CN110004361A - A kind of production method improving cold rolling DP980 steel yield tensile ratio and reaming performance - Google Patents
A kind of production method improving cold rolling DP980 steel yield tensile ratio and reaming performance Download PDFInfo
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- CN110004361A CN110004361A CN201910256184.0A CN201910256184A CN110004361A CN 110004361 A CN110004361 A CN 110004361A CN 201910256184 A CN201910256184 A CN 201910256184A CN 110004361 A CN110004361 A CN 110004361A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
Abstract
The invention discloses a kind of production methods for improving cold rolling DP980 steel yield tensile ratio and reaming performance, it is on the basis of the Design of Chemical Composition of existing cold rolling DP980 steel, pass through the technological parameter of control slab heating process, hot-rolled process, cooling and coiling process, so that hot rolling initial tissu includes pearlite, medium temperature Martensite-Bainite Mixed Microstructure and isometric columnar ferrite tissue, wherein crystallite dimension≤5.0 μm, average grain size≤3.2 μm.According to Martensite Volume Fraction > 30.0% in the cold rolling DP980 steel microscopic structure of production method provided by the present invention preparation, yield tensile ratio > 0.70, hole expansibility >=55%, elongation percentage reaches 12.9% or more simultaneously, there is the automobile structure and reinforcer of reaming flange requirement while especially suitable for requiring 980MPa grades of high-tensile, having good drawing feature.
Description
Technical field
The invention belongs to automobile cold-rolled high-strength steel technical fields, and in particular to a kind of raising cold rolling DP980 steel yield tensile ratio
With the production method of reaming performance.
Background technique
The fast development of auto industry forcefully pushes Chinese national economy to realize that high speed develops in recent years, but by
This high energy consumption and maximum discharge for generating, serious ground contamination environment, many negative effects are generated to people's daily life.
It can be seen that realize the sustainable development of auto industry, it is necessary to solve the problems, such as energy-saving and emission-reduction, low-carbon environment-friendly, this is also each
State's auto industry faces the matter of utmost importance to be solved, while but also people Hyundai Motor is proposed it is safe and environment-friendly, easypro
Suitable, energy conservation should realize lightweight in the new demand of one, also guarantee vehicle performance simultaneously, therefore whole by design optimization
Bassinet structure and the various new materials of application, new process become the target pursued when researching and developing new model of Automobile Enterprises and lead
To.The research and development and popularization of cold rolling DP980 steel, the trend of responsive motor lightweight development, but it is directed to the cold rolling DP of 980MPa rank
Steel, research and development and designer propose new demand, not only have good drawing feature, while must meet in part manufacturing
Reaming, the requirement of flange.Traditional cold rolling DP980 steel has the characteristics that low yield strength ratio, is unable to satisfy during cold machine-shaping
Reaming, the requirement of flange, the defects of inevitably cracking.As it can be seen that in the chemistry of existing 980MPa rank cold rolling DP steel
In ingredient design basis, by regulating and controlling the key process parameter of each process section, high-yield-ratio and hole expansibility is produced, is provided simultaneously with
The cold rolling DP980 steel of good drawing feature, is those skilled in the art's technical problem urgently to be resolved.Existing 980MPa rank is cold
Technology disclosed in DP steel is rolled, is the cold rolling DP980 steel for low yield strength ratio (< 0.70), carries out production method, processing side
Method or preparation method illustrate, and related describe or explanation to reaming performance without detailed: publication number CN105803321A is introduced
A kind of 980MPa grades of ultra-fine grain containing vanadium cold-rolled biphase steel and preparation method thereof, wherein yield tensile ratio is 0.59 and 0.57, and is pressed
According to the cold rolling DP980 steel of production method of the present invention preparation, yield tensile ratio reaches 0.70 or more；Publication number CN107058869A is described
Ultralow yield tensile ratio 980MPa grades of cold-rolled biphase steels and its manufacturing method, yield tensile ratio < 0.50, and yield tensile ratio of the present invention reaches 0.70
More than；Publication number CN105861926A describes the dual phase steel and its production method of a kind of tensile strength 1000MPa, yield tensile ratio
0.665~0.695；Publication number CN 105132816A describes a kind of 1000MPa grades of cold rolled annealed dual phase steel and its production method
And purposes, yield tensile ratio 0.63~0.66；It is cold that publication number CN107043888A describes a kind of 980MPa that cold-bending property is excellent grade
It rolls dual phase sheet steel and preparation method thereof to compare with the present invention, ingredient mentality of designing and technical issues that need to address difference,
CN107043888A needs the Ti of additional addition 0.06~0.10%, and increases Nb content to 0.05% or more, increases Mn content
To 2.4% or more (present invention is free of Ti microalloy element, Nb content be 0.020~0.050%, Mn content be 2.00~
2.50%) it, compares with the cold rolling product volume reaming performance of same thickness specification of the present invention and wants low 5~6%.
