CN110117755A - A kind of preparation method of 980MPa grades of low yield strength ratio cold rolling medium managese steel - Google Patents
A kind of preparation method of 980MPa grades of low yield strength ratio cold rolling medium managese steel Download PDFInfo
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- CN110117755A CN110117755A CN201910423314.5A CN201910423314A CN110117755A CN 110117755 A CN110117755 A CN 110117755A CN 201910423314 A CN201910423314 A CN 201910423314A CN 110117755 A CN110117755 A CN 110117755A
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention discloses a kind of preparation method of 980MPa grades of low yield strength ratio cold rolling medium managese steel, belongs to technical field of metal material heat treatment.The present invention is at low cost without adding remaining any alloying element using traditional medium managese steel as raw material.Preparation method includes steel-making, continuous casting, hot rolling, pickling cold continuous rolling, continuous annealing；Cold-reduced sheet is heated to A when continuous annealingc3- 30 DEG C~Ac3+20℃；Then slowly cool to 640~670 DEG C；M is finally cooled to the cooling rate of 15~30 DEG C/ss+ 20~50 DEG C of progress overaging partition processing.The preparation method of 980MPa grades of low yield strength ratio cold rolling medium managese steel provided by the invention, obtain tiny isometric ferrite, lower bainite body and austenite or lower bainite and austenite complex tissue, the cold rolling medium managese steel being prepared has the characteristics that high intensity, high-elongation, low yield strength ratio and forming property are good, present invention process simple possible, it is of less demanding to technological equipment, it can be produced on existing continuous annealing production line.
Description
Technical field:
The invention belongs to technical field of metal material heat treatment, and in particular to manganese in a kind of 980MPa grades of low yield strength ratio cold rolling
The preparation method of steel.
Background technique:
In recent years, with the continuous growth of car ownership and yield, and by non-renewable fuel consumption and environment
Pollution bring pressure is gradually aggravated, and is gradually added sternly with the demand and national environmental protection policy of energy-saving and emission-reduction, automotive light weight technology is more next
More attract attention.Automotive light weight technology is to reduce automobile kerb weight, as far as possible under the premise of proof strength and safety to mention
The dynamic property of high automobile realizes energy-saving and emission-reduction.According to statistics, the every loss of weight 10% of automobile, can reduce oil consumption 8%~10%, discharge subtracts
Few 10%, emission reduction effect is obvious.The realization of automotive light weight technology needs material technology, Optimum design of lightweight technology, light weight
Change three aspect joint development of green manufacture technology, is material, various integrated, the wherein material such as designs, shapes technology
Innovation be basis and core.Body lightening material technology path mainly includes unimach, almag, composite material
Glass carbon fiber etc., but consider from Life cycle discharge, green circulatory utilization, automobile die and personnel's adaptability etc.,
Unimach has apparent advantage compared to other materials, is material most promising in future automobile lightweight.
At present for Light-weighting High Strength Steel Used in Automobiles, occurs the first generation, the second generation and third generation vapour in succession
Automobile-used advanced high-strength steel.Since the advanced high-strength steel of first generation automobile is while intensity increases, plasticity is decreased, strong to mould
Product is lower, is generally lower than 15GPa%, is difficult to adapt to requirement of the automobile industry to high formability and high security；Second generation automobile
Possess higher plasticity and strength and ductility product while with higher-strength with advanced high-strength steel, but its alloying element is very high,
High production cost, craftsmanship are poor with weldability.However the advanced high-strength steel of third generation automobile has the advanced height of first generation automobile
Alloying element, technique applicability and the cost of strong steel, and plasticity and strength and ductility product and the advanced high-strength steel of second generation automobile are close
The features such as, it is the following most potential automotive light weight technology material.Allusion quotation of the medium managese steel as third generation automobile advanced high-strength steel
Type represents one of steel grade, receives the extensive concern of metallurgy with automobile industry in recent years.
