CN106319355A - Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof - Google Patents
Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof Download PDFInfo
- Publication number
- CN106319355A CN106319355A CN201510336578.9A CN201510336578A CN106319355A CN 106319355 A CN106319355 A CN 106319355A CN 201510336578 A CN201510336578 A CN 201510336578A CN 106319355 A CN106319355 A CN 106319355A
- Authority
- CN
- China
- Prior art keywords
- cold
- rolled steel
- steel sheet
- steel
- containing rare
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a rare earth-contained high-manganese cold-rolled steel plate and a manufacturing method thereof. The steel plate comprises the following components in percentage by weight: 0.4-0.8% of C,14-20% of Mn, 0.05-0.15% of RE, P not more than 0.020%, S not more than 0.012%, 1.0-2.0% of Al, 0.01-0.03% of N, and the balance of Fe and inevitable impurities; and the steel plate satisfies the conditions that: Mn+20*C not less than 30% and Al+5*RE not less than 1.8%. The steel plate is produced by a cold rolling-continuous annealing process to obtain austenite with 100% of room-temperature microstructure, reaches the recrystallization fraction of 80-95%, the yield strength of 450-650 MPa, the tensile strength of 950-1100 MPa and the ductility of above 50%, is excellent in splitting delay performance, is ultrahigh in strength, and is suitable for a vehicle structural part and a safety part with complex shapes.
Description
Technical field
The invention belongs to high manganese cold-rolled steel field, be specifically related to a kind of containing rare-earth high-Mn cold-rolled steel sheet and
Manufacture method, its yield strength is 450～650MPa, and tensile strength, 980～1100MPa, extends
Rate is more than 50%, and delayed fracture is functional, it is adaptable to complex-shaped automobile structure and safety
Part, and other association area.
Background technology
Improve the intensity of steel plate to subtract a kind of development trend that steel-sheet thickness is steel plate in recent years, greatly
Amount uses intensity ultrahigh-strength steel plates more than 780MPa rank to substitute orthodox car steel, is vapour
Car realizes the optimal material solution of " loss of weight is energy-conservation, improve safety and reduction manufacturing cost ", right
Build low-carbon (LC) social meaning great.Vehicle weight often alleviates 10%, can consume 5%～8% by saving fuel oil,
CO can be reduced accordingly simultaneously2Greenhouse gases and NOx、SO2Discharge Deng pollutant.
Traditional unimach brings the bright of plasticity and forming property while realizing high intensity
Aobvious decline, it is difficult to meet the following demand to high formability automobile unimach of auto industry.With
Phase transformation strengthening is that the development and application of main advanced high-strength vehicle steel has become as each big steel in the world
One of main flow problem of Inland Steel's research.By adding a certain amount of austenite stabilizer element in steel
As C, Mn, Cu etc. obtain the austenite structure of significant proportion, to increase substantially the machinery of material
Performance, has become as an important directions of automobile steel development.The highest C, Mn content
Full austenite steel, when its tensile strength reaches 1000MPa, elongation percentage is up to more than 50%.But,
There is the most serious delayed fracture risk, i.e. after cold deformation, material in this kind of high manganese full austenite steel capital
Material ftractures after easily causing certain time because self containing H or absorb H from environment.Postpone
Problem of Cracking is serious potential safety hazard, as can not be effectively solved, will be unable to realize answering in automobile industry
With.
At present, the method improving delayed fracture in potassium steel mainly has the alloying elements such as interpolation V, Al.
Improvement for potassium steel delayed fracture performance is a study hotspot, and relevant manufacture patent is more, but
Be these invention the most all concentrate on employing V, Al all compositions design, these elements be added on metallurgy
On all there is respective problem.The effect of V is unstable, controls difficulty relatively big, on useful industrially
There is bigger problem；The effect of Al is stable, and industrial prospect is preferable, but Al is added to smelting in a large number
Refining, continuous casting bring bigger technological difficulties.
