CN105039851B - Ti Alloying TAM steel and its manufacture method - Google Patents
Ti Alloying TAM steel and its manufacture method Download PDFInfo
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Abstract
The present invention relates to a kind of Ti Alloying TAM steel and its manufacturing process, belong to metal ingredient design and technical field of hot working.A kind of present invention Ti Alloying TAM steel, its chemical composition is by weight percentage：C 0.18～0.21%, Si 1.48～1.55%, Mn 1.90～2.20%, P≤0.020%, S≤0.015%, Ti 0.04～0.06%, Al≤0.04%, balance of Fe and inevitable impurity.The present invention adds appropriate titanium using Ti Alloying mode, improve the obdurability of TAM steel by the precipitation of the carbide of titanium etc., thus improve the comprehensive mechanical property of titaniferous TAM steel, making steel plate have higher intensity and plasticity, especially there is excellent resistant to hydrogen and cause delayed fracture property.The production of titaniferous TAM steel of the present invention Q＆P technique of adopting new technology makes steel structure property more stable.
Description
Technical field
The present invention relates to a kind of Ti Alloying TAM steel and its manufacturing process, belong to metal ingredient design and hot-working process
Field.
Background technology
TAM steel, also known as TRIP type annealing martensite steel (TRIP-aided Annealed Martensite Matrix),
It is one kind of Q＆P steel.Automobile Q＆P (Quenching and ParTiTioning) steel is as third generation AHSS (AdTianced
High Strength Steels) steel, there is inherent advantage, reached the matched well of intensity and plasticity, laboratory data shows
Show, the automobile intensity of Q＆P steel is in more than 1000MPa, and elongation percentage reaches more than 18%, be entirely capable of competent bumper (anti-
Hit crossbeam), the requirement of the part such as side collision prevention girders (W type).The maximum feature of TAM steel is to breach the polygon ferrum of traditional TRIP steel
Ferritic matrix or bainite matrix, employ the annealing lath horse that lath martensite is formed when two-phase section reheats
Family name's body is organized, lamellar retained austenite between coordinating with lath, obtains excellent mechanical property.This kind of steel typically also can be by adding
Enter Nb and TI etc., strengthened using precipitate, obtain excellent mechanical property.In recent years, the exploitation of unimach with
And the becoming increasingly conspicuous of Delayed hydride cracking problem, effect in terms of the resistance to Delayed hydride cracking improving unimach for the titanium is also
To substantial amounts of research.When trace Ti is solidly soluted in austenite, and in subsequent low temperature aging again after disperse educt, possess strong
Strong hydrogen trapping effect, Recent study finds, titanium mainly separated out by crystal grain thinning and TiC be used as irreversible hydrogen trap Lai
Improve the resistance for delayed fracture of high strength steel.
Wherein, the reason why phase change induction plasticity steel (TRIP steel) is than other high strength steel excellent performances are according to steel
Alloy chemical combination Transformation Principle, using specific chemical composition and unique Technology for Heating Processing, fully use " phase change induction in steel
The result of martensite effect ".When containing a certain amount of austenite former in steel, then face in two-phase section (α+γ) temperature
Boundary anneals and in subsequent middle temperature austempering, thus obtaining larger amount of retained austenite, when steel is made by load
During with deforming, the retained austenite in steel will be made to carry out strain induced martensite phase transformation, lead to the intensity of steel, plasticity significantly carries
Height, as " TRIP effect ".
And the new technology Q＆P technique for steel heat treatment, different from traditional quenching-tempering process, its be in order to
Obtain stable retained austenite, contain Si in application steel, Al (or even P) element, to hinder Fe3The precipitation of C, makes carbon from martensite
It is assigned to austenite, austenite answers rich carbon, will not be changed into martensite when cooling down again, having toughness concurrently for high strength steel provides
New effective technique.Meanwhile, after stable austenite film is formed around martensite bundle, reduce hydrogen induced cracking spreading rate,
Thus improve steel resistant to hydrogen to cause delayed fracture property.