However, the cold rolling medium managese steel using bell-type annealing will appear very long yield point elongation, punching press during stretching
Cheng Zhonghui generates luders band, causes component surface obvious wrinkling occur, limits the application of cold rolling medium managese steel,
Therefore the luders band problem of urgent need to resolve cold rolling medium managese steel.Cold rolling medium managese steel luders band is improved at present and mainly passes through 2
Kind approach: first: being handled after cold rolling using 2 step intercritical annealings, such as Chinese patent CN107858586A；Second: cold rolling is even
Q&P technique is used on continuous anneling production line, is on the one hand improved production efficiency, is on the other hand improved its performance, such as Chinese patent
CN106191390A、CN109517947A、CN109536686A、CN105648317A、CN108950150A、
CN105648317A.It is this that the technological process of production is increased using 2 step critical annealings processing, it increases manufacturing cost, and adopt
Belt steel surface easily occurs to bond and reduce surface quality when being handled with higher temperature critical annealing；Using Q&P continuous annealing process
Although relatively excellent mechanical property can be obtained, hardening heat is required very low in production process, and partition temperature generally exists
350~400 DEG C, hardening heat with poor 100~200 DEG C of partition temperature, this does not have quick induction heating function in current overaging section
It cannot achieve on traditional continuous annealing production line of energy.
Summary of the invention:
The present invention In view of the above shortcomings of the prior art, provides a kind of 980MPa grades of low yield strength ratio cold rolling medium managese steel
Preparation method.By the optimization design of continuous annealing process, the tissue of cold rolling medium managese steel is regulated and controled, keeps its luders band existing
The problems such as being greatly improved or being eliminated, solve formability of materials and production procedure long, at high cost, surface quality is poor；Together
When break through traditional Q&P thinking, using completely new organization design thought, solve traditional continuous annealing process feasibility problems.This
Inventive method finally obtains answering for tiny isometric ferrite, lower bainite and austenite complex tissue or lower bainite and austenite
Be combined and knit, yield strength >=400MPa of prepared medium managese steel product, tensile strength >=980MPa, elongation percentage >=21%, bend
Strong ratio≤0.50.
Specific step is as follows for a kind of preparation method of 980MPa grades of low yield strength ratios cold rolling medium managese steel provided by the invention:
(1) smelting molten steel, molten steel are smelted using conventional converter or electric arc furnaces, are then refined using LF and RH, refining
The elemental gas such as S, O, H in main removal steel, ingredient is by mass percentage are as follows: and C:0.09~0.12%, Si:0:10~
0.30%, Mn:4.80~7.20%, Al:0.02~0.05%, P≤0.020%, S≤0.0030%, surplus are Fe and can not
The residual impurities element avoided.
(2) continuous casting, continuous casting is poured using full guard and electromagnetic agitation, thickness of strand 230mm, and the slab after continuous casting is straight
Connect hot charging.
(3) hot rolling, hot rolling are rolled using roughing+finish rolling, and roughing rolls in austenite recrystallization area, and rough rolling step is adopted
With 8~10 passes, workpiece thickness is 30~50mm, and finish rolling is rolled in austenite Unhydrated cement, and the finish rolling stage uses 6
~7 passes, roll rear coil of strip and are batched at 680~720 DEG C by 850~890 DEG C of finishing temperature.
(4) pickling cold continuous rolling, hot-strip is after hydrochloric acid turbulence acid dip trimming, through 4~5 Stands Cold Tandem Mills by hot-rolled strip
Steel is rolled to target thickness.
(5) it anneals, using continuous annealing furnace, strip is heated to 170 DEG C of progress with the rate of heat addition of 2~4 DEG C/s first
Preheating, is then further heated to A for strip with the rate of heat addition of 0.8~1.5 DEG C/sc3- 30 DEG C~Ac3+ 20 DEG C of progress sammings,
Soaking time is 260~320s, is then cooled to 640~670 DEG C of slow cooling temperature with the cooling rate of 1.5~3 DEG C/s, then with 15
The cooling rate of~30 DEG C/s is cooled to Ms+ 20~50 DEG C of 300~800s of ageing treatment, are finally cooled to room with the rate of 1~2 DEG C/s
Temperature.
Design philosophy of the invention is as follows:
The present invention uses traditional medium managese steel chemical component, and without adding remaining alloying element, cost of alloy is low, economical.
Course of hot rolling high temperature is batched, to reduce cold-rolling deformation drag.Alloying element is expanded by optimization design in annealing process
It dissipates to be regulated and controled with tissue, it is made to obtain tiny isometric ferrite, lower bainite and austenite or lower bainite and austenite
Complex tissue.
Influence of the preparation process to product of the present invention:
Smelting and refining treatment: purpose is to ensure that the basis requirement of molten steel, removes the pernicious gases such as oxygen, the hydrogen in steel
Cold short and hydrogen induced cracking sensibility is prevented, and the necessity such as carbon, manganese, silicon are added with objectionable impurities, reduction steel inclusions such as P, S
Alloying element, carry out the adjustment of alloying element.