International monopoly WO1993013233 (A1) disclose one possess superior forming property, intensity and
The high Mn austenitic steel of weldability and manufacture method thereof, its composition is C :≤1.5%, Mn:
15.0-35.0%, Al:0.1-6.0%, and may add Si, Cu, Nb, Ti, Ni, N etc. other
Element, remaining is Fe and impurity.This invention steel is fully austenitic structure, and grain size is less than 40 μm,
Forming property is superior, and elongation percentage is up to more than 50%, but its yield strength is only up to 300MPa
Left and right, tensile strength is only up to about 600MPa, for automobile super-high strength steel, intensity
More not enough.
United States Patent (USP) US20120288396 (A1) discloses the austenitic steel of a kind of superelevation ductility, and it becomes
It is divided into Mn:8～16%, Cu :≤3%, C: meet 33.5C+Mn≤25 and 33.5-Mn >=22, and
May add other element such as Cr, Ti, Nb, N, remaining for Fe with impurity, Austria of steel in this invention
Family name's body mark is more than 99%, and yield strength 300～630MPa, elongation percentage about 30%, for vapour
Automobile-used steel, the addition of Cu for control cost the most unfavorable, and about 30% elongation percentage with tradition
High-strength steel phase transformation does not the most possess clear superiority.
International monopoly WO2006048034 (A1) discloses a kind of high intensity TWIP steel and uses strip
Continuous casting producing method, its composition is: C:0.003～1.3%, Mn:18～30%, Ni≤10%, Si≤8%,
Al≤10%, Cr≤10%, N≤0.6%, Cu≤3%, separately there are the elements such as V, Ti, Mo, Nb, B.
This invention steel is TWIP steel, yield strength 340～580MPa, tensile strength 700～1100MPa,
Elongation percentage 30～65%, but in this invention, the Mn content of steel is higher, and add the Al of more than 3%
And Si, bigger problem can be there is at aspects such as steel-making, continuous castings.The surface quality control of thin strap continuous casting product
Difficulty processed is relatively big, the popularization more problems in terms of automobile steel.
International monopoly WO2009084792 (A1) discloses a kind of high intensity anti-delayed fracture height Mn steel
And manufacture method, its composition is: C:0.3～0.9, Mn:15～25%, Si≤0.1～2%, Al:
0.01～4%, Cr≤10%, N≤0.6%, Cu≤3%, additionally, it is possible to add V, Ti, Mo, Nb,
Cr, elements such as w, in this invention, the tensile strength of steel is at more than 920MPa, elongation percentage >=55%.
This invention Steel Properties is superior, but Mn content is higher, and cost control is the most unfavorable.
Chinese patent 200810239893.X discloses TWIP steel and the preparation work thereof of a kind of P strengthening
Skill, its composition is: C:0.01～0.08, Mn:15～35%, Si≤1～6%, Al:1～6%, P:
0.062～0.2%, remaining for Fe and impurity, the tensile strength 610～915MPa of steel in this invention, surrender
Intensity 225～610MPa, elongation percentage 45～85.5%, the forming property of steel is superior, but yield strength and
Low cross-intensity, it is more difficult to meet the requirement of future automobile unimach.It addition, use P strong
The high-strength steel changed also has bigger difficulty with other steel grade when welding.
Rare earth element is typically used for improving inclusion morphology, purifying steel in Ferrous Metallurgy, is performance
Excellent hydrogen storage material, it has good solidification, uses addition rare earth element to change H element
There is not been reported for kind potassium steel anti-delayed fracture performance.
Summary of the invention
It is an object of the invention to provide a kind of containing rare-earth high-Mn cold-rolled steel sheet and manufacture method thereof, it is thus achieved that
Steel plate yield strength is 450～650MPa, and tensile strength is 980～1100MPa, and elongation percentage is 50%
Above, room temperature microstructure is full austenite, and delayed fracture is functional, and intensity is high, and formability is high.