In prior art, the ordinary steel without titanium is adopted mostly to the research of TRIP steel, and technique simply uses tradition
Technique, the comprehensive mechanical property of the TRIP steel of its preparation, such as intensity and plasticity, especially its resistant to hydrogen cause delayed fracture property,
All it is not met by the requirement of third generation automobile steel.
Content of the invention
First technical problem to be solved by this invention is to provide one kind to have more preferable intensity and plasticity, especially has
Excellent resistant to hydrogen is had to cause the Ti Alloying TAM steel of delayed fracture property.
Ti Alloying TAM steel, its chemical composition is by weight percentage：C 0.18～0.21%, Si 1.48～
1.55%th, Mn1.90～2.20%, P≤0.020%, S≤0.015%, Ti 0.04～0.06%, Al≤0.04%, balance of
Fe and inevitable impurity.
Further, as preferred technical scheme, Ti Alloying TAM steel described above, its chemical composition by weight hundred
Ratio is divided to be calculated as：C 0.1963%, Si 1.53%, Mn2.13%, P 0.0067%, S 0.0056%, Ti0.05%,
Al0.0088%, balance of Fe and inevitable impurity.
Ti Alloying TAM steel described above, its yield strength Rp0.2＞ 500MPa, tensile strength Rm ＞ 1050MPa, have no progeny
Percentage elongation A ＞ 25%, strength and ductility product Rm × A ＞ 25GPa %.
Further, as preferred technical scheme, Ti Alloying TAM steel described above, yield strength R of steelp0.2=
649MPa, tensile strength Rm=1112MPa, elongation after fracture A=26.8%, strength and ductility product Rm × A=29.8GPa %.
Ti Alloying TAM steel described above, its metallographic structure is martensitic matrix+retained austenite+bainite/ferrite
Line and staff control.
The present invention improves TAM due to the precipitation of the carbide of slab titaniferous using new titanium alloy composition design etc.
The obdurability of steel, thus improve the comprehensive mechanical property of titaniferous TAM steel, especially shows that Ti-containing steel has excellent resistant to hydrogen and causes
Delayed fracture property, this steel grade can make full use of climbs steel v-ti magnetite ore resources.By system, scientifically grasp steel in various
The hydrogen trap potentiality of tissue defects and precipitate are it is established that the anti-Delayed hydride cracking of hydrogen storage ferrous materials and unimach
Solution, either the exploitation for third generation automobile steel is significant with application, the utilization to following hydrogen energy source
Strategic material stock technology is provided, promotes national economy sustainable development, safeguard that national energy security provides material guarantee.With
When the research in this field for the China can be made to be in international forward position, form the design of material with independent intellectual property right and control skill
Art.
Second technical problem to be solved by this invention is to provide a kind of preparation method of Ti Alloying TAM steel.
The preparation method of Ti Alloying TAM steel, it specifically includes traditional mechanical rolling mill practice smelting, hot rolling, cold rolling and new
Technique Q＆P technique：
A, mechanical press technique：Steel billet is smelted and is cast into slab, after heating 70～90min at 1150～1250 DEG C,
Hot rolling is rolled into 3～5mm thickness hot rolled steel plate again, then through cold rolling to 1～1.5mm, cold rolling reduction ratio is 65～75%, obtains
To ferrite+pearlitic structrure；Wherein, 750～850 DEG C of hot rolling finishing temperature, 650～700 DEG C of coiling temperature；
B, Q＆P technique：The cold-reduced sheet that a step is obtained, is first warming up to 900～920 DEG C of austenitizing temperature with 10 DEG C/s,
Insulation 600s, then room temperature is cooled to 50 DEG C/s；Then 760～850 DEG C of annealing temperature is again warming up to 10 DEG C/s, insulation
600s, then 150～450 DEG C of partition temperature is cooled to 50 DEG C/s, it is incubated 50～200s, finally room temperature is cooled to 50 DEG C/s,
Obtain final product.
