CN101363102A - TRIP steel sheet for high strength cold rolled continuous annealing and preparation method thereof - Google Patents
TRIP steel sheet for high strength cold rolled continuous annealing and preparation method thereof Download PDFInfo
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- CN101363102A CN101363102A CNA2008101198245A CN200810119824A CN101363102A CN 101363102 A CN101363102 A CN 101363102A CN A2008101198245 A CNA2008101198245 A CN A2008101198245A CN 200810119824 A CN200810119824 A CN 200810119824A CN 101363102 A CN101363102 A CN 101363102A
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Abstract
A high-strength and cold-rolled TRIP steel plate for continuous annealing and a preparation method thereof belong to the technical field of high-strength cold rolled steel. The components of the steel plate are as follows according to mass percentages: 0.1-0.4% of C, 0.5-2.5% of Si, 0.5-2.5% of Mn, 0.01-0.10% of Nb, 0.01-0.10% of Ti, 0.1-1.0% of Cu, 0.1-1.0% of Ni, not more than 0.03% of P, not more than 0.02% of S, and Fe. The steel plate has the advantages of superior workability and surface properties, the mechanical properties of the steel plate are improved by adding Nb, Ti, Cu, Ni, and the like, which provides the plate with the combination of high tensile strength and high specific elongation.
Description
Technical field
The present invention relates to high intensity cold steel rolling technical field, particularly provide a kind of high strength cold rolled continuous annealing with TRIP (TRIP is the abbreviation of phase-change induced plastic) steel plate and preparation method thereof.
Background technology
For a long time, ferrous materials is the main material of using of automotive industry always, although in recent years along with the decline of car weight, the ratio of ferrous materials is still keeping leading status descending.The appearance of aluminium, magnesium and plastic automotive is conspicuous to the threat of Iron And Steel Industry, and the research project of ultralight steel car body (ULSAB) is carried out in 35 Iron And Steel Company's cooperations of 18 countries in the whole world for this reason, to meet the challenge of aluminium and magnesium.Its characteristics mainly are to use high-strength steel (HSS), super-high strength steel (UHSS, AHSS) in a large number, and do not re-use or seldom use traditional low carbon mild steel, such as, common aluminium killed steel, IF steel etc.
The car industry requirement loss of weight this means the material that working strength is higher, so that can reduce the thickness of parts under the prerequisite of not abandoning security and functional requirement.Ultrahigh-strength steel (UHSS) light sheet products, especially TRIP product made from steel have outstanding high strength and good plasticity combination, therefore can provide terms of settlement for this problem.
The research report of domestic relevant TRIP steel is less relatively, and many places are carried out system and waited study few with big production experiment in laboratory stage.Baosteel began to develop cold rolling TRIP steel from 2002, realized the commercialization of the cold rolling TRIP steel of 600MPa rank, and successful Application and domestic automobile industry.In order further to alleviate car weight, it is very necessary to develop high level TRIP steel.
There is scholar (adding the influence of 0.5% bronze medal and bainiteization) to discover, adds the Cu element, can significantly improve intensity sacrificing under a little plasticity condition to 0.2C_1.5Mn_1.5Si deformation induced plasticity TRIP steel plate tissue and mechanical property.So, can significantly improve comprehensive mechanical performance by adding a small amount of alloying element.
Summary of the invention
The purpose of this invention is to provide a kind of TRIP steel sheet for high strength cold rolled continuous annealing and preparation method thereof, this steel constitution is used for being fit to by cold rolling preparation the product made from steel of continuous annealing.
Steel plate composition of the present invention is (a quality percentage composition):
C:0.1%～0.4%, Si:0.5%～2.5%, Mn:0.5%～2.5%, Nb:0.01%～0.10%, Ti:0.01%～0.10%, Cu:0.1%～1.0%, Ni:0.1%～1.0%, P :≤0.03%, S :≤0.02%, surplus is an iron.
TRIP steel sheet for high strength cold rolled continuous annealing step of preparation process of the present invention is:
1, add alloy element Nb in tapping, Ti is by tiny carbon niobium nitride titanium, pinning austenite grain boundary, refinement strand crystal grain;
2, strand is rolled into steel billet: hot rolling finishing temperature is Ar3+50 ℃～Ar3+150 ℃, obtains hot rolling blank;
3, hot rolling steel billet being cooled to 600～750 ℃ of temperature batches;
4, batch the described hot rolling steel billet of back pickling, to remove oxide compound;
5, the cold rolling described hot rolling steel billet of draught of employing 50%～70% is to reduce thickness;
6, be incubated described cold rolling steel billet down at 750～900 ℃, soaking time is 60～200s; Employing is cooled to 350～500 ℃ greater than the speed of cooling of 20～50 ℃/s with described cold rolling steel billet; Be incubated described cold rolling steel billet in this temperature range, the time is 100～600s; Adopt the speed of cooling of 20～50 ℃/s that described cold rolling steel billet is cooled to room temperature then; The steel plate yield strength that obtains is 450～700MPa, and tensile strength is greater than 980MPa, and unit elongation A50 is greater than 20%.