In order to achieve the above object, the technical scheme is that
A kind of cold-rolled steel sheet Han rare-earth high-Mn, its composition by weight percent is: C:0.4～0.8%,
Si≤0.5%；Mn:14～20%；RE:0.05～0.15%；P≤0.020%；S≤0.012%；Al:
1.0～2.0%；N:0.01～0.03%；Remaining is Fe and inevitable impurity；And meet,
Mn+20 × C >=30%；Al+5 × RE >=1.8%.
Preferably, in the composition of described steel plate, C:0.5～0.7%；Mn:15～18%；Al:
1.0～1.5%, by weight percentage.
Further, Si≤0.5%, preferably Si≤0.1% in described inevitable impurity.
The present invention containing rare-earth high-Mn cold-rolled steel sheet, its room temperature microstructure is full austenite, surrender
Intensity is 450～650MPa, and tensile strength is 980～1100MPa, and elongation percentage is more than 50%.
In the Design of Chemical Composition of the present invention:
C: be maximally effective austenite stabilizer element in steel, material stacking fault energy can be effectively improved, press down
Austenite phase transformation processed, thus improve stabilization of austenite.In potassium steel, add appropriate C, can
Under identical stabilization of austenite level, significantly reduce Mn content, thus reduce material cost.
Mn: be effective austenite stabilizer element.In potassium steel, the effect of Mn is similar with C,
Material stacking fault energy can be effectively improved, reduce martensite transformation temperature Ms, improve stabilization of austenite.
It addition, different from the effect of Mn in ordinary carbon steel, in high Mn austenitic steel, carrying of Mn content
The high reduction that can cause the strength of materials, therefore, on the premise of guaranteeing material stabilization of austenite, needs
To reduce Mn content as far as possible.
Mn+20 × C >=30wt.%: owing to C and Mn can play stable austenite, it is achieved full Ovshinsky
The effect of soma, therefore C and Mn can mutually compensate for a certain extent.The present invention is by big
Amount test data analyzer, confirms when the addition of Mn and C meets relational expression Mn+20 × C >=30wt.%
Time, it can be ensured that in steel of the present invention, austenite has enough stability, to realize room temperature microstructure
For full austenite.
Al: the anti-delayed fracture performance of material can be effectively improved.But the membership that adds of Al significantly deteriorates
The smelting of steel and continuous casting performance, water blocking mouthh when easily causing continuous casting.And smelting and casting process
In, a large amount of Al2O3Formation can reduce molten steel flow, to cause slag, slab problems of crack.
On the premise of guaranteeing that material delayed fracture performance is qualified, Al content needs to reduce as far as possible.
RE: for mischmetal.It is generally acknowledged that the RE (rare earth) effect in steel only improves folder
Foreign material form, purification steel, the raising strength of materials.But in steel of the present invention, RE serves more
Add important effect.On the one hand, RE is good hydrogen-absorbing material, can with H react formation stable
Hydride, thus reduce the diffusible H content in material, improve material anti-delayed fracture performance.High
The delayed fracture problem of manganese austenite steel plate is the most serious factor restricting its industrialization.Existing height
Mn austenitic steel is in order to improve the delayed fracture performance of material, it has to add substantial amounts of Al at steel grade,
Although achieving being obviously improved of delayed fracture performance, but also bring steel-making, casting character aobvious
Write and deteriorate, had a strong impact on the manufacturability of TWIP steel.In steel of the present invention, can be with by RE
Al is compound to be added, and makes Al+5 × RE >=1.8wt.%；Material delayed fracture performance can not reduced
Under premise, reduce the addition of Al, simultaneously work as improving the effect of the mechanical property of materials.The opposing party
Face, secondary cold-rolling is the effective ways improving high manganese austenite hardness of steel, but high Mn austenitic steel adds
Work hardening capacity is the highest, and secondary cold-rolling would generally bring being decreased obviously of plasticity.Adding RE can be effective
Postponement twin generates, thus reduces the work hardening capacity at material deformation initial stage, improves the cold rnning of material
Plasticity after work, beneficially material carry out secondary cold working production.
