continuous rolling process to coordinate sub-sectional cooling technique simultaneously, obtain containing proeutectoid ferrite+martensite+residual austenite body tissue.
Summary of the invention
The present invention aims to provide carburizing Q & P steel that a kind of heart portion plasticity is good, surface hardness is high and preparation method thereof, and this steel has gradient microstructure.
The invention provides a kind of Q & P steel with gradient structure, be made up of the component of following weight percent:
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%，
All the other are Fe.
Further, described in there is the Q & P steel of gradient structure, be made up of the component of following weight percent:
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%，
All the other are Fe.
Wherein the adding carbon content when can increase intercritical annealing in austenite and reduce this austenitic Ms temperature (martensite transformation temperature) to lesser temps of Cr and Al.
The invention provides a kind of above-mentioned preparation method with the Q & P steel of gradient structure, mainly comprise the following steps:
The first step, is first heated to rapidly austenitizing temperature 800-1100 DEG C by steel, and isothermal 5-30min makes abundant austenitizing;
Second step, then carries out surface cementation at 700-900 DEG C, and carburizing time is 10-50h, and whole cementation process will be that atmosphere is carried out with nitrogen;
3rd step, a certain quenching temperature (200-500 DEG C) between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 2-9h is incubated in this temperature range;
4th step, then at tempering temperature 300-600 DEG C, isothermal 5-600min carries out carbon distribution, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, and the carbon content in austenite raises, thus makes the rich carbon of residual austenite and can stablize to room temperature;
5th step, is finally quenched into room temperature again, obtains the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
The invention provides the preparation method of the Q & P steel preferably with gradient structure, comprise the following steps:
The first step, is first heated to rapidly austenitizing temperature 850-950 DEG C by steel, and isothermal 6-20min makes abundant austenitizing;
Second step, then carries out surface cementation at 740-850 DEG C, and carburizing time is 10-20h, and whole cementation process will be that atmosphere is carried out with nitrogen;
3rd step, a certain quenching temperature (300-450 DEG C) between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 2-4h is incubated in this temperature range;
4th step, then at tempering temperature 330-500 DEG C, isothermal 5-30min carries out carbon distribution, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, and the carbon content in austenite raises, thus makes the rich carbon of residual austenite and can stablize to room temperature;
5th step, is finally quenched into room temperature again, obtains the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
The invention provides a kind of the low-alloy high-strength toughness Multiphase Steel and the heat treating method thereof that meet scale operation, adopt technique scheme, the method utilizing carburizing+quenching+carbon to distribute, makes steel obtain gradient heterogeneous structure.The present invention is compared with traditional Q & P technique, and realize that carbon occurs in drawing process by carburizing and new alloy and phase transformation design and distribute, this technology can ensure technology stability and tissue gradient in large-size products production.
First the present invention will ensure the high strength of steel, and its matrix need select martensitic stucture, and this martensitic stucture should based on the thin lath martensite containing high density dislocation.Secondly, distribute (Q & P) by advanced thermal treatment process quenching carbon to make will have retained austenitic film between martensite lath.Final acquisition contains the two-phase complex tissue of dislocation type martensite and residual austenite.The toughness of prepared steel is greatly improved and maintains higher intensity.Its high strength derives from refined crystalline strengthening and the dislocations strengthening of martensite and complex tissue, and good plasticity derives from tissue exists the softening of appropriate residual austenite and initial quench martensitic stucture, and has the heterogeneous structure of gradient.
Of the present invention
beneficial effect:
(1) the present invention realizes higher strength and ductility product by new alloy and phase transformation design, and quenching temperature controlled within the specific limits, this technology can ensure technology stability and tissue gradient in large-size products production;
(2) the present invention surface of Q & P steel of preparing is owing to have passed through carburizing, and its surface structure is high carbon martensite and residual austenite, and its core structure is low carbon martensite and residual austenite;
(3) the present invention obtains the technique of this gradient structure simply, ensure that again it has good toughness, and low alloying is with low cost, has the extensive prospect of industrial practical application while increasing the intensity of steel.Frayed or shock proof parts can be widely used in, especially in vehicle, mine mechanism etc.