Continuous casting: continuous casting is poured using full guard and electromagnetic agitation, is segregated with reducing steel inclusion with Mn is prevented, and improves casting
Base quality；The good slab of continuous casting is directly subjected to hot charging, to prevent cooling and crack in heating process.
Hot rolling: hot rolling, hot rolling are rolled using roughing+finish rolling, and roughing rolls in austenite recrystallization area, rough rolling step
Using 8~10 passes, to refine original austenite grain；Workpiece thickness is 30~50mm, and finish rolling is not tied again in austenite
Crystalline region rolling, finish rolling stage use 6~7 passes, 850~890 DEG C of finishing temperature, improve Nucleation rate and refinement group
It knits, and prevents banded structure；It rolls rear coil of strip to be batched at 680~720 DEG C, to reduce cold-rolling deformation drag.
Pickling cold continuous rolling: hot-strip is after hydrochloric acid turbulence acid dip trimming, through 4~5 Stands Cold Tandem Mills by hot-strip
It is rolled to target thickness, cold rolling reduction ratio 45~65%；
Annealing: continuous annealing furnace is used, strip is heated to 170 DEG C with the rate of heat addition of 2~4 DEG C/s first and is carried out in advance
Then strip is further heated to A with the rate of heat addition of 0.8~1.5 DEG C/s by heatc3- 30 DEG C~Ac3+ 20 DEG C of progress sammings are protected
The warm time is 260~320s, recrystallizes it sufficiently and makes crystal grain refinement, is on the other hand conducive to the expansion of Mn element
It dissipates；Then it is cooled to 640~670 DEG C of slow cooling temperature with the cooling rate of 1.5~3 DEG C/s, forms it into a certain amount of tiny isometric
Ferrite；M is then cooled to the cooling rate of 15~30 DEG C/ss+ 20~50 DEG C of 400~900s of ageing treatment, bring it about shellfish
The phase transformation of family name's body and partition processing, spread C, Mn alloying element in ferrite bainite into the austenite not changed, stablize difficult to understand
Family name's body；Room temperature is finally cooled to the rate of 1~2 DEG C/s.
The present invention has following technical characterstic:
1, the present invention uses completely new organization design thought, carries out tissue to cold rolling medium managese steel on continuous annealing production line
Regulation, while improving formability, process operability is strong.Compared with existing 2 step annealing eliminates yield point elongation method, adopt
Process flow is shortened with this method, reduces energy consumption, improves surface quality and production efficiency, reduces production cost.With it is existing
There is continuous annealing Q&P technique to compare, needs to be rapidly heated after traditional Q&P technique quenching to higher partition temperature, existing continuous
It is difficult to realize on anneling production line；And the present invention carries out heat preservation partition by the way that steel plate is cooled to Ms point temperatures above, connects in tradition
It can be mass on continuous anneling production line, process operability is strong.
2, the present invention regulates and controls tissue by optimizing annealing process, obtains fine ferrite, lower bainite and Ovshinsky
Bluk recombination tissue or lower bainite and austenite complex tissue, the steel plate after guaranteeing annealing have high-intensitive, high-ductility same
When, have the characteristics that lower yield tensile ratio, continuous surrender, effectively eliminates the long yield point elongation phenomenon of cold rolling medium managese steel, thus
Significantly improve the formability of product.
3, the present invention is designed using traditional low-carbon, low silicon, alloying of manganese, is not added with remaining alloying element in steel, is reduced
Smelting production difficulty and cost of alloy, have saved resource.
Specific embodiment:
A kind of preparation method of 980MPa grades of heretofore described low yield strength ratio cold rolling medium managese steel: (1) it smelts；(2) even
Casting；(3) hot rolling；(4) pickling cold continuous rolling；(5) it anneals.Molten steel of the invention pours into continuous casting installation for casting from tundish, then by continuous casting
Good slab direct hot charging carries out hot rolling, most afterwards after strip is rolled to target thickness by pickling cold continuous rolling, at continuous annealing
Reason obtains required product.
In the embodiment of the present invention, mechanics properties testing using GB/T228-2010 " metal material stretching test part 1:
Room temperature test method ", tensile test specimen scale distance 50mm.
In order to further preferably explain foregoing invention, the present invention is further retouched by following specific embodiment
It states:
Embodiment 1: the chemical component of steel includes: C:0.10%, Si:0.27%, Mn:5.15%, Al:0.023%, P:
0.007%, S:0.0021%, surplus are Fe and inevitable residual impurities element.