Si: in potassium steel, Si can reduce stabilization of austenite, for keeping complete austenite structure
Unfavorable, the most in the present invention, Si is as a kind of impurity element, and content is limited in less than 0.5%,
Preferably Si≤0.1%.
P: have certain solution strengthening effect, but the membership that adds of P significantly deteriorates material plasticity, fall
Low welding performance.In the present invention using P as impurity element, control in low-level as far as possible.
S: as far as possible control in relatively low level as its content of impurity element.
N: act on similar with C, is effective austenite stabilizer element.In potassium steel, improve
N content is conducive to increasing stabilization of austenite, improves material property, and in the present invention, N content controls
0.01～0.03%.
The manufacture method containing rare-earth high-Mn cold-rolled steel sheet of the present invention, comprises the steps:
1) smelting, strand
By mentioned component electric furnace smelting, it is casting continuously to form slab；
2) hot rolling
Heating of plate blank, heating-up temperature 1170～1230 DEG C；Then hot rolling, finishing temperature is 1000 ± 30
℃；Coiling temperature 650～850 DEG C；
3) cold rolling
Pickling, cold rolling, cold rolling reduction 30～60%；
4) annealing
Annealing in continuous annealing furnace, annealing temperature T is 650～800 DEG C, and annealing time t is
60～180s, and the combination of annealing temperature and annealing time meets following relation:
, there is austenite recrystallization in 1900≤Tlgt≤2200, finally stable to room temperature.
The steel plate room temperature microstructure that the present invention obtains is 100% austenite；Recrystallization mark is
80～95%；Yield strength is 450～650MPa, and tensile strength is 950～1100MPa, and elongation percentage exists
More than 50%.
In the recrystallization annealing of steel of the present invention, increase annealing temperature and annealing time is all conducive to element
Diffusion, promotes the recrystallization process of austenite.Therefore exist certain between annealing temperature and annealing time
The mutual compensating action of degree.The present invention is analyzed by great number tested data, confirms when annealing temperature T
When meeting relational expression 1900≤Tlgt≤2200 with annealing time t, it can be ensured that it is suitable to obtain after annealing
Full austenite recrystallized structure, to guarantee the performance of steel of the present invention.
The steel of the present invention is fully austenitic structure, there is not other type phase transformation, uses hot-rolled high to add
What hot stove was incubated act as reducing rolling load, making strand homogenization of composition.
In the manufacture method of the present invention, the reason using continuous annealing is that the cover annealing time is long,
Generally more than 6h, easily causes generation Carbide Precipitation in high Mn austenitic steel, and stabilization of austenite declines,
Thus affect the final structure property of steel of the present invention.Therefore, compared with cover annealing, continuous annealing
Having the clear superiorities such as tissue, superior performance, production efficiency is high, energy-conservation, the present invention uses and moves back continuously
Fire produces, and in annealing process, potassium steel completes the recrystallization process of Deformation structure, it is thus achieved that recrystallization is divided
Several 80～95% full austenite finally organize.
Beneficial effects of the present invention:
The present invention uses C, Mn, Al, RE composition design, without expensive alloying element,
Lower cost for material, the product manufacturability cold rolling full Ovshinsky of high Mn good, superior performance can be obtained
Body product made from steel.In potassium steel, add rare earth element, utilize the hydrogen storage property of rare earth element, effectively drop
Al content in low material, is obtaining while preferable anti-delayed fracture performance, the smelting of material,
Continuous casting performance significantly improves.Add RE and also can effectively postpone twin generation, thus reduce material deformation
The work hardening capacity at initial stage, after improving the cold working of material, to carry out secondary cold for plasticity, beneficially material
Processing.Steel of the present invention uses electric furnace smelting, continuous casting, hot rolling, pickling and cold-rolling, even moves back producer
Formula, production efficiency is high, properties of product uniformity is good.