Description of drawings
Fig. 1 is an annealing process synoptic diagram of the present invention.Wherein, X-coordinate is the time, unit: second; Ordinate zou is a temperature.
Embodiment
C: carbon is austenite stabilizer element, reduces the Ms point strongly.The austenite that only contains a certain amount of C could be residual in room temperature.And owing to transform inductive plasticity-.When C concentration is little 0.05% the time, almost can't guarantee 5% more residual austenite, thereby can not realize purpose of the present invention.On the other hand, surpass 0.4% and can make the non-constant of weldability, so C content can not be too high.
Mn: manganese plays austenitic function of stabilizer, thereby can reduce the Ms temperature of residual austenite.In addition, manganese can be restrained perlite and form, and, can also improve the intensity aggregate level of steel by solution strengthening.On the one hand, add excessive Mn and can cause when when holding temperature is cooled off, can not fully forming perlite, thereby make the broken concentration deficiency in the residual austenite, cause its stability decreases.On the other hand, the Mn too high levels also will improve the hardness of weld seam, and promote the formation of deleterious banded structure.
Si: silicon mainly is present in the TRIP steel in the solid solution mode, the formation of cementite during the inhibition bainite transformation.Si is a ferrite former, and when heating in the critical zone, Si is more prone to be distributed in the ferrite rather than in austenite, thereby the Si dilution of austenite crystal edge.Si is distributed in the ferrite, improves the chemical potential of carbon in the ferrite, impels carbon in the ferrite to the austenite internal divergence, and carbon concentration raises in the residual austenite.C is further accumulated in the austenite that does not change, impel martensite to begin transition temperature M
SReduce to below the room temperature, form the residual austenite of rich carbon, obtain the primary condition that the TRIP effect produces.For fear of requiring,, should limit Si content to prevent to form crackle to the hot steel bloom material.By restriction Si content, also can avoid red squama occurring at hot rolling surface.
Nb: niobium is a kind of strong carbide forming element, the avidity of niobium and carbon is greater than vanadium, niobium commonly used carries out microalloying in ferrous materials, mainly be to utilize niobium to combine to form dispersing carbide with carbon, this carbide formation temperature that contains niobium is higher, may in high-temperature molten steel, exist, and its lattice parameter is close with austenite, can be used as austenitic crystallization nuclei, the niobium that adds trace can thinning solidification structure, in heat treatment process, separate out niobium carbide in addition and generally be the small and dispersed distribution, help dispersion-strengthened, and can stop high temperature austenite to be grown up.((C N), causes the waste of alloying element to form thick Nb for C, N) poly-partially but Nb can take place too much Nb.
Ti: titanium also is a kind of strong carbide forming element, effect similar to niobium.
The copper content of Cu:1% can improve the intensity of 50MPa, but the dissolving of copper only takes place when high temperature, and almost nil under the room temperature, copper also improves intensity by crystal grain thinning.In ferrite refrigerative process, the solubleness of copper reduces rapidly, produces precipitation strength.
Ni: the similar generation austenite of nickel to Mn, it can also improve intensity and plating performance simultaneously, and in addition, similar with Al to Si, Ni is not dissolved in the cementite.Suppress the cementite precipitation in the maintenance process in 350 ℃ of-600 ℃ of temperature ranges, and postpone conversion process.Ni can also improve the deterioration that adds the plasticity that Cu brought.
S: sulphur as remnants and harmful element except the machinability that can improve steel, all very unfavorable to extension, impelling strength and the hot-work of steel.So S must be controlled in 0.02%.
P: phosphorus is a kind of harmful element, has seriously destroyed the impelling strength of steel, and is also unfavorable to the hot-work and the weldability of steel.Equally, P also will be strict controlled within 0.03%.
Embodiment
The 1000MPa level cold rolled continuous annealing of the present invention manufacture method of TRIP steel:
At first smelt according to design mix, blank is rolled into thin plate after forging, and 860 ℃ of hot rolling finishing temperatures, coiling temperature are 650 ℃; Cold rolling draft is 65%; The two-phase region annealing temperature is 860 ℃, and the two-phase region annealing time is 120s or 180s, and the cooling rate CR1 that is chilled to isothermal temperature from annealing temperature is greater than 20 ℃/s; Isothermal temperature is respectively 380,420 and 460 ℃, and isothermal time is 240s, and the speed of cooling CR2 behind the isothermal is cooled to room temperature greater than 20 ℃/s, thereby obtains 1000MPa level cold rolled continuous annealing TRIP steel.Fig. 1 is an annealing process, and table 1 is a chemical ingredients, and table 2 is a mechanical property.