Summary of the invention
The technical problem to be solved by the present invention is on the basis of the Design of Chemical Composition of existing 980MPa rank cold rolling DP steel,
By regulating and controlling the key process parameter of each process section, high-yield-ratio and hole expansibility are produced, good drawing feature is provided simultaneously with
Cold rolling DP980 steel is unable to satisfy reaming during cold machine-shaping to solve the cold rolling DP980 steel of traditional low yield strength ratio, turns over
The requirement on side, thus the problem of the defects of inevitably cracking.
In order to solve the above technical problems, of the invention provide a kind of raising cold rolling DP980 steel yield tensile ratio and reaming performance
Production method, carry out in accordance with the following methods control each process section technological parameter:
(1) steel making working procedure: its chemical component includes C:0.080~0.130% by weight percentage, and Si:0.28~
0.50%, Mn:2.00~2.50%, Alt:0.040~0.070%, Cr:0.40~0.70%, Mo:0.20~0.30%, Nb:
0.020~0.050%, and limit N≤0.005%, P≤0.008%, S≤0.005%, O≤0.003%, surplus be Fe and its
His inevitable impurity, but the implementation of production method of the present invention is not limited only to the design of this ingredient；
(2) heating of plate blank process: by heating steel billet, it is 1180~1220 DEG C that soaking section temperature, which is arranged, soaking time≤
30min；
(3) hot-rolled process: roughing mill and the sub-distribution of finishing mill road and each percentage pass reduction are by level two roughing setting up mould
Type calculates；Roughing outlet temperature be 1020~1050 DEG C, wherein hot rolling base-material thickness 2.00mm < hot rolling base-material thickness≤
The roughing outlet base thickness of 4.00mm is 40mm, and it is 50mm that 4.00mm < hot rolling base-material thickness≤6.00mm roughing, which exports base thickness,；
860~890 DEG C of finish rolling finishing temperature, and guarantee last two percentage pass reduction >=10% of finishing rolling mill；
(4) it cooling and coiling process: is taken after finish rolling and rolls rear leading portion rapid cooling technique, with the cooling rate of >=40 DEG C/s
550~580 DEG C are quickly cooled to, is batched；
(5) acid rolls process: then the above-mentioned coils of hot-rolled steel of pickling uses 65.0~70.0% drafts to remove oxide
Carry out cold rolling；
(6) continuous annealing process: the steel band after acid is rolled carries out continuous annealing, soaking temperature (Ac1+ 15 DEG C)~(Ac1+ 25 DEG C),
Slow cooling section terminates 680~700 DEG C of temperature, and rapid cooling section terminates 250~270 DEG C of temperature, 240~260 DEG C of overaging section temperature；
(7) smooth process: the coil of strip progress after continuous annealing is smooth, and smooth elongation control is 0.4~0.6%, so
It batches afterwards and obtains finished steel coils of the invention.
A kind of production method improving cold rolling DP980 steel yield tensile ratio and reaming performance of the present invention, passes through control panel
Base heating process, hot-rolled process, cooling and coiling process technological parameter, hot rolling initial tissu includes (10.0~21.0%) pearl
Body of light, (32.0~55.0%) medium temperature Martensite-Bainite Mixed Microstructure and (25.0~57.0%) isometric columnar ferrite tissue, wherein
Crystallite dimension≤5.0 μm, average grain size≤3.2 μm.