The present invention is controlled by suitable composition design and cold rolling-continuous annealing process, it is possible to realize
The tensile strength of more than 950MPa and the elongation percentage of more than 50%.
The steel of the present invention will have preferable application prospect in automotive safety structural member, be particularly suitable for
Manufacture shape structural member extremely complex, exigent to forming property and safety member, such as car door
Crash bar, bumper and B post etc..
Accompanying drawing explanation
Fig. 1 is that the embodiment of the present invention 7 changes number with the comparative example 2 elongation percentage under the conditions of cold roller and deformed
According to.
Detailed description of the invention
Below in conjunction with specific embodiment, the invention will be further described.
The composition of the embodiment of the present invention through smelting, hot rolling, cold rolling, annealing and smooth after product, its
Middle composition is as shown in table 1, and annealing process and mechanical property situation are as shown in table 2, and Fig. 1 is the present invention
Embodiment 7 and the comparative example 2 elongation percentage delta data under the conditions of cold roller and deformed.
As can be seen from Table 1, the present invention coordinates through suitable composition design and technique, obtain containing dilute
The high manganese cold-rolled steel sheet room temperature microstructure of soil is 100% austenite；Recrystallization mark is 80～95%；Bend
Take intensity 450～650MPa, tensile strength 950～1100MPa, elongation percentage more than 50%,
Delayed fracture super high tensile cold-rolled steel plate of good performance.
The RE of Fig. 1 data explanation present invention there was added and helps slow down steel plate at cold roller and deformed lower elongation percentage
The degree declined, still keeps higher formability after being conducive to carrying out secondary cold-rolling processing.
Table 1 unit: percentage by weight
| Sequence number | C | Mn | Al | RE | N | P | S | Si |
| Embodiment 1 | 0.5 | 18 | 1.3 | 0.1 | 0.024 | 0.015 | 0.003 | 0.19 |
| Embodiment 2 | 0.8 | 12 | 1.2 | 0.15 | 0.018 | 0.005 | 0.005 | 0.13 |
| Embodiment 3 | 0.8 | 13 | 2.0 | 0.05 | 0.014 | 0.004 | 0.003 | 0.02 |
| Embodiment 4 | 0.4 | 19 | 1.1 | 0.15 | 0.027 | 0.016 | 0.012 | 0.11 |
| Embodiment 5 | 0.5 | 18 | 1.8 | 0.05 | 0.028 | 0.009 | 0.005 | 0.15 |
| Embodiment 6 | 0.7 | 14 | 1.4 | 0.10 | 0.026 | 0.013 | 0.008 | 0.25 |
| Embodiment 7 | 0.6 | 16 | 1.2 | 0.15 | 0.028 | 0.010 | 0.002 | 0.07 |
| Embodiment 8 | 0.6 | 15 | 1.5 | 0.10 | 0.020 | 0.007 | 0.006 | 0.09 |
| Embodiment 9 | 0.4 | 20 | 1.6 | 0.05 | 0.021 | 0.017 | 0.005 | 0.50 |
| Embodiment 10 | 0.6 | 16 | 1.3 | 0.10 | 0.017 | 0.009 | 0.002 | 0.16 |
| Embodiment 11 | 0.7 | 15 | 1.0 | 0.20 | 0.010 | 0.014 | 0.010 | 0.08 |
| Embodiment 12 | 0.8 | 14 | 1.5 | 0.10 | 0.011 | 0.006 | 0.010 | 0.05 |
| Embodiment 13 | 0.7 | 15 | 1.1 | 0.15 | 0.013 | 0.007 | 0.005 | 0.17 |
| Embodiment 14 | 0.6 | 16 | 1.4 | 0.10 | 0.027 | 0.004 | 0.003 | 0.38 |
| Embodiment 15 | 0.8 | 13 | 1.7 | 0.05 | 0.015 | 0.003 | 0.003 | 0.06 |
| Embodiment 16 | 0.6 | 17 | 1.9 | 0.05 | 0.016 | 0.020 | 0.004 | 0.16 |
| Comparative example 1 | 0.6 | 16 | - | - | 0.011 | 0.017 | 0.008 | 0.08 |
| Comparative example 2 | 0.6 | 16 | 1.2 | - | 0.028 | 0.013 | 0.006 | 0.25 |
| Comparative example 3 | - | 20 | 3.0 | - | - | - | - | 3.0 |
| Comparative example 4 | 0.5 | 18 | 2.3 | - | - | - | - | - |
Table 2
Claims (11)
1. a cold-rolled steel sheet Han rare-earth high-Mn, its chemical component weight percentage ratio is:
C:0.4～0.8%；
Mn:14～20%；
RE:0.05～0.15%；
P :≤0.020%；
S :≤0.012%；
Al:1.0～2.0%；
N:0.01～0.03%；
Remaining is Fe and inevitable impurity, and meets, Mn+20 × C >=30%；
Al+5 × RE >=1.8%.