Its process flow are as follows: smelting → continuous casting → hot rolling → pickling cold continuous rolling → continuous annealing → finished product.
Technological parameter: hot rolling finishing temperature is 867 DEG C, hot rolled thickness: 3.5mm, cold-rolling thickness: 1.5mm, continuous annealing temperature
740 DEG C, soaking time 300s of degree, 670 DEG C of slow cooling temperature, 23 DEG C/s of rapid cooling rate, 350 DEG C of overaging temperature, overaging heat preservation
Time 400s, obtained cold rolling medium managese steel yield strength are 408.6MPa, tensile strength 993.1MPa, and elongation percentage is
23.5%, yield tensile ratio 0.41, strength and ductility product 23.34GPa% organizes as tiny isometric ferrite+lower bainite+residual austenite
Body.
Embodiment 2: the chemical component of steel includes: C:0.11%, Si:0.24%, Mn:7.05%, Al:0.028%, P:
0.009%, S:0.0018%, surplus are Fe and inevitable residual impurities element.
Its process flow are as follows: smelting → continuous casting → hot rolling → pickling cold continuous rolling → continuous annealing → finished product.
Technological parameter: hot rolling finishing temperature is 884 DEG C, hot rolled thickness: 3.2mm, cold-rolling thickness: 1.4mm, continuous annealing temperature
740 DEG C, soaking time 300s of degree, 650 DEG C of slow cooling temperature, 18 DEG C/s of rapid cooling rate, 350 DEG C of overaging temperature, overaging heat preservation
Time 650s, obtained cold rolling medium managese steel yield strength are 466.6MPa, tensile strength 1092.3MPa, and elongation percentage is
21.8%, yield tensile ratio 0.43, strength and ductility product 23.81GPa% organizes as tiny isometric ferrite+lower bainite+residual austenite
Body.
Embodiment 3: the chemical component of steel includes: C:0.11%, Si:0.15%, Mn:6.23%, Al:0.019%, P:
0.015%, S:0.0014%, surplus are Fe and inevitable residual impurities element.
Its process flow are as follows: smelting → continuous casting → hot rolling → pickling cold continuous rolling → continuous annealing → finished product.
Technological parameter: hot rolling finishing temperature is 873 DEG C, hot rolled thickness: 3.0mm, cold-rolling thickness: 1.2mm, continuous annealing temperature
760 DEG C, soaking time 280s of degree, 660 DEG C of slow cooling temperature, 25 DEG C/s of rapid cooling rate, 335 DEG C of overaging temperature, overaging heat preservation
Time 900s, obtained cold rolling medium managese steel yield strength are 546.5MPa, tensile strength 1153.0MPa, and elongation percentage is
23.8%, yield tensile ratio 0.47, strength and ductility product 27.4GPa% organizes as lower bainite+retained austenite.
Embodiment 4: the chemical component of steel includes: C:0.10%, Si:0.27%, Mn:5.15%, Al:0.023%, P:
0.007%, S:0.0021%, surplus are Fe and inevitable residual impurities element.
Its process flow are as follows: smelting → continuous casting → hot rolling → pickling cold continuous rolling → continuous annealing → finished product.
Technological parameter: hot rolling finishing temperature is 867 DEG C, hot rolled thickness: 3.2mm, cold-rolling thickness: 1.2mm, continuous annealing temperature
780 DEG C, soaking time 300s of degree, 670 DEG C of slow cooling temperature, 20 DEG C/s of rapid cooling rate, 350 DEG C of overaging temperature, overaging heat preservation
Time 450s, obtained cold rolling medium managese steel yield strength are 517.6MPa, tensile strength 1102.1MPa, and elongation percentage is
23.0%, yield tensile ratio 0.47, strength and ductility product 25.35GPa% organizes as lower bainite+retained austenite.
Embodiment 5: the chemical component of steel includes: C:0.10%, Si:0.27%, Mn:5.15%, Al:0.023%, P:
0.007%, S:0.0021%, surplus are Fe and inevitable residual impurities element.
Its process flow are as follows: smelting → continuous casting → hot rolling → pickling cold continuous rolling → continuous annealing → finished product.
