CN102321854A - TRIP (Transformation-Induced Plasticity) steel and production method thereof - Google Patents
TRIP (Transformation-Induced Plasticity) steel and production method thereof Download PDFInfo
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- CN102321854A CN102321854A CN201110281155A CN201110281155A CN102321854A CN 102321854 A CN102321854 A CN 102321854A CN 201110281155 A CN201110281155 A CN 201110281155A CN 201110281155 A CN201110281155 A CN 201110281155A CN 102321854 A CN102321854 A CN 102321854A
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Abstract
The invention discloses TRIP (Transformation-Induced Plasticity) steel with low carbon content and high manganese content and a production method thereof, belonging to the technical field of steel products. The TRIP steel is the steel with the low carbon content and the high manganese content. The production method of the TRIP steel comprises the steps of smelting, thermal and continuous rolling, acid-washing in a push-pull manner, cold rolling, annealing in a cover manner and flattening. The yield strength of the TRIP steel is 400-900 MPa. The tensile strength of the TRIP steel is 1000-1500 MPa. The bake hardening value of the TRIP steel is 30-70 MPa. The TRIP steel can be applied to automobile components, and therefore, the TRIP steel has good application prospect in the respects of reducing the weight of an automobile and increasing the safety.
Description
Technical field
The present invention relates to the steel technical field, particularly a kind of low-carbon high-manganese TRIP steel and bell-type annealing working method thereof.
Background technology
Low-carbon (LC) TRIP steel plate, the big production of industry at present adopted continuous annealing processes in a large number, and it is used for automotive industry more, is mainly used in the car safety structural part, chassis member, as: B post inner panel, collision prevention girders etc.By the composition requirement is C≤0.32% to TRIP steel (780MPa level) among the Europe superscript EN10336-2007; Si≤2.20%; Mn≤2.50%; S≤0.015%; P≤0.12%, Al≤2.0%; Cr+Mo≤0.60%; Nb+Ti≤0.20%; V≤0.20%; B≤0.005%; Surplus is Fe.Its performance requriements is ys 470MPa≤Rp
0.2≤600MPa, tensile strength 3Rm>=780MPa, elongation after fracture requires A
80>=21%, n
10>=0.16, baking hardening value BH
2>=40MPa.For the strong TRIP steel of the superelevation more than the 780MPa level, in Europe superscript and GB, all do not make relevant provisions.When the TRIP steel was produced in pickling and cold-rolling associating unit and continuous annealing unit, because carbon equivalent is in laser welder, there was very big difficulty in the upper limit of especially narrow lap welder aspect stably manufactured and the logical plate stability; And, because the continuous annealing of TRIP steel is very high to the speed of cooling requirement, thereby, require very high to production line.
Summary of the invention
For the problems referred to above, the present invention proposes a kind of tensile strength and reach 1000MPa above low-carbon high-manganese TRIP steel and bell-type annealing working method thereof.
The chemical ingredients mass percent of TRIP steel provided by the invention is respectively: C0.08%～0.15%, Mn4.0%～8.0%, Si0.10%～0.25%; P 0.01%～0.10%, S≤0.015%, Als0.02～0.06%; Cr+Mo0.04%～0.40%, Cu+Ni0.05%～0.20%, Nb+Ti0.04%～0.15%; B0.0002%～0.0050%, N≤0.010%, surplus is Fe and impurity.
The working method of TRIP steel provided by the invention comprises smelting, hot continuous rolling, plug-type pickling, cold rolling, annealing, smooth, the said bell-type annealing that is annealed into; In the said process of bell type annealing, the Heating temperature scope is 500～730 ℃, and soaking time is 15～25 hours, and wherein, the hot(test)-spot temperature scope is 500～730 ℃, and the cold-point temperature scope is 500～730 ℃.
As preferably, in the said hot continuous rolling process, Heating temperature is 1250 ± 30 ℃, and finishing temperature is 930 ± 20 ℃, and coiling temperature is 580 ± 30 ℃.
As preferably, in the said cold-rolled process, cold rolling draft is controlled to be 55～75%.
As preferably, in the said formation process, control unit elongation 0.8 ± 0.3%.