Embodiment
Further illustrate the present invention below by embodiment, but be not limited to following examples.
embodiment 1
The component of embodiment of the present invention steel and weight percent content are: C:0.15%, Si:2.11%, Mn:1.80%, Cr:0.9%, Al:3.0%, S:0.0065%, P:0.0078%, and all the other are Fe.
The thin lath martensite steel containing high density dislocation chosen by described steel.
First steel is heated to rapidly austenitizing temperature (850 DEG C) isothermal 10min, makes abundant austenitizing; Then carry out surface cementation at 740 DEG C, carburizing time is 10h, and whole cementation process will be that atmosphere is carried out with nitrogen; A certain quenching temperature 300 DEG C between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 3h is incubated in this temperature range.Then carbon distribution is carried out at certain tempering temperature 330 DEG C of isothermal 10min; Finally be quenched into room temperature again, obtain the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
Obtain Multiphase Steel product according to GB/T228.1-2010 " metal material stretching test part 1: room temperature test method " inspection institute, stretching experiment carries out on ZwickT1-FR020TNA50 standard tensile test machine.After tested, the heart portion tensile strength Rm of steel is 1457MPa, heart portion yield strength Rp
0.2for 892MPa, breaking elongation is 22.9%.Surface cementation layer hardness is 560HV.
embodiment 2
The component of embodiment of the present invention steel and weight percent content are: C:0.18%, Si:2.01%, Mn:2.03%, Cr:0.9%, Al:2.5%, S:0.0053%, P:0.0068%, and all the other are Fe.
First steel is heated to rapidly austenitizing temperature (900 DEG C) isothermal 8min, makes abundant austenitizing; Then carry out surface cementation at 770 DEG C, carburizing time is 15h, and whole cementation process will be that atmosphere is carried out with nitrogen; A certain quenching temperature 350 DEG C between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 3h is incubated in this temperature range.Then carbon distribution is carried out at certain tempering temperature 400 DEG C of isothermal 10min.Finally be quenched into room temperature again, obtain the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
After tested, the heart portion tensile strength Rm of steel is 1421MPa, heart portion yield strength Rp
0.2for 873MPa, breaking elongation is 23.8%.Surface cementation layer hardness is 580HV.
embodiment 3
The component of embodiment of the present invention steel and weight percent content are: C:0.21%, Si:1.16%, Mn:2.32%, Cr:1.1%, Al:1.6%, S:0.0051%, P:0.0069%, and all the other are Fe.
First steel is heated to rapidly austenitizing temperature (900 DEG C) isothermal 15min, makes abundant austenitizing; Then carry out surface cementation at 800 DEG C, carburizing time is 20h, and whole cementation process will be that atmosphere is carried out with nitrogen; A certain quenching temperature 400 DEG C between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 4h is incubated in this temperature range.Then carbon distribution is carried out at certain tempering temperature 420 DEG C of isothermal 10min.Finally be quenched into room temperature again, obtain the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
After tested, the heart portion tensile strength Rm of steel is 1415MPa, heart portion yield strength Rp
0.2for 871MPa, breaking elongation is 24.7%.Surface cementation layer hardness is 606HV.
embodiment 4
The component of embodiment of the present invention steel and weight percent content are: C:0.28%, Si:1.16%, Mn:2.48%, Cr:1.9%, Al:1.8%, S:0.0052%, P:0.0054%, and all the other are Fe.
First steel is heated to rapidly austenitizing temperature (920 DEG C) isothermal 15min, makes abundant austenitizing; Then carry out surface cementation at 850 DEG C, carburizing time is 20h, and whole cementation process will be that atmosphere is carried out with nitrogen; A certain quenching temperature 450 DEG C between rapid quenching to Ms and Mf, and in nitrogen atmosphere, 4h is incubated in this temperature range.Then carbon distribution is carried out at certain tempering temperature 500 DEG C of isothermal 6min.Finally be quenched into room temperature again, obtain the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
After tested, the heart portion tensile strength Rm of steel is 1463MPa, heart portion yield strength Rp
0.2for 882MPa, breaking elongation is 23.6%.Surface cementation layer hardness is 622HV.