Technological parameter: hot rolling finishing temperature is 867 DEG C, hot rolled thickness: 3.2mm, cold-rolling thickness: 1.2mm, continuous annealing temperature
780 DEG C, soaking time 300s of degree, 670 DEG C of slow cooling temperature, 18 DEG C/s of rapid cooling rate, 350 DEG C of overaging temperature, overaging heat preservation
Time 600s, obtained cold rolling medium managese steel yield strength are 538.1MPa, tensile strength 1087.9MPa, and elongation percentage is
22.9%, yield tensile ratio 0.49, strength and ductility product 24.91GPa% organizes as lower bainite+retained austenite.
Embodiment the result shows that, the method for the present invention is not added with any alloying element on the basis of traditional medium managese steel, using even
Continuous annealing process, regulates and controls tissue by continuous annealing process parameter optimization, improves strip surface quality and formability, contracting
Short production procedure improves production efficiency, reduces cost；By solving existing continuous annealing overaging section to tissue brand-new design
It cannot achieve quenching partition technological problems, present invention process is simple, strong operability.
Claims (1)
1. a kind of preparation method of 980MPa grades of low yield strength ratio cold rolling medium managese steel, it is characterised in that the specific steps of the preparation method
It is as follows:
(1) smelting molten steel, molten steel are smelted using conventional converter or electric arc furnaces, are then refined using LF and RH, and ingredient is pressed
Mass percent are as follows: C:0.09~0.12%, Si:0:10~0.30%, Mn:4.80~7.20%, Al:0.02~0.05%, P
≤ 0.020%, S≤0.0030%, surplus are Fe and inevitable residual impurities element；
(2) continuous casting, continuous casting is poured using full guard and electromagnetic agitation, thickness of strand 230mm, and the slab after continuous casting is directly warm
Dress；
(3) hot rolling, hot rolling are rolled using roughing+finish rolling, and roughing rolls in austenite recrystallization area, and rough rolling step uses 8
~10 passes, workpiece thickness are 30~50mm, and finish rolling is rolled in austenite Unhydrated cement, and the finish rolling stage uses 6~7
Passes, roll rear coil of strip and are batched at 680~720 DEG C by 850~890 DEG C of finishing temperature；
(4) pickling cold continuous rolling, hot-strip is after hydrochloric acid turbulence acid dip trimming, through 4~5 Stands Cold Tandem Mills by Rolling for Hot Rolled Strip
To target thickness；
(5) it anneals, using continuous annealing furnace, strip is heated to 170 DEG C with the rate of heat addition of 2~4 DEG C/s first and is preheated,
Then strip is further heated to by A with the rate of heat addition of 0.8~1.5 DEG C/sc3- 30 DEG C~Ac3+ 20 DEG C of progress sammings, heat preservation
Time is 260~320s, is then cooled to 640~670 DEG C of slow cooling temperature with the cooling rate of 1.5~3 DEG C/s, then with 15~30
DEG C/cooling rate of s is cooled to Ms+ 20~50 DEG C of 300~800s of ageing treatment, are finally cooled to room temperature with the rate of 1~2 DEG C/s.
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| CN201910423314.5A CN110117755B (en) | 2019-05-21 | 2019-05-21 | Preparation method of 980 MPa-grade cold-rolled medium manganese steel with low yield ratio |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113308649A (en) * | 2021-05-14 | 2021-08-27 | 唐山钢铁集团有限责任公司 | Low-yield-ratio 1000 MPa-grade cold-rolled dual-phase strip steel and production method thereof |
| CN113373376A (en) * | 2021-05-27 | 2021-09-10 | 本钢板材股份有限公司 | Bainite non-quenched and tempered high-strength steel with tensile strength of more than or equal to 960MPa and manufacturing method thereof |
| CN113462956A (en) * | 2021-05-25 | 2021-10-01 | 上海大学 | Large-section high-hardenability high-strength medium manganese forged steel and preparation method thereof |
| CN116536566A (en) * | 2023-03-28 | 2023-08-04 | 本钢板材股份有限公司 | Production method of 980 MPa-grade ultralow-carbon cold-rolled medium-manganese steel |
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| CN113462956B (en) * | 2021-05-25 | 2022-06-14 | 上海大学 | Large-section high-hardenability high-strength medium manganese forged steel and preparation method thereof |
| CN113373376A (en) * | 2021-05-27 | 2021-09-10 | 本钢板材股份有限公司 | Bainite non-quenched and tempered high-strength steel with tensile strength of more than or equal to 960MPa and manufacturing method thereof |
| CN116536566A (en) * | 2023-03-28 | 2023-08-04 | 本钢板材股份有限公司 | Production method of 980 MPa-grade ultralow-carbon cold-rolled medium-manganese steel |
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