The most according to claim 1 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that C content is
0.5～0.7%.
The most according to claim 1 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that Mn content
15～18%.
The most according to claim 1 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that Al content is
1.0～1.5%.
The most according to claim 1 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that described can not
Si≤0.5% in the impurity avoided.
The most according to claim 5 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that Si content≤0.1
%.
7. according to described in any one of claim 1 to 6 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that
The room temperature microstructure of described steel plate is 100% austenite, and recrystallization mark is 80～95%.
8. according to described in any one of claim 1 to 6 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that
The yield strength of described steel plate is 450～650MPa, and tensile strength, 950～1100MPa, extends
Rate is more than 50%.
9. according to the manufacture method containing rare-earth high-Mn cold-rolled steel sheet described in any one of claim 1 to 8,
Comprise the steps:
1) smelting, strand
By mentioned component electric furnace smelting, it is casting continuously to form slab；
2) hot rolling
Heating of plate blank, heating-up temperature 1170～1230 DEG C；Then hot rolling, finishing temperature is 1000 ± 30
DEG C, coiling temperature 650～850 DEG C；
3) cold rolling
Pickling, cold rolling, cold rolling reduction 30～60%；
4) annealing
Annealing in continuous annealing furnace, annealing temperature T is 650～800 DEG C, and annealing time t is
60～180s, and annealing temperature and annealing time meet following relation:
, there is austenite recrystallization in 1900≤Tlgt≤2200, finally stable to room temperature.
The most according to claim 9 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that described steel plate
Room temperature microstructure be 100% austenite, recrystallization mark is 80～95%.
11. is according to claim 9 containing rare-earth high-Mn cold-rolled steel sheet, it is characterised in that described steel plate
Yield strength 450～650MPa, tensile strength is 950～1100MPa, and elongation percentage is 50%
Above.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510336578.9A CN106319355A (en) | 2015-06-17 | 2015-06-17 | Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201510336578.9A CN106319355A (en) | 2015-06-17 | 2015-06-17 | Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN106319355A true CN106319355A (en) | 2017-01-11 |
Family
ID=57732556
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510336578.9A Pending CN106319355A (en) | 2015-06-17 | 2015-06-17 | Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106319355A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108754339A (en) * | 2018-05-23 | 2018-11-06 | 何满潮 | NPR anchor poles Steel material and its production method |
| CN112342352A (en) * | 2020-10-22 | 2021-02-09 | 西安工程大学 | Corrosion-resistant high-manganese austenitic steel plate and preparation method thereof |
| WO2021259278A1 (en) * | 2020-06-24 | 2021-12-30 | 宝山钢铁股份有限公司 | Multi-layer composite cold-rolled steel plate and manufacturing method therefor |
| CN114000062A (en) * | 2021-11-05 | 2022-02-01 | 贵州大学 | Low-temperature-resistant high-toughness structural steel treated by trace rare earth and preparation method thereof |
| CN115491614A (en) * | 2022-09-29 | 2022-12-20 | 武汉科技大学 | Austenitic high manganese steel with strength-elongation product of more than 60 GPa% and production method thereof |
| CN115537672A (en) * | 2022-07-19 | 2022-12-30 | 燕山大学 | Low-cost austenitic steel with yield strength of more than 1000MPa and warm rolling preparation process thereof |