The cold rolling DP980 steel thickness specification of the present invention covers 0.80~2.00mm range, in microscopic structure
Martensite Volume Fraction > 30.0%, yield tensile ratio > 0.70, hole expansibility >=55%, while elongation percentage reaches 12.9% or more.
The beneficial effects of adopting the technical scheme are that the technical problem to be solved by the present invention is to existing
On the basis of the Design of Chemical Composition of 980MPa rank cold rolling DP steel, by regulating and controlling the key process parameter of each process section, produce
High-yield-ratio (> 0.70) and hole expansibility (>=55%) are provided simultaneously with the cold rolling of good drawing feature (elongation percentage >=12.9%)
DP980 steel is unable to satisfy reaming, flange to solve the cold rolling DP980 steel of traditional low yield strength ratio during cold machine-shaping
It is required that thus the problem of the defects of inevitably cracking.Especially suitable for requiring 980MPa grades of high-tensile, tool
There are the automobile structure and reinforcer of reaming flange requirement while standby good drawing feature.
Detailed description of the invention
Fig. 1 is the initial micro-organization chart of hot rolling of technique 1-I preparation in the embodiment of the present invention 1；
Fig. 2 is that the crystallite dimension EBSD of the initial microstructure of technique 1-I hot rolling in the embodiment of the present invention 1 analyzes result；
Fig. 3 is the micro-organization chart of the cold rolling DP980 steel of technique 1-I preparation in the embodiment of the present invention 1.
Specific embodiment
It is that a specific embodiment of the invention is described in further detail, but embodiments of the present invention are not limited to below
This.
Examples 1 to 3: a kind of production method improving cold rolling DP980 steel yield tensile ratio and reaming performance of the present invention,
As described below.
The chemical component of steel billet includes C:0.080~0.130%, Si by weight percentage in the embodiment of the present invention 1~3:
0.28~0.50%, Mn:2.00~2.50%, Alt:0.040~0.070%, Cr:0.40~0.70%, Mo:0.20~
0.30%, Nb:0.020~0.050%, and limit N≤0.005%, P≤0.008%, S≤0.005%, O≤0.003% are remaining
Amount is Fe and other inevitable impurity.The tapping ladle chemistry of steel billet is as shown in table 1 in specific embodiment 1~3, steel
Base is with a thickness of 230mm.
The practical smelting ingredient (mass percent, %) of 1 embodiment of table
Hot rolling base-material thickness 2.00mm < hot rolling base-material thickness≤4.00mm roughing exports in the embodiment of the present invention 1~3
Base thickness is 40mm, and it is 50mm that 4.00mm < hot rolling base-material thickness≤6.00mm roughing, which exports base thickness,.
The specific heating of plate blank process of the embodiment of the present invention 1~3, hot-rolled process, cooling and coiling process, acid roll process,
Continuous annealing process, the technical process of smooth process are as described below:
(1) heating of plate blank process: by heating steel billet, it is 1180~1220 DEG C that soaking section temperature, which is arranged, soaking time≤
30min；
(2) hot-rolled process: roughing mill and the sub-distribution of finishing mill road and each percentage pass reduction are by level two roughing setting up mould
Type calculates；Roughing outlet temperature is 1020~1050 DEG C, hot rolling base-material thickness 2.00mm < hot rolling base-material thickness≤4.00mm
It is 40mm that roughing, which exports base thickness,；It is 50mm that 4.00mm < hot rolling base-material thickness≤4.50mm roughing, which exports base thickness,；Finish rolling finish to gauge
860~890 DEG C of temperature, and guarantee last two percentage pass reduction >=10% of finishing rolling mill；
(3) it cooling and coiling process: is taken after finish rolling and rolls rear leading portion rapid cooling technique, with the cooling rate of >=40 DEG C/s
550~580 DEG C are quickly cooled to, is batched；
(4) acid rolls process: then the above-mentioned coils of hot-rolled steel of pickling uses 65.0~70.0% drafts to remove oxide
Carry out cold rolling；
(5) continuous annealing process: the steel band after acid is rolled carries out continuous annealing, soaking temperature (Ac1+ 15 DEG C)~(Ac1+ 25 DEG C),
Slow cooling section terminates 680~700 DEG C of temperature, and rapid cooling section terminates 250~270 DEG C of temperature, 240~260 DEG C of overaging section temperature.
