CN105063311A - Processing method for improving surface quality of TRIP steel - Google Patents
Processing method for improving surface quality of TRIP steel Download PDFInfo
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- CN105063311A CN105063311A CN201510596778.8A CN201510596778A CN105063311A CN 105063311 A CN105063311 A CN 105063311A CN 201510596778 A CN201510596778 A CN 201510596778A CN 105063311 A CN105063311 A CN 105063311A
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Abstract
The invention provides a processing method for improving surface quality of TRIP steel, comprising the following steps: (1) preparing the TRIP steel from the following raw materials by weight percent: 0.10-0.25% of C, 1.0-4.0% of Mn, less than or equal to 0.5% of Si, 1.0-5.0% of Al, less than or equal to 0.1% of Cr, less than or equal to 0.01% of P, less than or equal to 0.01% of S, and the balance of Fe and inevitable impurities by virtue of smelting, and cogging the TRIP steel into a steel plate; (2) rolling the steel plate to the thickness of 4mm; (3) rolling the steel plate to the thickness of 1mm; (4) annealing the steel plate; and (5) performing isothermal quenching on the high aluminum TRIP steel plate obtained in the step (4). According to the scheme in the invention, by setting the annealing temperature of the high aluminum TRIP steel plate to be above Ac3 and below the liquidus temperature, the defect that the heat treatment temperature of conventional TRIP steel only can be limited between Ac1-Ac3, so as to cause a narrower annealing process window can be improved.
Description
Technical field
The invention belongs to metallurgical material technical field, be specifically related to a kind of working method improving TRIP steel surface quality.
Background technology
Current automobile, towards lightweight, energy-conservation and low cost future development, adopts high tensile steel plate to be the major measure that car industry and iron and steel circle are taked for this trend of reply.Baking hardened steel (BH steel), high-strength low-alloy steel (HSLA steel), dual phase steel (DP steel), Multiphase Steel (CP steel), martensitic steel (M steel) and phase change induction plasticity steel (TRIP steel) etc. are had in high-strength steel.Have yield strength due to TRIP steel and tensile strength is high, ductility is strong, stamping ability advantages of higher, is considered to the high Strength Steel for Motor Vehicles of a new generation, has all carried out a large amount of research and developments both at home and abroad.The best applications prospect of TRIP steel is arrangements for automotive doors fender rod, collision bumper and chassis structure part etc.
TRIP steel can be divided into hot rolling and Cold-Rolled TRIP Steel.Cold-Rolled TRIP Steel, owing to having the advantages such as the good and thinner thickness of surface quality, is applied more in actual production.The thermal treatment process of Cold-Rolled TRIP Steel as shown in Figure 1, first carries out two-phase region annealing to TRIP steel, and then is quickly cooled to Bainite Region to carry out isothermal quenching, finally again by TRIP steel air cooling to room temperature.
The object of two-phase region annealing is to obtain ferrite and austenite.When Bainite Region isothermal, partial austenitic changes bainite into, also has small part austenite to remain, in process of cooling subsequently, is not transformed into residual austenite.The microstructure of final Cold-Rolled TRIP Steel is ferrite+bainite+residual austenite.
TRIP steel is by the strain induced martensite forming core under viscous deformation effect of the residual austenite in TRIP effect and steel, introduces phase transformation strengthening and plasticity growth mechanisms and improves the intensity of steel plate and plasticity.Therefore in TRIP steel, the volume fraction of residual austenite and stability are the principal elements affecting TRIP steel mechanical property.
In TRIP steel, stable residual austenite, suppresses the precipitation of carbide extremely important.Because the formation of any carbide all will consume carbon, make to reduce for the carbon content be enriched in residual austenite, thus reduce the mechanical stability of residual austenite, the final remained austenite content formed is reduced.By adding the silicon of high level to suppress the precipitation of carbide in traditional TRIP steel.But high silicon content can make the coating degradation of TRIP steel.Because aluminium also has the effect suppressing carbide to be formed, therefore can to substitute with aluminium or Some substitute silicon improves the coating performance of TRIP steel.