| WO2023241546A1 (en) * | 2022-06-15 | 2023-12-21 | 宝山钢铁股份有限公司 | Highly formable and easily phosphated high-manganese cold-rolled steel plate having tensile strength of 1000-1600 mpa, and manufacturing method therefor |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101346480A (en) * | 2005-12-26 | 2009-01-14 | Posco公司 | High manganese steel strips with excellent coatability and superior surface property, coated steel strips using steel strips and method for manufacturing the steel strips |
| CN101660086A (en) * | 2008-08-25 | 2010-03-03 | 鞍钢股份有限公司 | Light and high-performance twin crystal induced plasticity steel and preparation method thereof |
| CN102011052A (en) * | 2010-12-27 | 2011-04-13 | 东北大学 | Preparation method of twin crystal induced plastic steel plate |
| CN102345077A (en) * | 2011-09-21 | 2012-02-08 | 西南石油大学 | Large-expansion-ratio expansion pipe steel with high product of strength and elongation and preparation method thereof |
| CN102400036A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Twin crystal induced plasticity steel with high elongation and high hole expansion rate and manufacturing method thereof |
-
2015
- 2015-06-17 CN CN201510336578.9A patent/CN106319355A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101346480A (en) * | 2005-12-26 | 2009-01-14 | Posco公司 | High manganese steel strips with excellent coatability and superior surface property, coated steel strips using steel strips and method for manufacturing the steel strips |
| CN101660086A (en) * | 2008-08-25 | 2010-03-03 | 鞍钢股份有限公司 | Light and high-performance twin crystal induced plasticity steel and preparation method thereof |
| CN102400036A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | Twin crystal induced plasticity steel with high elongation and high hole expansion rate and manufacturing method thereof |
| CN102011052A (en) * | 2010-12-27 | 2011-04-13 | 东北大学 | Preparation method of twin crystal induced plastic steel plate |
| CN102345077A (en) * | 2011-09-21 | 2012-02-08 | 西南石油大学 | Large-expansion-ratio expansion pipe steel with high product of strength and elongation and preparation method thereof |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108754339A (en) * | 2018-05-23 | 2018-11-06 | 何满潮 | NPR anchor poles Steel material and its production method |
| CN108754339B (en) * | 2018-05-23 | 2020-06-19 | 何满潮 | Production method of NPR anchor rod steel material |
| WO2021259278A1 (en) * | 2020-06-24 | 2021-12-30 | 宝山钢铁股份有限公司 | Multi-layer composite cold-rolled steel plate and manufacturing method therefor |
| EP4173818A4 (en) * | 2020-06-24 | 2023-12-20 | Baoshan Iron & Steel Co., Ltd. | Multi-layer composite cold-rolled steel plate and manufacturing method therefor |
| CN112342352A (en) * | 2020-10-22 | 2021-02-09 | 西安工程大学 | Corrosion-resistant high-manganese austenitic steel plate and preparation method thereof |
| CN112342352B (en) * | 2020-10-22 | 2022-07-01 | 西安工程大学 | Corrosion-resistant high-manganese austenitic steel plate and preparation method thereof |
| CN114000062B (en) * | 2021-11-05 | 2023-09-22 | 贵州大学 | Low-temperature-resistant high-toughness structural steel treated by trace rare earth and preparation method thereof |
| CN114000062A (en) * | 2021-11-05 | 2022-02-01 | 贵州大学 | Low-temperature-resistant high-toughness structural steel treated by trace rare earth and preparation method thereof |
| WO2023241546A1 (en) * | 2022-06-15 | 2023-12-21 | 宝山钢铁股份有限公司 | Highly formable and easily phosphated high-manganese cold-rolled steel plate having tensile strength of 1000-1600 mpa, and manufacturing method therefor |
| CN115537672A (en) * | 2022-07-19 | 2022-12-30 | 燕山大学 | Low-cost austenitic steel with yield strength of more than 1000MPa and warm rolling preparation process thereof |