(6) smooth process: the coil of strip progress after continuous annealing is smooth, and smooth elongation control is 0.4~0.6%, so
It batches afterwards and obtains finished steel coils of the invention.
In the embodiment of the present invention 1~3, the A that is measured by dilatometryc1It is respectively as follows: 765 DEG C, 755 DEG C, 757 DEG C.
The specific controlled rolling and cooling process parameter of the embodiment of the present invention 1~3 in actual production is as shown in table 2.
The main technique control parameter of 2 embodiment of table
Microscopic examination and Mechanics Performance Testing, test and analysis are carried out to the cold rolling DP980 steel sampling being prepared
As a result 3 are specifically shown in Table.Hot rolling initial tissu is mixed including (10.0~21.0%) pearlite, (32.0~55.0%) medium temperature bainite
Be combined and knit and (25.0~57.0%) isometric columnar ferrite tissue, wherein crystallite dimension≤5.0 μm, average grain size≤
3.2μm。
The mechanical property and microscopic structure volume fraction of 3 embodiment of table
Attached drawing 1 be the embodiment of the present invention 1 in technique 1-I preparation the initial micro-organization chart of hot rolling, by 10.0% pearlite,
40.8% medium temperature Martensite-Bainite Mixed Microstructure and 49.2% isometric columnar ferrite tissue are formed.The initial microstructure of hot rolling
EBSD crystallite dimension analysis the result shows that, 4.35 μm of the equal < of crystallite dimension, wherein 3.0 μm of size < of crystal grain accounts for 72.04%.It is flat
Equal 2.9 μm of crystallite dimension, is shown in attached drawing 2.
Martensite Volume Fraction > in the cold rolling DP980 steel microscopic structure that the embodiment of the present invention 1~3 is prepared
30.0%, attached drawing 3 is the micro-organization chart of the cold rolling DP980 steel of technique 1-I preparation in the embodiment of the present invention 1, wherein martensite
Volume fraction reaches 31.0%.
Mechanical experimental results show the cold rolling DP980 steel being prepared according to production method provided by the invention, resist
Tensile strength > 980MPa (actual test result is 994~1132MPa)；Yield tensile ratio > 0.70, hole expansibility >=55% extend simultaneously
Rate reaches 12.9% or more, and see Table 3 for details.It is from the comparing result in table 3 it is observed that (open compared to more existing public technology
Number CN 105803321A；CN 107058869A etc.), according to production method provided by the invention, pass through regulation each process section
Key process parameter, the cold rolling DP980 steel being prepared have good drawing feature when yield tensile ratio is improved to > 0.70
Hole expansibility >=55% simultaneously.
The above described is only a preferred embodiment of the present invention, being not that the invention has other forms of limitations, appoint
What those skilled in the art changed or be modified as possibly also with the technology contents of the disclosure above equivalent variations etc.
It imitates embodiment and is applied to other fields, but without departing from the technical solutions of the present invention, according to the technical essence of the invention
Any simple modification, equivalent variations and remodeling to the above embodiments, still fall within the protection scope of technical solution of the present invention.