Further, as preferred technical scheme, the preparation method of Ti Alloying TAM steel described above：
After in a step, slab heats 80min preferably at 1200 DEG C, then hot rolling is rolled into 4mm thickness hot rolled steel plate, then passes through
Cold rolling obtains cold-rolled steel sheet after 1.2mm, and cold rolling reduction ratio is 70%；Wherein, hot rolling finishing temperature is preferably 800 DEG C, volume
Temperature is taken to be preferably 670 DEG C；
The cold-reduced sheet in b step obtaining a step, is first warming up to 920 DEG C of austenitizing temperature with 10 DEG C/s, insulation
600s, then room temperature is cooled to 50 DEG C/s；Then 800 DEG C of annealing temperature is again warming up to 10 DEG C/s, is incubated 600s, then with 50
DEG C/s is cooled to 400 DEG C of partition temperature, it is incubated 200s, finally room temperature is cooled to 50 DEG C/s, obtaining final product metallographic structure of the present invention is
Martensitic matrix+retained austenite+bainite/ferritic line and staff control TAM steel.
The TAM steel of the preparation method preparation of preferred Ti Alloying TAM steel described above, its yield strength Rp0.2=
649MPa, tensile strength Rm=1112MPa, elongation after fracture A=26.8%, strength and ductility product Rm × A=29.8GPa %.
Wherein, in a step, hot rolling technology can adopt 2050 hot strip rolling mill, cold rolling on cold-rolling mill before need heat
Rolled steel plate pickling, to remove surface scale and greasy dirt.
The present invention adds appropriate titanium using Ti Alloying mode, improves TAM steel by the precipitation of the carbide of titanium etc.
Obdurability, thus improve the comprehensive mechanical property of titaniferous TAM steel, making steel plate have higher intensity and plasticity, especially having
Excellent resistant to hydrogen is had to cause delayed fracture property.The manufacturing technique method of titaniferous TAM steel of the present invention, increasing compared with common production method
Add an intermediate annealing process, made steel structure property more stable.
Specific embodiment
Ti Alloying TAM steel, its chemical composition is by weight percentage：C 0.18～0.21%, Si 1.48～
1.55%th, Mn1.90～2.20%, P≤0.020%, S≤0.015%, Ti 0.04～0.06%, Al≤0.04%, balance of
Fe and inevitable impurity.
Further, as preferred technical scheme, Ti Alloying TAM steel described above, its chemical composition by weight hundred
Ratio is divided to be calculated as：C 0.1963%, Si 1.53%, Mn2.13%, P 0.0067%, S 0.0056%, Ti0.05%, Al
0.0088%, balance of Fe and inevitable impurity.
Ti Alloying TAM steel described above, its yield strength Rp0.2＞ 500MPa, tensile strength Rm ＞ 1050MPa, have no progeny
Percentage elongation A ＞ 25%, strength and ductility product Rm × A ＞ 25GPa %.
Further, as preferred technical scheme, Ti Alloying TAM steel described above, yield strength R of steelp0.2=
649MPa, tensile strength Rm=1112MPa, elongation after fracture A=26.8%, strength and ductility product Rm × A=29.8GPa %.
Ti Alloying TAM steel described above, its metallographic structure is martensitic matrix+retained austenite+bainite/ferrite
Line and staff control.
The present invention improves TAM due to the precipitation of the carbide of slab titaniferous using new titanium alloy composition design etc.
The obdurability of steel, thus improve the comprehensive mechanical property of titaniferous TAM steel, especially shows that Ti-containing steel has excellent resistant to hydrogen and causes
Delayed fracture property, this steel grade can make full use of climbs steel v-ti magnetite ore resources.By system, scientifically grasp steel in various
The hydrogen trap potentiality of tissue defects and precipitate are it is established that the anti-Delayed hydride cracking of hydrogen storage ferrous materials and unimach
Solution, either the exploitation for third generation automobile steel is significant with application, the utilization to following hydrogen energy source
Strategic material stock technology is provided, promotes national economy sustainable development, safeguard that national energy security provides material guarantee.With
When the research in this field for the China can be made to be in international forward position, form the design of material with independent intellectual property right and control skill
Art.