The beneficial effect of TRIP steel provided by the invention and working method thereof is:
The mass percent scope of TRIP steel C provided by the invention is 0.08%～0.15%; The mass percent scope of Mn is 4.0%～8.0%; For the low-carbon high-manganese steel, in annealing process, under the driving of Si and Al; C, Mn make the TRIP effect give full play at the above-mentioned stable residual austenite that in austenite, spreads.The employing bell-type annealing of the working method of TRIP steel provided by the invention is annealed, because bell-type annealing to the speed of cooling no requirement (NR), is compared with continuous annealing, has reduced the requirement to apparatus for production line, produces flexible, convenient.The ys scope of TRIP steel provided by the invention is 400～900MPa, and the tensile strength scope is 1000～1500MPa, and baking hardening value scope is 30～70MPa, and, unit elongation A
80Better, the long-pending Rm * A of strong plasticity
80More than 20,000.The present invention provides the TRIP steel to be applied on the automobile structure, thereby has good application prospects aspect automobile loss of weight and the raising security.
Description of drawings
Fig. 1 is a bell-type annealing hot(test)-spot temperature control graphic representation of the present invention.
Fig. 2 is a bell-type annealing cold-point temperature change curve of the present invention.
Fig. 3 is the structure microstructure picture of TRIP steel provided by the invention.
Embodiment
In order to understand the present invention in depth, the present invention is elaborated below in conjunction with accompanying drawing and specific embodiment.
The chemical ingredients mass percent of TRIP steel provided by the invention is respectively: C0.08%～0.15%, Mn4.0%～8.0%, Si0.10%～0.25%; P 0.01%～0.10%, S≤0.015%, Als0.02～0.06%; Cr+Mo0.04%～0.40%, Cu+Ni0.05%～0.20%, Nb+Ti0.04%～0.15%; B0.0002%～0.0050%, N≤0.010%, surplus is Fe and impurity.The mass percent scope of this TRIP steel C is 0.08%～0.15%; The mass percent scope of Mn is 4.0%～8.0%, for the low-carbon high-manganese steel, in annealing process; Under the driving of Si and Al; C, Mn make the TRIP effect give full play at the above-mentioned stable residual austenite that in austenite, spreads, and accompanying drawing 3 is the structure microstructure picture of TRIP steel provided by the invention.This TRIP steel has higher intensity.
The working method of TRIP steel provided by the invention comprises smelting, hot continuous rolling, plug-type pickling, cold rolling, bell-type annealing, smooth.
The chemical ingredients mass percent of wherein, smelting the slab make is respectively: C0.08%～0.15%, Mn4.0%～8.0%, Si0.10%～0.25%; P 0.01%～0.10%, S≤0.015%, Als0.02～0.06%; Cr+Mo0.04%～0.40%, Cu+Ni0.05%～0.20%, Nb+Ti0.04%～0.15%; B0.0002%～0.0050%, N≤0.010%, surplus is Fe and impurity.
Wherein, Heating temperature is 1250 ± 30 ℃ in the hot continuous rolling process, and finishing temperature is 930 ± 20 ℃; Coiling temperature is 580 ± 30 ℃; In the said temperature parameter, lower coiling temperature is that the annealed structure of superfine crystal particle has been done preparation in advance, guarantees to anneal to carry out in the critical zone; And guarantee rational heating rate and soaking time, thereby make the structure of TRIP steel provided by the invention have the martensite content of proper ratio, remained austenite content and ferrite content.
Wherein, cold rolling employing single chassis is cold rolling, and the draft in the cold-rolled process is controlled to be 55～75%, finishes the thickness of the band steel of back acquisition to guarantee cold-rolled process, and cold rolling ferritic recrystallize carries out smoothly in the assurance annealing process;
Wherein, in the process of bell type annealing, the Heating temperature scope is 500～730 ℃, makes that the hot(test)-spot temperature scope is 500～730 ℃, and soaking time is 15～25 hours; The cold-point temperature scope is 500～730 ℃.Accompanying drawing 1 is TRIP steel provided by the invention hot(test)-spot temperature control graphic representation in process of bell type annealing, and accompanying drawing 2 is TRIP steel provided by the invention cold-point temperature change curve in process of bell type annealing.Because bell-type annealing to the speed of cooling no requirement (NR), is compared with continuous annealing, has reduced the requirement to apparatus for production line, produce flexible, convenient.
Wherein, smooth employing single chassis is smooth, wherein; In the formation process, the control unit elongation is 0.8 ± 0.3%, so that duplicate required roughness at belt steel surface; Thereby improve band rigidity ability, and the control unit elongation can also be adjusted the ys of being with steel 0.8 ± 0.3%.