Claims (3)
1. it is a kind of improve cold rolling DP980 steel yield tensile ratio and reaming performance production method, which is characterized in that in accordance with the following methods into
The technological parameter of row control each process section:
(1) steel making working procedure: its chemical component includes C:0.080~0.130% by weight percentage, Si:0.28~0.50%,
Mn:2.00~2.50%, Alt:0.040~0.070%, Cr:0.40~0.70%, Mo:0.20~0.30%, Nb:0.020~
0.050%, and N≤0.005% is limited, P≤0.008%, S≤0.005%, O≤0.003%, surplus is Fe and other can not
The impurity avoided, but the implementation of production method of the present invention is not limited only to the design of this ingredient；
(2) heating of plate blank process: by heating steel billet, it is 1180~1220 DEG C that soaking section temperature, which is arranged, soaking time≤30min；
(3) hot-rolled process: roughing mill and the sub-distribution of finishing mill road and each percentage pass reduction are by level two roughing setting up model meter
It calculates；Roughing outlet temperature is 1020~1050 DEG C, wherein hot rolling base-material thickness 2.00mm < hot rolling base-material thickness≤4.00mm
It is 40mm that roughing, which exports base thickness, and it is 50mm that 4.00mm < hot rolling base-material thickness≤6.00mm roughing, which exports base thickness,；Finish rolling finish to gauge
860~890 DEG C of temperature, and guarantee last two percentage pass reduction >=10% of finishing rolling mill；
(4) cooling and coiling process: taking after finish rolling and roll rear leading portion rapid cooling technique, quick with the cooling rate of >=40 DEG C/s
550~580 DEG C are cooled to, is batched；
(5) acid rolls process: then the above-mentioned coils of hot-rolled steel of pickling is carried out with removing oxide using 65.0~70.0% drafts
Cold rolling；
(6) continuous annealing process: the steel band progress continuous annealing after acid is rolled, Ac1+15 DEG C~Ac1+25 DEG C of soaking temperature, slow cooling section
Terminate 680~700 DEG C of temperature, rapid cooling section terminates 250~270 DEG C of temperature, 240~260 DEG C of overaging section temperature；
(7) smooth process: the coil of strip progress after continuous annealing is smooth, then smooth elongation control is rolled up 0.4~0.6%
It takes and obtains finished steel coils of the invention.
2. a kind of production method for improving cold rolling DP980 steel yield tensile ratio and reaming performance according to claim 1, feature
It is, by the technological parameter of control slab heating process, hot-rolled process, cooling and coiling process, hot rolling initial tissu includes
10.0~21.0% pearlite, 32.0~55.0% medium temperature Martensite-Bainite Mixed Microstructure and 25.0~57.0% etc. shaft-like
Ferritic structure, wherein crystallite dimension≤5.0 μm, average grain size≤3.2 μm.
3. a kind of production method for improving cold rolling DP980 steel yield tensile ratio and reaming performance according to claim 1, feature
It is, the cold rolling DP980 steel thickness specification covers 0.80~2.00mm range, Martensite Volume Fraction > in microscopic structure
30.0%, yield tensile ratio > 0.70, hole expansibility >=55%, while elongation percentage reaches 12.9% or more.
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Cited By (5)
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| CN111979490A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | High-ductility and high-formability cold-rolled DH590 steel and production method thereof |
| CN111979489A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade high-plasticity cold-rolled DH steel and preparation method thereof |
| CN112048681A (en) * | 2020-09-07 | 2020-12-08 | 鞍钢股份有限公司 | 980 MPa-grade high-formability cold-rolled DH steel and preparation method thereof |
| CN112553531A (en) * | 2020-12-04 | 2021-03-26 | 山东钢铁集团日照有限公司 | Low-cost hot forming steel for pipe making and production and preparation method thereof |
| CN113403544A (en) * | 2021-05-21 | 2021-09-17 | 鞍钢股份有限公司 | Automobile ultra-high formability 980 MPa-grade cold-rolled continuous annealing steel plate and preparation method thereof |
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| CN111979490A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | High-ductility and high-formability cold-rolled DH590 steel and production method thereof |
| CN111979489A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade high-plasticity cold-rolled DH steel and preparation method thereof |
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| CN112048681B (en) * | 2020-09-07 | 2021-11-16 | 鞍钢股份有限公司 | 980 MPa-grade high-formability cold-rolled DH steel and preparation method thereof |
| CN111979490B (en) * | 2020-09-07 | 2021-12-24 | 鞍钢股份有限公司 | High-ductility and high-formability cold-rolled DH590 steel and production method thereof |
| CN112553531A (en) * | 2020-12-04 | 2021-03-26 | 山东钢铁集团日照有限公司 | Low-cost hot forming steel for pipe making and production and preparation method thereof |
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Application publication date: 20190712 |