Being more than elaborate to embodiments of the invention, is implement under premised on technical solution of the present invention.The above embodiment of the present invention can also make a variety of changes, and simple, equivalence that namely every claims according to the present patent application and description are done change and modify, and all fall into the claims of patent of the present invention.
Claims (5)
1. there is a Q & P steel for gradient structure, it is characterized in that: be made up of the component of following weight percent:
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%，
All the other are Fe.
2. the Q & P steel with gradient structure according to claim 1, is characterized in that: be made up of the component of following weight percent:
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%，
All the other are Fe.
3. the preparation method with the Q & P steel of gradient structure described in claim 1 or 2, is characterized in that: comprise the following steps:
The first step, is first heated to rapidly austenitizing temperature 800-1100 DEG C by steel, and isothermal 5-30min makes abundant austenitizing;
Second step, then carries out surface cementation at 700-900 DEG C, and carburizing time is 10-50h, and whole cementation process will be that atmosphere is carried out with nitrogen;
3rd step, rapid quenching to 200-500 DEG C, and is incubated 2-9h in nitrogen atmosphere;
4th step, then at tempering temperature 300-600 DEG C, isothermal 5-600min carries out carbon distribution, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, and the carbon content in austenite raises, thus makes the rich carbon of residual austenite and can stablize to room temperature;
5th step, is finally quenched into room temperature again, obtains the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
4. the preparation method with the Q & P steel of gradient structure according to claim 3, is characterized in that: comprise the following steps:
The first step, is first heated to rapidly austenitizing temperature 850-950 DEG C by steel, and isothermal 6-20min makes abundant austenitizing;
Second step, then carries out surface cementation at 740-850 DEG C, and carburizing time is 10-20h, and whole cementation process will be that atmosphere is carried out with nitrogen;
3rd step, rapid quenching to 300-450 DEG C, and is incubated 2-4h in this temperature range in nitrogen atmosphere;
4th step, then at tempering temperature 330-500 DEG C, isothermal 5-30min carries out carbon distribution, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, and the carbon content in austenite raises, thus makes the rich carbon of residual austenite and can stablize to room temperature;
5th step, is finally quenched into room temperature again, obtains the gradient heterogeneous structure stablizing martensite and residual austenite in room temperature.
5. the preparation method with the Q & P steel of gradient structure according to claim 3, is characterized in that: the thin lath martensite containing high density dislocation chosen by described steel.
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| CN105734213A (en) * | 2016-05-08 | 2016-07-06 | 东北大学 | Q-P (quenching and partitioning) steel plate and twice partitioning preparation method thereof |
| CN105779708A (en) * | 2016-04-27 | 2016-07-20 | 上海人本集团有限公司 | Thermal treatment process for high-carbon chromium bearing steel |
| 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 |
| CN108070791A (en) * | 2016-11-18 | 2018-05-25 | 北方工业大学 | High-strength anchor rod for mine reinforcement |
| CN108893734A (en) * | 2018-07-02 | 2018-11-27 | 中北大学 | A kind of surface of low-carbon steel duplex heat treatment 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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| CN103732764A (en) * | 2011-07-01 | 2014-04-16 | 罗奇钢铁公司 | Method for manufacturing a high-strength structural steel and a high-strength structural steel product |
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Cited By (7)
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| CN105779708A (en) * | 2016-04-27 | 2016-07-20 | 上海人本集团有限公司 | Thermal treatment process for high-carbon chromium bearing steel |
| CN105734213A (en) * | 2016-05-08 | 2016-07-06 | 东北大学 | Q-P (quenching and partitioning) steel plate and twice partitioning preparation method thereof |
| 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 |
| CN108070791A (en) * | 2016-11-18 | 2018-05-25 | 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 |
| CN108893734A (en) * | 2018-07-02 | 2018-11-27 | 中北大学 | A kind of surface of low-carbon steel duplex heat treatment 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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