The ys scope of TRIP steel provided by the invention is 400～900MPa, and the tensile strength scope is 1000～1500MPa, and baking hardening value scope is 30～70MPa, and, unit elongation A
80Better, the long-pending Rm * A of strong plasticity
80More than 20,000.The present invention provides the TRIP steel to be applied on the automobile structure, thereby has good application prospects aspect automobile loss of weight and the raising security.
Embodiment
Adopt aforesaid method to smelt to produce respectively the C shown in the listed sequence number of table 11, sequence number 2, sequence number 3, sequence number 4, the slab of Mn content (all the other compositions slightly).Slab is carried out hot continuous rolling, and wherein, Heating temperature is 1250 ± 30 ℃, and finishing temperature is 930 ± 20 ℃; Coiling temperature is 580 ± 30 ℃, adopts single chassis cold rolling, and the draft in the cold-rolled process is controlled to be 55～75%, afterwards; Heat according to the Heating temperature shown in the listed sequence number of table 11, sequence number 2, sequence number 3, sequence number 4 respectively, control corresponding hot(test)-spot temperature, and insulation, when cold-point temperature reaches this Heating temperature; I.e. cooling cooling, last, adopt single chassis smooth; Wherein, in the formation process, the control unit elongation is 0.8 ± 0.3%.
Table 1 TRIP steel provided by the invention corresponding C, Mn content
And corresponding Heating temperature and respective performances
Can find out that from table 1 TRIP steel ys Re scope provided by the invention is 400～900MPa, tensile strength Rm scope is 1000～1500MPa, baking hardening value RH
2Scope is 30～70MPa, and, unit elongation A
80Better, the long-pending Rm * A of strong plasticity
80More than 20,000.
The present invention provides the TRIP steel to be applied on the automobile structure, thereby has good application prospects aspect automobile loss of weight and the raising security.
Above-described embodiment; The object of the invention, technical scheme and beneficial effect have been carried out further explain, and institute it should be understood that the above is merely embodiment of the present invention; Be not limited to the present invention; All within spirit of the present invention and principle, any modification of being made, be equal to replacement, improvement etc., all should be included within protection scope of the present invention.
Claims (5)
1. a TRIP steel is characterized in that, the chemical ingredients mass percent is respectively: C0.08%～0.15%, Mn4.0%～8.0%; Si0.10%～0.25%, P 0.01%～0.10%, S≤0.015%, Als0.02～0.06%; Cr+Mo0.04%～0.40%, Cu+Ni0.05%～0.20%, Nb+Ti0.04%～0.15%; B0.0002%～0.0050%, N≤0.010%, surplus is Fe and impurity.
2. based on the working method of the described TRIP steel of claim 1, comprise smelting, hot continuous rolling, plug-type pickling, cold rolling, annealing, smooth, it is characterized in that the said bell-type annealing that is annealed into; In the said process of bell type annealing, the Heating temperature scope is 500 ~ 730 ℃, and soaking time is 15 ~ 25 hours, and wherein, the hot(test)-spot temperature scope is 500 ~ 730 ℃, and the cold-point temperature scope is 500 ~ 730 ℃.
3. method according to claim 2 is characterized in that, in the said hot continuous rolling process, Heating temperature is 1250 ± 30 ℃, and finishing temperature is 930 ± 20 ℃, and coiling temperature is 580 ± 30 ℃.
4. method according to claim 2 is characterized in that, in the said cold-rolled process, cold rolling draft is controlled to be 55～75%.