The preparation method of Ti Alloying TAM steel, it specifically includes traditional mechanical rolling mill practice smelting, hot rolling, cold rolling and new
Technique Q＆P technique：
A, mechanical press technique：Steel billet is smelted and is cast into slab, after heating 70～90min at 1150～1250 DEG C,
Hot rolling is rolled into 3～5mm thickness hot rolled steel plate again, then through cold rolling to 1～1.5mm, cold rolling reduction ratio is 65～75%, obtains
To ferrite+pearlitic structrure；Wherein, 750～850 DEG C of hot rolling finishing temperature, 650～700 DEG C of coiling temperature；
B, Q＆P technique：The cold-reduced sheet that a step is obtained, is first warming up to 900～920 DEG C of austenitizing temperature with 10 DEG C/s,
Insulation 600s, then room temperature is cooled to 50 DEG C/s；Then 760～850 DEG C of annealing temperature is again warming up to 10 DEG C/s, insulation
600s, then 150～450 DEG C of partition temperature is cooled to 50 DEG C/s, it is incubated 50～200s, finally room temperature is cooled to 50 DEG C/s,
Obtain final product.
Further, as preferred technical scheme, the preparation method of Ti Alloying TAM steel described above：
After in a step, slab heats 80min preferably at 1200 DEG C, then hot rolling is rolled into 4mm thickness hot rolled steel plate, then passes through
Cold rolling obtains cold-rolled steel sheet after 1.2mm, and cold rolling reduction ratio is 70%；Wherein, hot rolling finishing temperature is preferably 800 DEG C, volume
Temperature is taken to be preferably 670 DEG C；
The cold-reduced sheet in b step obtaining a step, is first warming up to 920 DEG C of austenitizing temperature with 10 DEG C/s, insulation
600s, then room temperature is cooled to 50 DEG C/s；Then 800 DEG C of annealing temperature is again warming up to 10 DEG C/s, is incubated 600s, then with 50
DEG C/s is cooled to 400 DEG C of partition temperature, it is incubated 200s, finally room temperature is cooled to 50 DEG C/s, obtaining final product metallographic structure of the present invention is
Martensitic matrix+retained austenite+bainite/ferritic line and staff control TAM steel.
The TAM steel of the preparation method preparation of preferred Ti Alloying TAM steel described above, its yield strength Rp0.2=
649MPa, tensile strength Rm=1112MPa, elongation after fracture A=26.8%, strength and ductility product Rm × A=29.8GPa %.
Wherein, in a step, hot rolling technology can adopt 2050 hot strip rolling mill, cold rolling on cold-rolling mill before need heat
Rolled steel plate pickling, to remove surface scale and greasy dirt.
With reference to embodiment, the specific embodiment of the present invention is further described, therefore the present invention is not limited
System is among described scope of embodiments.
Embodiment 1
Each composition percentage composition of Ti Alloying TAM steel of the present invention is with reference to shown in table 1：
The percentage composition of table 1 Ti Alloying TAM steel
Each composition percentage composition according to Ti Alloying TAM steel in table 1 carries out traditional mechanical rolling mill practice smelting, heat
Roll, cold rolling and new technology Q＆P technique, its traditional mechanical rolling mill practice specific process parameter is shown in Table 2：
Table 2 mechanical press technique specific process parameter
New technology Q＆P technique specific process parameter is shown in Table 3：
Table 3 Q＆P technique specific process parameter
According to each composition percentage composition and table 2 mechanical press technique, the table 3Q＆P technique of Ti Alloying TAM steel in table 1,
The mechanical property of prepared TAM steel is shown in Table 4：
The mechanical property of table 4 Ti Alloying TAM steel
| Numbering | Yield strength/MPa | Tensile strength/MPa | Elongation after fracture | Strength and ductility product/GMa % |
| 1 | 649 | 1112 | 26.8% | 29.8 |
| 2 | 668 | 1243 | 26.1% | 32.4 |
| 3 | 687 | 1098 | 25.3% | 27.8 |
| 4 | 669 | 1026 | 25.9% | 26.6 |
| 5 | 654 | 1203 | 26.7% | 30.5 |
Claims (3)
1. Ti Alloying TAM steel preparation method it is characterised in that：Comprise the following steps：
