CN105274436A - High-carbon microalloyed steel with strength and ductility product above 50 GPa% and heat treatment process - Google Patents
High-carbon microalloyed steel with strength and ductility product above 50 GPa% and heat treatment process Download PDFInfo
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Abstract
The invention provides high-carbon microalloyed steel with a strength and ductility product above 50 GPa% and a heat treatment process. The steel comprises the following components in percentage by mass: 0.60-0.75 of C, 1.0-2.0 of Mn, 1.0-2.0 of Si, 0.30-1.00 of Cr, 0.20-1.00 of Ni, 0.02-0.06 of Nb, and the balance of iron. The heat treatment process firstly performs the tempering treatment, and then performs the quenching-distribution-tempering (Q-P-T) process. The performance of high-carbon steel is improved through controlling the components of the high-carbon steel and changing the heat treatment process; and the strength and ductility product reaches above 50 GPa%.
Description
Technical field
The present invention relates to a kind of composition and thermal treatment process of steel, particularly, relate to high carbon microalloyed steel and thermal treatment process that a kind of strength and ductility product reaches more than 50GPa%.
Background technology
Intensity (unit; MPa) and unit elongation (unit: %) be the fundamental property of structured material requirement.Intensity and plasticity (available unit elongation represents) normally mutually exclusive, namely the strength of materials improves, and plasticity just reduces, otherwise intensity reduces, and plasticity just improves.In order to judge the quality of a structured material performance, the product of breaking elongation when usually adopting the tensile strength of material (corresponding to the intensity of the highest uniform elongation on stress strain curve) simply and rupture, be called strength and ductility product (productofstrengthandelongation, PSE), it is as the criterion of over-all properties.High strength and ductility product represents the over-all properties that material has had, and its approach is obtained by best materials Composition Design and best Design of Heat Treatment Process.High strength and ductility product is the important indicator of AHSS (advancedhighstrengthsteel, AHSS).
Nearly ten years, AHSS more and more more is used to automotive industry, and it effectively can reduce the consumption of structural part, as alleviated the weight of automobile structure, reaches the effect of energy-saving and emission-reduction.AHSS can be divided into three generations according to strength and ductility product at present: what strength and ductility product was less than 30GPa% is called first-generation AHSS (1GPa=1000MPa), it is Fe-Mn-Si base micro-(low) alloy low-carbon (LC) or medium carbon steel, such as dual phase steel (dualphase), phase change induction plasticity (transformationinducedplasticity, TRIP) steel, quenching-distribute (quenchingandpartitioning, Q & P) steel and quenching-distribution-tempering (quenching-partitioning-tempering, Q-P-T) steel.Strength and ductility product is greater than 50GPa% and is called s-generation AHSS, such as Gao Meng (Mn) twinning-induced plasticity (twinninginducedplasticity, TWIP).The strength and ductility product of the third generation (also known as a new generation, newgeneration) AHSS is between 30GPa% and 50GPa%, such as, and middle carbon Q-P-T steel, Medium Manganese Steel.
Through finding prior art literature search:
Sugimoto, K.-i., Tsunezawa, M., Hojo, T. & Ikeda, S.Ductilityof0.1 ~ 0.6C-1.5Si-1.5Mnultrahigh-strengthTRIP-aidedsheetsteelsw ithbainiticferritematrix.ISIJinternational44,1608-1614 (2004). article carries out the thermal treatment of different process to 0.1 ~ 0.6C – 1.5Si – 1.5MnTRIP steel, obtains the TRIP steel being organized as bainite ferrite matrix.Test-results shows, what the steel of different carbon content obtained maximum intensity and plasticity after carrying out identical thermal treatment process is still 0.6C steel, and its optimum performance is intensity 1300MPa and unit elongation 23%, and obtaining most high strength and ductility is 30GPa%.
Tomita, Y. & Morioka, K.Effectofmicrostructureontransformation-inducedplastici tyofsilicon-containinglow-alloysteel.MaterialsCharacteri zation38,243-250 (1997). different heat treatment art breading is carried out to 0.6C-1.5Si-0.8Mn steel, obtaining optimum performance is intensity 1000MPa and unit elongation 30%, and strength and ductility product is ~ 30GPa%.
The people such as Jiang Li have studied the tensile property under the differently strained speed of 0.63C-1.75Si-1.68Mn-0.028P-0.013STRIP steel room temperature.Through 900 DEG C of heating, insulation 20min, 340 DEG C of isothermal 2h process, the tensile property tested under differently strained speed obtains as drawn a conclusion: the unit elongation of high-carbon Si-Mn TRIP steel brings up to about 22% by 14% ~ 15%; Yield strength brings up to 1198MPa by 1015MPa; Ultimate strength brings up to 1546MPa by 1448MPa; The over-all properties that intensity coordinates with plasticity reaches 22 ~ 34GPa%.