Find in production practice, after the aluminium (>=1%) adding better quality mark in TRIP steel, TRIP steel can generate in process of setting
δferrite.That is, in liquidus temperature following high alumina TRIP steel, there is ferritic structure all the time.During traditional TRIP steel is produced, annealing temperature be selected in two-phase region (
a c1above,
a c3below,
a c1with
a c3calculation formula as follows) be to obtain ferrite and austenite structure.Because high alumina TRIP steel exists ferrite all the time below liquidus temperature, therefore its annealing temperature can be set in
a c1above, below liquidus temperature, ferrite and austenite structure can be obtained equally like this.In austempering process subsequently, due to the imperfection of bainite transformation, some austenite inevitable left behind and becomes residual austenite, thus can obtain the TRIP structure of steel of typical ferrite+bainite+residual austenite.So just, the present situation that traditional TRIP steel annealing temperature process window is narrower can be improved.
a c1with
a c3calculation formula be:
A c1(℃)=723-10.7Mn-13.9Ni+29Si+16.9Cr+290As+6.38W
A c3(℃)=910-230C
1/2-15.2Ni+44.7Si+104V+31.5Mo+13.1W
The symbol of element in formula represents its content (massfraction, %).
Summary of the invention
For prior art Problems existing, the invention provides a kind of working method improving TRIP steel surface quality.By rational thermal treatment process, cold rolling high alumina TRIP steel is made to have typical TRIP structure of steel and ferrite+bainite+residual austenite.Technical scheme of the present invention is:
Improve a working method for TRIP steel surface quality, carry out according to following processing step:
(1) according to weight percent be: C:0.10 ~ 0.25%; Mn:1.0 ~ 4.0%; Si :≤0.5%; Al:1.0 ~ 5.0%; Cr≤0.1%; P :≤0.01%; S≤0.01%; Surplus is the chemical composition apolegamy raw material of Fe and other inevitable impurity, adopts intermediate frequency vacuum induction furnace to smelt TRIP steel at 1500 ~ 1600 DEG C, is become by TRIP steel ingot formation thickness to be the steel plate of 50mm afterwards;
(2) adopt two roller reversible hot rollss by TRIP steel plate rolling to 4mm, processing parameter is: Heating temperature is 1150 ~ 1250 DEG C, and finishing temperature is 930 ~ 970 DEG C, and reduction in pass is 10 ~ 50%, through 5 ~ 7 passes to target thickness;
(3) adopt four roller unidirectional type cold-rolling mills by the TRIP steel plate rolling of step (2) to 1mm, processing parameter is: reduction in pass is 10 ~ 40%, through 5 ~ 10 passes to target thickness;
(4) annealed in box type heater by the high alumina TRIP steel plate of step (3), processing parameter is: annealing temperature is 800 ~ 1000 DEG C, and soaking time is 3 ~ 30min;
(5) the high alumina TRIP steel plate of step (4) is carried out isothermal quenching in salt bath furnace, processing parameter is: quenching temperature is 400 ~ 450 DEG C, soaking time is 3 ~ 30min, and air cooling, to room temperature, obtains the high alumina TRIP steel being organized as ferrite+bainite+residual austenite.
The described high alumina TRIP steel tensile strength being organized as ferrite+bainite+residual austenite is 445 ~ 520MPa, and yield strength is 320 ~ 350MPa, and unit elongation is 33.17 ~ 33.61%, and strength and ductility product is 16917 ~ 17477MPa%.
The principle of the present invention program's thermal treatment design is:
1, the aluminium adding high level in TRIP steel can make to occur in TRIP smelting steel process of setting
δferrite, when existing in TRIP steel
δduring ferrite,
a c3during annealing temperature above, below liquidus temperature, all can obtain ferrite+austenite structure.In austempering process subsequently, partial austenitic changes bainite into, but due to the imperfection of bainite transformation, have partial austenitic and left behind and become residual austenite, thus the TRIP structure of steel of ferrite+bainite+residual austenite can be obtained.