Table 1 chemical ingredients
| C | Si | Mn | P | S | Cu | Ni | Nb | Ti |
| 0.24 | 1.40 | 1.5 | 0.01 | 0.005 | 0.5 | 0.31 | 0.03 | 0.015 |
Table 2 main technique and mechanical property
| Embodiment | Annealing temperature/℃ | Annealing time/s | Isothermal temperature/℃ | Isothermal time/s | Yield strength/MPa | Tensile strength/MPa | Unit elongation/% |
| 1 | 860 | 120 | 380 | 240 | 668 | 945 | 23.8 |
| 2 | 860 | 120 | 420 | 240 | 680 | 995 | 21.3 |
| 3 | 860 | 120 | 460 | 240 | 695 | 1015 | 20.5 |
| 4 | 860 | 180 | 420 | 240 | 705 | 1012 | 20.9 |
Claims (2)
1. high strength cold rolled continuous annealing phase-change induced plastic steel plate, it is characterized in that the steel plate composition is: C:0.1%～0.4%, Si:0.5%～2.5%, Mn:0.5%～2.5%, Nb:0.01%～0.10%, Ti:0.01%～0.10%, Cu:0.1%～1.0%, Ni:0.1%～1.0%, P :≤0.03%, S :≤0.02%, surplus is an iron; Be mass percent.
2. one kind prepares the method that the described high strength cold rolled continuous annealing of claim 1 is used phase-change induced plastic steel plate, it is characterized in that processing step is:
(1) add alloy element Nb in tapping, Ti is by tiny carbon niobium nitride titanium, pinning austenite grain boundary, refinement strand crystal grain;
(2) strand is rolled into steel billet: hot rolling finishing temperature is Ar3+50 ℃～Ar3+150 ℃, obtains hot rolling blank;
(3) hot rolling steel billet being cooled to 600～750 ℃ of temperature batches;
(4) batch the described hot rolling steel billet of back pickling, to remove oxide compound;
(5) the cold rolling described hot rolling steel billet of draught of employing 50%～70%;
(6) be incubated described cold rolling steel billet down at 750～900 ℃, soaking time is 60～200s; Then, adopt the speed of cooling of 20～50 ℃/s that described cold rolling steel billet is cooled to 350～500 ℃, insulation 100～600s; Adopt the speed of cooling of 20～50 ℃/s that described cold rolling steel billet is cooled to room temperature then; The steel plate yield strength that obtains is 450～700MPa, and tensile strength is greater than 980MPa, and unit elongation A50 is greater than 20%.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101838769A (en) * | 2010-04-09 | 2010-09-22 | 武汉钢铁(集团)公司 | Steel for hot rolling U type steel sheet pile with tensile strength more than or equal to 600MPa and production method thereof |
| CN102409235A (en) * | 2010-09-21 | 2012-04-11 | 鞍钢股份有限公司 | High-strength cold rolling transformation induced plasticity steel plate and preparation method thereof |
| CN103695765A (en) * | 2013-12-11 | 2014-04-02 | 蔡志辉 | Cold-rolled medium manganese steel with high strength and high plasticity and preparation method thereof |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
| CN109504900A (en) * | 2018-12-05 | 2019-03-22 | 鞍钢股份有限公司 | A kind of superhigh intensity cold rolling transformation induced plasticity steel and preparation method thereof |
| CN109694990A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | Light phase transition inducing plasticity steel and its production method with good strong plasticity |
| CN109943769A (en) * | 2017-12-20 | 2019-06-28 | 宝山钢铁股份有限公司 | 780MPa rank low-carbon and low-alloy TRIP steel and its quick heat treatment method |
-
2008
- 2008-09-11 CN CN2008101198245A patent/CN101363102B/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101838769A (en) * | 2010-04-09 | 2010-09-22 | 武汉钢铁(集团)公司 | Steel for hot rolling U type steel sheet pile with tensile strength more than or equal to 600MPa and production method thereof |
| CN102409235A (en) * | 2010-09-21 | 2012-04-11 | 鞍钢股份有限公司 | High-strength cold rolling transformation induced plasticity steel plate and preparation method thereof |
| CN103695765A (en) * | 2013-12-11 | 2014-04-02 | 蔡志辉 | Cold-rolled medium manganese steel with high strength and high plasticity and preparation method thereof |
| CN109694990A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | Light phase transition inducing plasticity steel and its production method with good strong plasticity |
| CN109943769A (en) * | 2017-12-20 | 2019-06-28 | 宝山钢铁股份有限公司 | 780MPa rank low-carbon and low-alloy TRIP steel and its quick heat treatment method |
| CN109943769B (en) * | 2017-12-20 | 2021-06-15 | 宝山钢铁股份有限公司 | 780 MPa-grade low-carbon low-alloy TRIP steel and rapid heat treatment method thereof |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
| CN109504900A (en) * | 2018-12-05 | 2019-03-22 | 鞍钢股份有限公司 | A kind of superhigh intensity cold rolling transformation induced plasticity steel and preparation method thereof |
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