The article " control deepfreeze is on the impact of the microstructure and property of medium high carbon Si-Mn non-carbide bainitic steel " that Liu Zhongxia etc. deliver, " metal heat treatmet " 52-57 (2005), this article have studied the impact of controlled cooling model thermal treatment process on the microstructure and mechanical property of high-carbon Si-Mn non-carbide bainitic steel.Result shows, 0.63C-1.92Si-0.76Mn micro-alloyed steel can obtain carbide-free Bainite tissue after cooling control technology process in very wide process parameters range; Along with the prolongation of sample cooling time in oil, the block retained austenite scale of construction constantly reduces, and retained austenite body thin film content constantly increases; The intensity of material, plasticity and toughness constantly increase along with the prolongation of oil cooling time.Material after cooling 7s ~ 8s in oil in air furnace 360 DEG C of insulation 3600s ~ 5400s process there is best intensity, plasticity, namely intensity reaches 1200MPa, and unit elongation 23%, strength and ductility product reaches 27.6GPa%.
Above research is all passed through to control high carbon steel composition and change thermal treatment process to reach the performance improving high carbon steel bar none, but the result obtained is compared with the 50GPa% obtained in the present invention, and gap clearly.This shows under carbon silicomanganese content similar situation, and high carbon steel is by changing alloying element proportioning and thermal treatment process, and the performance of high carbon steel still has very large raising space.
Summary of the invention
For in prior art by controlling high carbon steel composition and change thermal treatment process to improve the performance of high carbon steel but the highest situation only reaching 34GPa% of strength and ductility product to reach, the present invention proposes and a kind ofly can reach the composition of the high carbon microalloyed steel of more than 50GPa% and the technology of thermal treatment process.
According to a first aspect of the invention, a kind of strength and ductility product is provided to reach the high carbon microalloyed steel of more than 50GPa%, its composition (massfraction, %) specific as follows:
C:0.60 ~ 0.75, Mn:1.0 ~ 2.0, Si:1.0 ~ 2.0, Cr:0.30 ~ 1.00, Ni:0.20 ~ 1.00, Nb:0.02 ~ 0.06, residue is iron;
High carbon microalloyed steel, its composition preferable range following (massfraction, %):
C:0.64 ~ 0.69, Mn:1.3 ~ 1.8, Si:1.3 ~ 1.8, Cr:0.40 ~ 1.00, Ni:0.20 ~ 1.00, Nb:0.03 ~ 0.06, residue is iron.
Mentioned component principle of design of the present invention: high carbon content can reduce martensite start temperature (Ms), thus in ratio, carbon and low-carbon martensitic steels obtain the retained austenite more with high-ductility.Si adds, one is the precipitation suppressing fragility cementite, two is promote that carbon is assigned in retained austenite from supersaturation martensite to go, thus in the process of the last cool to room temperature of quenching-distribution-tempering (Q-P-T) technique, have more retained austenite to exist.Mn, Cr add the main hardening capacity improving steel, have solution strengthening effect concurrently; Ni adds the notch sensitivity mainly improving material; Nb adds, by forming stable Nb carbide, can fining austenite grains in hot rolling and austenitizing process, thus its phase-change product of refinement-martensitic tissue, improve yield strength and the toughness of steel thus; The stable Nb carbide of separating out in tempering, replaces the cementite of fragility, can improve the tensile strength of steel.
According to a further aspect in the invention, a kind of above-mentioned Heat Treatment Of Steel technique is provided, described technique is to pending 50GPa% high carbon microalloyed steel (workpiece of hot-rolled sheet or different shape), first normalizing treatment is carried out, as the pre-treatment of quenching-distribution-tempering subsequently (Q-P-T) technique, be specially:
Normalizing process (workpiece for hot-rolled sheet or different shape): in 840 DEG C-860 DEG C insulations (soaking time is limited to organize complete austenitizing and crystal grain not to grow up), air cooling is to room temperature subsequently;
Q-P-T technique: austenitizing temperature: 820 DEG C-860 DEG C, is then quenched to martensite start temperature (M
s) and end temp (M
f) between certain temperature (T
q): 110 DEG C-180 DEG C, insulation (soaking time is that the completeness distributed according to quenching part sectional dimension and carbon is determined), last water-cooled is to room temperature.
The above-mentioned Design of Heat Treatment Process principle of the present invention:
Normalizing treatment is as the pre-treatment of Q-P-T technique, its objective is in order to the content of pearlite in alloy in thinning microstructure and minimizing hot rolling, for Q-P-T technique obtains the martensitic matrix of refinement and the carbide of Dispersed precipitate, the more important thing is that dispersion for obtaining having mechanical stability and tiny retained austenite provide tissue to prepare.