2, the rate of diffusion that the aluminium adding high level in TRIP steel can make carbon in steel is accelerated, and is incubated 5min and just there will be pearlitic structure at traditional austempering temperature 500 DEG C.Obviously can reduce the carbon content in residual austenite due to perlite, cause residual austenite mechanical stability to reduce, have a strong impact on the mechanical property of TRIP steel, therefore the austempering temperature of cold rolling high alumina TRIP steel should control at 400 ~ 450 DEG C.
The invention has the beneficial effects as follows:
1. the annealing temperature of high alumina TRIP steel plate is set in TRIP steel by the present invention program
a c3above, below liquidus temperature, improving traditional TRIP steel heat treatment temperature can only be confined to
a c1~
a c3between the narrower shortcoming of the annealing process window that causes.
2. the present invention program designs the aluminium adding 1.0 ~ 5.0% in TRIP steel, effectively improves the surface quality of TRIP steel plate, and suppresses the precipitation of carbide, and less on the plasticity impact of steel plate.In addition, present invention process is simple, and easy to implement, commercial viability is higher.
Accompanying drawing explanation
Fig. 1 is the thermal treatment process of existing Cold-Rolled TRIP Steel;
Fig. 2 is the metallographic structure figure of high alumina TRIP steel prepared by the embodiment of the present invention 1;
Fig. 3 is the metallographic structure figure of high alumina TRIP steel prepared by the embodiment of the present invention 2;
Fig. 4 is the metallographic structure figure of high alumina TRIP steel prepared by the embodiment of the present invention 3;
In accompanying drawing, A
c1for austenite phase transformation when hypoeutectoid steel heats starts temperature, A
c3for austenite phase transformation end temp when hypoeutectoid steel heats, B
sfor bainitic transformation starts temperature, B
ffor bainitic transformation end temp, F is ferrite, and B is bainite, and RA is residual austenite.
Embodiment
The two roller reversible hot rollss adopted in the embodiment of the present invention are made products.
The four roller unidirectional type cold-rolling mills adopted in the embodiment of the present invention are made products.
The box type heater model adopted in the embodiment of the present invention is: RX-36-10.
The salt bath furnace model adopted in the embodiment of the present invention is: SG-75-8.
The microstructure of LEICAQ550IW type opticmicroscope to high alumina TRIP steel is adopted to observe in the embodiment of the present invention.
Embodiment 1
(1) according to weight percent be: C:0.18%; Si:0.3%; Mn:1.56%; Al:1.44%; Cr:0.077%; P:0.008%; S:0.008%; Surplus is the chemical composition apolegamy raw material of Fe and other inevitable impurity, adopts intermediate frequency vacuum induction furnace to smelt TRIP steel at 1500 ~ 1600 DEG C, is become by TRIP steel ingot formation thickness to be the steel plate of 50mm afterwards; Measure this steel plate
a c1be 790 DEG C,
a c3it is 895 DEG C.
(2) adopt two roller reversible hot rollss by TRIP steel plate rolling to 4mm, processing parameter is: Heating temperature is 1200 DEG C, and finishing temperature is 930 DEG C, and reduction in pass is 10 ~ 50%, through 7 passes to target thickness;
(3) adopt four roller unidirectional type cold-rolling mills by the TRIP steel plate rolling of step (2) to 1mm, processing parameter is: reduction in pass is 10 ~ 40%, through 10 passes to target thickness;
(4) annealed in box type heater by the high alumina TRIP steel plate of step (3), processing parameter is: annealing temperature is 920 DEG C, and soaking time is 5min;
(5) the high alumina TRIP steel plate of step (4) is carried out isothermal quenching in salt bath furnace, processing parameter is: quenching temperature is 450 DEG C, and soaking time is 5min, and air cooling, to room temperature, obtains the high alumina TRIP steel being organized as ferrite+bainite+residual austenite.
High alumina TRIP steel prepared by the present embodiment, tensile strength is 520MPa, and yield strength is 350MPa, unit elongation is 33.61%, and strength and ductility product is 17477MPa%, in addition, high alumina TRIP structure of steel prepared by the present embodiment is ferrite+bainite+residual austenite, as shown in Figure 2.