A, mechanical press technique：Steel are smelted and is cast into slab, after heating 70～90min at 1150～1250 DEG C, hot rolling
Obtain 3～5mm thickness hot rolled steel plate, then obtain 1～1.5mm thick cold rolled steel sheet through cold rolling；Wherein, hot rolling finishing temperature 750～
850 DEG C, 650～700 DEG C of coiling temperature, cold rolling reduction ratio is 65～75%；
B, Q＆P technique：The cold-reduced sheet that a step is obtained, is first warming up to 900～920 DEG C of austenitizing temperature with 10 DEG C/s, insulation
600s, then room temperature is cooled to 50 DEG C/s；Then 760～850 DEG C of annealing temperature is again warming up to 10 DEG C/s, is incubated 600s,
Again 150～450 DEG C of partition temperature is cooled to 50 DEG C/s, is incubated 50～200s, finally room temperature is cooled to 50 DEG C/s, obtains final product titanium
Alloying TAM steel；
Wherein, the chemical composition of described Ti Alloying TAM steel is by weight percentage：C 0.18～0.21%, Si 1.48～
1.55%th, Mn 1.90～2.20%, P≤0.020%, S≤0.015%, Ti 0.04～0.06%, Al≤0.04%, surplus
For Fe and inevitable impurity.
2. according to claim 1 Ti Alloying TAM steel preparation method it is characterised in that：In a step, slab is at 1200 DEG C
After lower heating 80min, then hot rolling is rolled into 4mm thickness hot rolled steel plate, then obtains 1.2mm thick cold rolled steel sheet through cold rolling；Its
In, hot rolling finishing temperature is 800 DEG C, and coiling temperature is 670 DEG C, and cold rolling reduction ratio is 70%.
3. according to claim 1 Ti Alloying TAM steel preparation method it is characterised in that：Austenitizing temperature in b step
For 920 DEG C；Annealing temperature is 800 DEG C；Partition temperature is 400 DEG C, is incubated 200s under partition temperature.
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| CN105908093B (en) * | 2016-06-03 | 2018-04-03 | 北京科技大学 | A kind of steel plate and manufacture method with high-fatigue strength of the compound addition of vanadium, titanium |
| WO2019092482A1 (en) | 2017-11-10 | 2019-05-16 | Arcelormittal | Cold rolled heat treated steel sheet and a method of manufacturing thereof |
| CN108179256A (en) * | 2018-02-06 | 2018-06-19 | 东北大学 | A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product |
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| JP2007070660A (en) * | 2005-09-05 | 2007-03-22 | Nippon Steel Corp | High strength thin steel sheet having excellent formability, and method for producing the same |
| CN101155940A (en) * | 2005-03-30 | 2008-04-02 | 株式会社神户制钢所 | High strength cold rolled steel sheet and plated steel sheet excellent in the balance of strength and workability |
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
| JP2012031505A (en) * | 2010-06-28 | 2012-02-16 | Nippon Steel Corp | High-strength thin steel sheet excellent in elongation and uniform coating-baking hardenability and method for producing the same |
| CN102828109A (en) * | 2012-09-17 | 2012-12-19 | 辽宁科技大学 | Metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and production method thereof |
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| CA2531615A1 (en) * | 2004-12-28 | 2006-06-28 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | High strength thin steel sheet having high hydrogen embrittlement resisting property |
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|---|---|---|---|---|
| CN101155940A (en) * | 2005-03-30 | 2008-04-02 | 株式会社神户制钢所 | High strength cold rolled steel sheet and plated steel sheet excellent in the balance of strength and workability |
| JP2007070660A (en) * | 2005-09-05 | 2007-03-22 | Nippon Steel Corp | High strength thin steel sheet having excellent formability, and method for producing the same |
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
| JP2012031505A (en) * | 2010-06-28 | 2012-02-16 | Nippon Steel Corp | High-strength thin steel sheet excellent in elongation and uniform coating-baking hardenability and method for producing the same |
| CN102828109A (en) * | 2012-09-17 | 2012-12-19 | 辽宁科技大学 | Metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and production method thereof |
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