| CN115537672B (en) * | 2022-07-19 | 2023-08-18 | 燕山大学 | Low-cost austenitic steel with yield strength greater than 1000MPa and warm rolling preparation process thereof |
| CN115491614A (en) * | 2022-09-29 | 2022-12-20 | 武汉科技大学 | Austenitic high manganese steel with strength-elongation product of more than 60 GPa% and production method thereof |
| CN115491614B (en) * | 2022-09-29 | 2023-10-17 | 武汉科技大学 | Austenitic high manganese steel with strength-plastic product larger than 60 GPa% |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108796363B (en) | High-surface-quality aluminum-coated substrate steel suitable for large deformation and stamping and production method thereof | |
| CN106319355A (en) | Rare earth-contained high-manganese cold-rolled steel plate and manufacturing method thereof | |
| US20190169708A1 (en) | 1900 MPa GRADE PRESS HARDENING STEEL BY MEDIUM THIN SLAB CASTING AND DIRECT ROLLING AND METHOD FOR PRODUCING THE SAME | |
| CN113416890B (en) | High-hole-expansion high-plasticity 980 MPa-grade cold-rolled continuous annealing steel plate and preparation method thereof | |
| CN106191678B (en) | With the tensile strength >=1700MPa hot formings steel and production method of medium thin slab Direct Rolling | |
| CN102912219A (en) | TRIP steel plate with high product of strength and elongation and preparation method thereof | |
| CN102400043B (en) | Large-thickness steel plate for oceaneering | |
| CN104593664A (en) | Hot-rolled nanometer bainite steel, production method of hot-rolled nanometer bainite steel and manufacturing method of automotive frame | |
| CN103526111A (en) | Hot-rolled plate band steel with yield strength being 900MPa and preparation method thereof | |
| CN106086683B (en) | With the thin hot forming steel of tensile strength >=1700MPa of sheet billet Direct Rolling and production method | |
| CN111172466B (en) | Plasticity-enhanced cold-rolled dual-phase steel with tensile strength of 590MPa and production method thereof | |
| CN101660086A (en) | Light and high-performance twin crystal induced plasticity steel and preparation method thereof | |
| CN110846577A (en) | 690 MPa-grade high-strength low-yield-ratio medium-thickness manganese steel and manufacturing method thereof | |
| CN110331341B (en) | High-formability high-strength hot-galvanized dual-phase steel and production method thereof | |
| CN104120368A (en) | High-strength austenitic stainless steel for automobile frames and manufacturing method thereof | |
| CN109023149B (en) | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof | |
| CN108411196A (en) | Tensile strength is 680MPa grades of large-scale mobile steelss for pressure vessel use and production method | |
| CN108728728B (en) | High manganese steel with extremely low yield ratio and manufacturing method thereof | |
| KR20230024905A (en) | Ultra-high strength steel with excellent plasticity and manufacturing method thereof | |
| CN103361552A (en) | V-N microalloyed 460MPa thick plate and manufacturing method thereof | |
| CN106319356A (en) | High manganese hot-dip galvanized steel sheet containing rare earth and manufacture method thereof | |
| CN108588569B (en) | Ocean engineering steel with yield strength of more than or equal to 450MPa and preparation method thereof | |
| CN114381658A (en) | 800 MPa-grade low-welding-crack-sensitivity steel plate and manufacturing method thereof | |
| CN108866435B (en) | Composite microalloyed medium manganese steel for automobile and manufacturing method thereof | |
| CN108486482B (en) | High-yield-strength hot-rolled pickled steel plate with excellent comprehensive performance and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20170111 |