Embodiment 2
(1) according to weight percent be: C:0.18%; Si:0.3%; Mn:1.56%; Al:1.44%; Cr:0.077%; P:0.008%; S:0.008%; Surplus is the chemical composition apolegamy raw material of Fe and other inevitable impurity, adopts intermediate frequency vacuum induction furnace to smelt TRIP steel at 1500 ~ 1600 DEG C, is become by TRIP steel ingot formation thickness to be the steel plate of 50mm afterwards; Measure this steel plate
a c1be 790 DEG C,
a c3it is 895 DEG C.
(2) adopt two roller reversible hot rollss by TRIP steel plate rolling to 4mm, processing parameter is: Heating temperature is 1200 DEG C, and finishing temperature is 950 DEG C, and reduction in pass is 10 ~ 50%, through 7 passes to target thickness;
(3) adopt four roller unidirectional type cold-rolling mills by the TRIP steel plate rolling of step (2) to 1mm, processing parameter is: reduction in pass is 10 ~ 40%, through 10 passes to target thickness;
(4) annealed in box type heater by the high alumina TRIP steel plate of step (3), processing parameter is: annealing temperature is 960 DEG C, and soaking time is 5min;
(5) the high alumina TRIP steel plate of step (4) is carried out isothermal quenching in salt bath furnace, processing parameter is: quenching temperature is 450 DEG C, and soaking time is 5min, and air cooling, to room temperature, obtains the high alumina TRIP steel being organized as ferrite+bainite+residual austenite.
High alumina TRIP steel prepared by the present embodiment, tensile strength is 510MPa, and yield strength is 350MPa, unit elongation is 33.17%, and strength and ductility product is 16917MPa%, in addition, high alumina TRIP structure of steel prepared by the present embodiment is ferrite+bainite+residual austenite, as shown in Figure 3.
Embodiment 3
(1) according to weight percent be: C:0.2%; Si:0.2%; Mn:1.6%; Al:1.6%; Cr:0.07%; P:0.01%; S:0.009%; Surplus is the chemical composition apolegamy raw material of Fe and other inevitable impurity, adopts intermediate frequency vacuum induction furnace to smelt TRIP steel at 1500 ~ 1600 DEG C, is become by TRIP steel ingot formation thickness to be the steel plate of 50mm afterwards; Measure this steel plate
a c1be 800 DEG C,
a c3it is 910 DEG C.
(2) adopt two roller reversible hot rollss by TRIP steel plate rolling to 4mm, processing parameter is: Heating temperature is 1200 DEG C, and finishing temperature is 950 DEG C, and reduction in pass is 10 ~ 50%, through 7 passes to target thickness;
(3) adopt four roller unidirectional type cold-rolling mills by the TRIP steel plate rolling of step (2) to 1mm, processing parameter is: reduction in pass is 10 ~ 40%, through 10 passes to target thickness;
(4) annealed in box type heater by the high alumina TRIP steel plate of step (3), processing parameter is: annealing temperature is 960 DEG C, and soaking time is 5min;
(5) the high alumina TRIP steel plate of step (4) is carried out isothermal quenching in salt bath furnace, processing parameter is: quenching temperature is 450 DEG C, and soaking time is 5min, and air cooling, to room temperature, obtains the high alumina TRIP steel being organized as ferrite+bainite+residual austenite.
High alumina TRIP steel prepared by the present embodiment, tensile strength is 480MPa, and yield strength is 330MPa, unit elongation is 34.78%, and strength and ductility product is 16994MPa%, in addition, high alumina TRIP structure of steel prepared by the present embodiment is ferrite+bainite+residual austenite, as shown in Figure 4.