5. method according to claim 2 is characterized in that, in the said formation process, the control unit elongation is 0.8 ± 0.3%.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102719729A (en) * | 2012-06-18 | 2012-10-10 | 首钢总公司 | Automotive low-carbon aluminum-killed steel sheet and production method thereof |
| CN104294145A (en) * | 2014-10-20 | 2015-01-21 | 山东钢铁股份有限公司 | Bell-type annealing treatment-based cold rolled steel with tensile strength of 600MPa, and preparation method thereof |
| CN104651734A (en) * | 2014-12-11 | 2015-05-27 | 武汉钢铁(集团)公司 | 1000 MPa-level high-strength high-plasticity aluminum-containing medium manganese steel and manufacturing method thereof |
| CN104805378A (en) * | 2015-05-13 | 2015-07-29 | 东北大学 | High strength and toughness ultra-low carbon medium manganese steel middle-thickness plate and preparation method thereof |
| CN104911475A (en) * | 2015-06-25 | 2015-09-16 | 东北大学 | Low-carbon medium-manganese high-toughness super-thick steel plate and preparation method thereof |
| CN110055466A (en) * | 2019-05-21 | 2019-07-26 | 安徽工业大学 | The preparation method of hot rolling high-strength medium managese steel of the strength and ductility product greater than 30GPa% |
| CN110592485A (en) * | 2019-10-18 | 2019-12-20 | 山东钢铁集团日照有限公司 | Method for producing hot-galvanized TRIP780 steel with different yield strength grades |
| CN111944961A (en) * | 2020-08-13 | 2020-11-17 | 上海宝钢新材料技术有限公司 | Annealing method of variable-thickness automobile plate |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1729307A (en) * | 2002-12-20 | 2006-02-01 | 于西纳股份有限公司 | A steel composition for the production of cold rolled multiphase steel products |
| US20060162824A1 (en) * | 2005-01-27 | 2006-07-27 | United States Steel Corporation | Method for producing high strength, high ductility steel strip |
-
2011
- 2011-09-21 CN CN201110281155A patent/CN102321854A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1729307A (en) * | 2002-12-20 | 2006-02-01 | 于西纳股份有限公司 | A steel composition for the production of cold rolled multiphase steel products |
| US20060162824A1 (en) * | 2005-01-27 | 2006-07-27 | United States Steel Corporation | Method for producing high strength, high ductility steel strip |
Non-Patent Citations (1)
| Title |
|---|
| M. J. MERWIN: "Microstructure and Properties of Cold Rolled and Annealed Low-Carbon Manganese TRIP Steels", 《IRON & STEEL TECHNOLOGY》, vol. 5, 31 October 2008 (2008-10-31), pages 66 - 84, XP001516367 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102719729A (en) * | 2012-06-18 | 2012-10-10 | 首钢总公司 | Automotive low-carbon aluminum-killed steel sheet and production method thereof |
| CN102719729B (en) * | 2012-06-18 | 2014-04-02 | 首钢总公司 | Automotive low-carbon aluminum-killed steel sheet and production method thereof |
| CN104294145A (en) * | 2014-10-20 | 2015-01-21 | 山东钢铁股份有限公司 | Bell-type annealing treatment-based cold rolled steel with tensile strength of 600MPa, and preparation method thereof |
| CN104651734A (en) * | 2014-12-11 | 2015-05-27 | 武汉钢铁(集团)公司 | 1000 MPa-level high-strength high-plasticity aluminum-containing medium manganese steel and manufacturing method thereof |
| CN104805378B (en) * | 2015-05-13 | 2016-09-28 | 东北大学 | A kind of high tough Ultra-low carbon medium managese steel cut deal and preparation method thereof |
| CN104805378A (en) * | 2015-05-13 | 2015-07-29 | 东北大学 | High strength and toughness ultra-low carbon medium manganese steel middle-thickness plate and preparation method thereof |
| CN104911475A (en) * | 2015-06-25 | 2015-09-16 | 东北大学 | Low-carbon medium-manganese high-toughness super-thick steel plate and preparation method thereof |
| CN104911475B (en) * | 2015-06-25 | 2017-05-10 | 东北大学 | Preparation method for low-carbon medium-manganese high-toughness super-thick steel plate |
| CN110055466A (en) * | 2019-05-21 | 2019-07-26 | 安徽工业大学 | The preparation method of hot rolling high-strength medium managese steel of the strength and ductility product greater than 30GPa% |
| CN110055466B (en) * | 2019-05-21 | 2020-10-20 | 安徽工业大学 | Preparation method of hot-rolled high-strength medium manganese steel with strength-elongation product of more than 30GPa% |
| CN110592485A (en) * | 2019-10-18 | 2019-12-20 | 山东钢铁集团日照有限公司 | Method for producing hot-galvanized TRIP780 steel with different yield strength grades |
| CN111944961A (en) * | 2020-08-13 | 2020-11-17 | 上海宝钢新材料技术有限公司 | Annealing method of variable-thickness automobile plate |
| CN111944961B (en) * | 2020-08-13 | 2021-11-30 | 上海宝钢新材料技术有限公司 | Annealing method of variable-thickness automobile plate |
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Application publication date: 20120118 |