Q-P-T technique, the selection of austenitizing temperature and soaking time is to obtain fully austenitic structure keep crystal grain tiny at such a temperature.In Q-P-T technique, quenching temperature (T
q) selection be to obtain retained austenite as much as possible, be combined in carbon subsequently and distribute and tempering makes carbon be assigned to retained austenite from supersaturation martensite to go, realize having more retained austenite to exist in the process of in the end cool to room temperature thus.And the temperature and time of carbon partition and tempering also makes the dislocation desity in martensitic matrix be down to suitable degree, to obtain required intensity and the cooperation of plasticity.
Steel by above-mentioned process obtains: martensitic matrix (volume fraction: 65 ~ 75%), retained austenite (35% ~ 25%), stable Nb carbide (being less than 1%).Intensity 1700 ~ 2000MPa, unit elongation 32 ~ 28%, strength and ductility product 50 ~ 55GPa%.
Compared with prior art, the present invention has following beneficial effect:
Composition Design of the present invention and heat-treatment technology method can obtain the high strength martensitic steel that strength and ductility product is 50GPa%, reach the level of the strength and ductility product (50GPa%) of s-generation AHSS (high-carbon height MnTWIP steel).Compared with s-generation AHSS, steel of the present invention belongs to microalloying steel, its Mn content is only about 1/10th of s-generation AHSS, and tensile strength is far above high-carbon height MnTWIP steel, as Fe-18Mn-0.6-1.5SiTWIP steel is only 1100MPa.This high-carbon of the present invention and microalloying, the martensitic steel of high strength and high-ductility that strength and ductility product reaches 50MPa% has not yet to see report both at home and abroad.
Composition of the present invention and thermal treatment process are applicable to all kinds of mechanical structured member, forging or rolled piece.
Embodiment
Below in conjunction with specific embodiment, the present invention is described in detail.Following examples will contribute to those skilled in the art and understand the present invention further, but not limit the present invention in any form.It should be pointed out that to those skilled in the art, without departing from the inventive concept of the premise, some distortion and improvement can also be made.These all belong to protection scope of the present invention.
Embodiment 1
(1) the concrete composition of steel following (massfraction, %) in the present embodiment:
C:0.63, Mn:1.5, Si:1.5, Cr:0.6, Nb:0.05, residue is iron;
(2) concrete thermal treatment process of the present invention is as follows:
Pending is the thick hot-rolled sheet of 20mm.
First normalizing treatment is carried out, as the pre-treatment of quenching-distribution-tempering subsequently (Q-P-T) technique.Be specially:
Normalizing process: 850 DEG C, insulation 3600s, air cooling is to room temperature subsequently;
Q-P-T technique: austenitizing temperature: 830 DEG C, insulation 360s, is then quenched to: 160 DEG C of (martensite start temperature (M
s) and end temp (M
f) between temperature (T
q)), insulation 10s, last water-cooled is to room temperature.
Result:
Microtexture: martensitic matrix (volume fraction: 72%), retained austenite (26.8%), stable Nb carbide (being less than 1%).
Intensity 1860MPa, unit elongation 29%, strength and ductility product 53.940GPa%.
Embodiment 2
(1) the concrete composition of steel following (massfraction, %) in the present embodiment:
C:0.75, Mn:1.2, Si:1.3, Ni:1.0, Nb:0.06, residue is iron;
(2) concrete thermal treatment process of the present invention is as follows:
Pending is the thick hot-rolled sheet of 20mm.
First normalizing treatment is carried out, as the pre-treatment of quenching-distribution-tempering subsequently (Q-P-T) technique.Be specially:
Normalizing process: 850 DEG C, insulation 3600s, air cooling is to room temperature subsequently;
Q-P-T technique: austenitizing temperature: 830 DEG C, insulation 360s, is then quenched to: 140 DEG C of (martensite start temperature (M
s) and end temp (M
f) between temperature (T
q)), insulation 20s, last water-cooled is to room temperature.
Result:
Microtexture: martensitic matrix (volume fraction: 72%), retained austenite (27.4%), stable Nb carbide (being less than 1%).
Intensity 1960MPa, unit elongation 26.2%, strength and ductility product 51.352GPa%.
Embodiment 3
(1) the concrete composition of steel following (massfraction, %) in the present embodiment:
C:0.68, Mn:1.00, Si:1.50, Nb:0.04, residue is iron;
(2) concrete thermal treatment process of the present invention is as follows:
Pending is the thick hot-rolled sheet of 20mm.
First normalizing treatment is carried out, as the pre-treatment of quenching-distribution-tempering subsequently (Q-P-T) technique.Be specially:
Normalizing process: 850 DEG C, insulation 3600s, air cooling is to room temperature subsequently;
Q-P-T technique: austenitizing temperature: 820 DEG C, insulation 360s, is then quenched to: 115 DEG C of (martensite start temperature (M
s) and end temp (M
f) between temperature (T
q)), insulation 20s, last water-cooled is to room temperature.