Research process of the present invention is also based on prior art, and respectively not add the TRIP steel of aluminium and interpolation aluminium for starting material, and be set between Ac1 ~ Ac3 by annealing temperature, design two contrast experiments, experimental result is as follows:
Comparative example 1
The chemical composition (weight percent) of high alumina TRIP steel is: C:0.2%; Si:0.2%; Mn:1.6%; Al:1.6%; Cr:0.07%; P:0.010%; S:0.009%; Surplus is Fe and other inevitable impurity.Measure this steel plate
a c1be 800 DEG C,
a c3it is 910 DEG C.Annealing temperature is set in
a c1~
ac
3between, the TRIP steel tensile strength finally obtained is 500MPa, and yield strength is 340MPa, and unit elongation is 32.53%, and strength and ductility product is 16265MPa%.
Comparative example 2
The chemical composition (weight percent) of Al Containing TRIP Steel is not, C:0.15%; Si:1.5%; Mn:1.0%; Cr:0.10%; P:0.006%; S:0.007%; Surplus is Fe and other inevitable impurity.Measure this steel plate
a c1be 750 DEG C,
a c3it is 870 DEG C.Annealing temperature is set in
a c1~
ac
3between, the TRIP steel tensile strength finally obtained is 545MPa, and yield strength is 380MPa, and unit elongation is 31.24%, and strength and ductility product is 17026MPa%.
The mechanical performance compare of TRIP steel prepared by table 1 embodiment of the present invention and existing TRIP steel working method
| Numbering | The content % of aluminium in steel | Annealing temperature DEG C | Tensile strength/MPa | Yield strength/MPa | Unit elongation/% | Strength and ductility product/MPa% |
| Embodiment 1 | 1.44 | 920 | 520 | 350 | 33.61 | 17477 |
| Embodiment 2 | 1.44 | 960 | 510 | 350 | 33.17 | 16917 |
| Embodiment 3 | 1.6 | 960 | 480 | 330 | 34.78 | 16994 |
| Comparative example 1 | 1.6 | 830 | 500 | 340 | 32.53 | 16265 |
| Comparative example 2 | 0 | 790 | 545 | 380 | 31.24 | 17026 |
Above-mentioned three embodiments have been carried out high alumina TRIP steel
a c3annealing between ~ liquidus temperature, its mechanical property is in table 1.Table 1 has listed file names with the mechanical property of two comparative examples, and what adopt in comparative example is high alumina TRIP steel and the TRIP steel not containing aluminium, exists unlike the TRIP steel in comparative example
a c1~
a c3temperature section is annealed.Visible, change little high alumina TRIP steel with the aluminium of normative heat treatment, silicon total content and compare with not Al Containing TRIP Steel, through its tensile strength of high alumina TRIP steel of process of the present invention, yield strength and unit elongation, too large change does not occur.But the present invention makes the annealing region of high alumina TRIP steel widen, improve the present situation that traditional TRIP steel annealing process window is narrower.
Claims (2)
1. improve a working method for TRIP steel surface quality, it is characterized in that carrying out according to following processing step:
(1) according to weight percent be: C:0.10 ~ 0.25%; Mn:1.0 ~ 4.0%; Si :≤0.5%; Al:1.0 ~ 5.0%; Cr≤0.1%; P :≤0.01%; S≤0.01%; Surplus is the chemical composition apolegamy raw material of Fe and other inevitable impurity, adopts intermediate frequency vacuum induction furnace to smelt TRIP steel at 1500 ~ 1600 DEG C, is become by TRIP steel ingot formation thickness to be the steel plate of 50mm afterwards;
(2) adopt two roller reversible hot rollss by TRIP steel plate rolling to 4mm, processing parameter is: Heating temperature is 1150 ~ 1250 DEG C, and finishing temperature is 930 ~ 970 DEG C, and reduction in pass is 10 ~ 50%, through 5 ~ 7 passes to target thickness;
(3) adopt four roller unidirectional type cold-rolling mills by the TRIP steel plate rolling of step (2) to 1mm, processing parameter is: reduction in pass is 10 ~ 40%, through 5 ~ 10 passes to target thickness;
(4) annealed in box type heater by the high alumina TRIP steel plate of step (3), processing parameter is: annealing temperature is 800 ~ 1000 DEG C, and soaking time is 3 ~ 30min;
(5) the high alumina TRIP steel plate of step (4) is carried out isothermal quenching in salt bath furnace, processing parameter is: quenching temperature is 400 ~ 450 DEG C, soaking time is 3 ~ 30min, and air cooling, to room temperature, obtains the high alumina TRIP steel being organized as ferrite+bainite+residual austenite.
2. a kind of working method improving TRIP steel surface quality according to claim 1, the high alumina TRIP steel tensile strength being organized as ferrite+bainite+residual austenite described in it is characterized in that is 445 ~ 520MPa, yield strength is 320 ~ 350MPa, unit elongation is 33.17 ~ 33.61%, and strength and ductility product is 16917 ~ 17477MPa%.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106498307A (en) * | 2016-10-26 | 2017-03-15 | 武汉钢铁股份有限公司 | The good high-strength and high ductility lightweight steel of 780MPa level cold-forming properties and its manufacture method |
| CN106521335A (en) * | 2016-10-28 | 2017-03-22 | 东北大学 | High tensile strength and elongation TRIP steel bar material and equa-channel angular pressing preparation method |
| CN106636925A (en) * | 2016-12-30 | 2017-05-10 | 北京科技大学 | High-strength-and ductility-product cold-rolled TRIP steel and preparing method thereof |
| CN106868403A (en) * | 2017-03-28 | 2017-06-20 | 马钢(集团)控股有限公司 | A kind of great surface quality galvanizing TRIP steel plates and its manufacture method |
| CN108531690A (en) * | 2018-06-12 | 2018-09-14 | 东北大学 | A kind of heat treatment method for improving paralympic pattern and improving TRIP steel mechanical properties |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101280388A (en) * | 2008-05-20 | 2008-10-08 | 上海大学 | Zinc-platable low-carbon low-silicon cold rolled TRIP steel |
| CN102011051A (en) * | 2010-11-29 | 2011-04-13 | 上海大学 | High-strength and high-ductility medium carbon TRIP (transformation induced plasticity) steel and preparation method thereof |
-
2015
- 2015-09-18 CN CN201510596778.8A patent/CN105063311A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101280388A (en) * | 2008-05-20 | 2008-10-08 | 上海大学 | Zinc-platable low-carbon low-silicon cold rolled TRIP steel |
| CN102011051A (en) * | 2010-11-29 | 2011-04-13 | 上海大学 | High-strength and high-ductility medium carbon TRIP (transformation induced plasticity) steel and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| YANG ZHAO,ET AL.: "Effect of annealing temperature on microstructure and mechanical properties of a high Al-low Si TRIP steel", 《MATEC WEB OF CONFERENCES》 * |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106498307A (en) * | 2016-10-26 | 2017-03-15 | 武汉钢铁股份有限公司 | The good high-strength and high ductility lightweight steel of 780MPa level cold-forming properties and its manufacture method |
| CN106521335A (en) * | 2016-10-28 | 2017-03-22 | 东北大学 | High tensile strength and elongation TRIP steel bar material and equa-channel angular pressing preparation method |
| CN106521335B (en) * | 2016-10-28 | 2018-01-19 | 东北大学 | A kind of high strength and ductility TRIP Steel Bars and equal channel corner extrusion preparation method |
| CN106636925A (en) * | 2016-12-30 | 2017-05-10 | 北京科技大学 | High-strength-and ductility-product cold-rolled TRIP steel and preparing method thereof |
| CN106636925B (en) * | 2016-12-30 | 2018-05-18 | 北京科技大学 | A kind of high strength and ductility Cold-Rolled TRIP Steel and preparation method thereof |
| CN106868403A (en) * | 2017-03-28 | 2017-06-20 | 马钢(集团)控股有限公司 | A kind of great surface quality galvanizing TRIP steel plates and its manufacture method |
| CN106868403B (en) * | 2017-03-28 | 2019-07-02 | 马钢(集团)控股有限公司 | A kind of great surface quality hot galvanizing TRIP steel plate and its manufacturing method |
| CN108531690A (en) * | 2018-06-12 | 2018-09-14 | 东北大学 | A kind of heat treatment method for improving paralympic pattern and improving TRIP steel mechanical properties |
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