Result:
Microtexture: martensitic matrix (volume fraction: 68%), retained austenite (31.3%), stable Nb carbide (being less than 1%).
Intensity 2010MPa, unit elongation 25.5%, strength and ductility product 51.255GPa%.
Above specific embodiments of the invention are described.It is to be appreciated that the present invention is not limited to above-mentioned particular implementation, those skilled in the art can make various distortion or amendment within the scope of the claims, and this does not affect flesh and blood of the present invention.
Claims (5)
1. strength and ductility product reaches a high carbon microalloyed steel of more than 50GPa%, it is characterized in that: the composition following (massfraction, %) of described steel:
C:0.60 ~ 0.75, Mn:1.0 ~ 2.0, Si:1.0 ~ 2.0, Cr:0.30 ~ 1.00, Ni:0.20 ~ 1.00, Nb:0.02 ~ 0.06, residue is iron.
2. strength and ductility product according to claim 1 reaches the high carbon microalloyed steel of more than 50GPa%, it is characterized in that: the composition following (massfraction, %) of described steel:
C:0.64 ~ 0.69, Mn:1.3 ~ 1.8, Si:1.3 ~ 1.8, Cr:0.40 ~ 1.00, Ni:0.20 ~ 1.00, Nb:0.03 ~ 0.06, residue is iron.
3. strength and ductility product described in claim 1 or 2 reaches a thermal treatment process for the high carbon microalloyed steel of more than 50GPa%, it is characterized in that: first carry out normalizing treatment, as the pre-treatment of quenching-distribution-tempering subsequently (Q-P-T) technique, is specially:
Normalizing process: 840 DEG C-860 DEG C insulations, soaking time is limited to organize complete austenitizing and crystal grain not to grow up, and air cooling is to room temperature subsequently;
Q-P-T technique: austenitizing temperature: 820 DEG C-860 DEG C, be then quenched to martensite start temperature M
swith end temp M
fbetween certain temperature T
q: 110 DEG C-180 DEG C, insulation, soaking time is that the completeness distributed according to quenching part sectional dimension and carbon is determined, last water-cooled is to room temperature.
4. Heat Treatment Of Steel technique according to claim 3, is characterized in that: described thermal treatment process is applicable to all kinds of mechanical structured member, forging or rolled piece.
5. Heat Treatment Of Steel technique according to claim 3, is characterized in that: the steel obtained after described thermal treatment, its volume fraction: martensitic matrix: 65 ~ 75%, retained austenite 35% ~ 25%, stable Nb carbide (being less than 1%); Intensity 1700 ~ 2000MPa, unit elongation 32 ~ 28%, strength and ductility product 50 ~ 55GPa%.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106282494A (en) * | 2016-09-18 | 2017-01-04 | 扬州大学 | A kind of Q P Technology for Heating Processing of medium carbon alloy steel |
| CN107674955A (en) * | 2017-09-29 | 2018-02-09 | 安徽工业大学工商学院 | A kind of preparation method of low density steel of the strength and ductility product more than 50GPa% |
| CN108914004A (en) * | 2018-07-27 | 2018-11-30 | 武汉重工铸锻有限责任公司 | The heat treatment method of PCrNi3MoVA material forging elongation percentage can be improved |
| CN109777927A (en) * | 2019-03-15 | 2019-05-21 | 重庆明高机械制造有限公司 | A kind of potassium steel heat treatment process to struggle against for digging sand |
| CN110735022A (en) * | 2019-11-20 | 2020-01-31 | 安徽工业大学 | High-strength-ductility ultrahigh-strength automobile steel with cold and hot forming flexibility application |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106282494A (en) * | 2016-09-18 | 2017-01-04 | 扬州大学 | A kind of Q P Technology for Heating Processing of medium carbon alloy steel |
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| CN108914004B (en) * | 2018-07-27 | 2019-09-17 | 武汉重工铸锻有限责任公司 | The heat treatment method of PCrNi3MoVA material forging elongation percentage can be improved |
| CN109777927A (en) * | 2019-03-15 | 2019-05-21 | 重庆明高机械制造有限公司 | A kind of potassium steel heat treatment process to struggle against for digging sand |
| CN109777927B (en) * | 2019-03-15 | 2021-03-16 | 重庆明高机械制造有限公司 | High manganese steel heat treatment process for sand digging bucket |
| CN110735022A (en) * | 2019-11-20 | 2020-01-31 | 安徽工业大学 | High-strength-ductility ultrahigh-strength automobile steel with cold and hot forming flexibility application |
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